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Elsevier Editorial System(tm) for Materials and Design Manuscript Draft Manuscript Number Title Influence of ZnO nanoparticles addition on thermal analysis microstructure evolution and tensile behavior of Sn-50 wt Sb-05 wt Cu Lead-free solder alloy Article Type Original Article Keywords Keywords Sn-5Sb solder composite lead free yield stress ultimate tensile stress Corresponding Author Dr Eid A Eid Ph D Corresponding Authors Institution Basic Science Department Higher Technological Institute 44629 10th of Ramadan City Egypt First Author Eid A Eid Ph D Order of Authors Eid A Eid Ph D Aly Fouda Abstract AbstractSn-5wtSb-05wtCu (plain SSC505) and Sn-5wtSb-05wtCu-05wt ZnO (SSC-ZnO) composite solder alloys have been studied The variation in thermal behavior microstructure and tensile characteristics associated with mixing of 05wt ZnO nano-metric particles to plain SSC505 sousing differential scanning calorimetry (DSC) after addition of ZnO X-ray diffraction (XRD) analysis
-Sn SbSn and Cu6Sn5 intermetallic compounds (IMCs) beside some of ZnO planes in SSC-ZnO composite solder Field emission scanning electronic microscope (EF-SEM) investigation of SSC-ZnO composite solder revealed a homogenous uniform distribution size
-Sn grains Addition of ZnO nano-metric particles into the plain SSC505
addition adding ZnO nano-metric particles were found to be effective for reducing ductility by 43 of -Sn grains within SSC305-ZnO composite solder
Dear Editor
Irsquom pleased to present our work titled
Influence of ZnO nano-particles addition on thermal analysis
microstructure evolution and tensile behavior of Sn-50 wt Sb-05 wt
Cu Lead-free solder alloy
The effect of adding ZnO nano-particles to Sn-5wtSb-05wtCu
(plain SSC505) were studied The variation in thermal behavior
microstructure and tensile characteristics associated with mixing of
05wt ZnO nano-metric particles to plain SSC505 solder were
investigated X-ray diffraction analysis of SSC-ZnO confirms the
existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure
observations revealed finer IMCs due to active surface area of ZnO
nanoparticles that supports the strong adsorption effect Improvement in
the tensile parameters was achieved because of presence of ZnO
nanopowders as reinforcement agent The nano-sized particles are
dispersed uniformly and homogeneously distributed in Sn matrix which
provide high barrier by impeding grain boundary sliding and dislocation
movement
The work is valuable to be published in Materials and Design
We here confirm that
1 The article is original
2 The article has been written by the stated authors who are ALL aware
of its content and approve its submission
3 The article has not been published previously
4 The article is not under consideration for publication elsewhere
5 No conflict of interest exists or if such conflict exists the exact nature
Cover Letter
of the conflict must be declared
6 If accepted the article will not be published elsewhere in the same
form in any language without the written consent of the publisher
Please accept my best regards
Dr E A Eid
Dr Aly Nabeih Fouda
1
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Highlights (for review)
1
Influence of ZnO nanoparticles addition on thermal analysis
microstructure evolution and tensile behavior of
Sn-50 wt Sb-05 wt Cu
Lead-free solder alloy
E A Eid a A N Fouda
b
(a) Basic Science Department Higher Technological Institute 44629 10th of Ramadan City Egypt
(b) Physics department Faculty of Science Suez-Canal University 41522 Ismailia Egypt
Abstract
Sn-5wtSb-05wtCu (plain SSC505) and Sn-5wtSb-05wtCu-05wt ZnO
(SSC-ZnO) composite solder alloys have been studied The variation in thermal behavior
microstructure and tensile characteristics associated with mixing of 05wt ZnO nano-
metric particles to plain SSC505 solder were investigated A slight increment in the
melting temperature [Tm= 089 oC] was recorded using differential scanning calorimetry
(DSC) after addition of ZnO X-ray diffraction (XRD) analysis confirmed the existence
of -Sn SbSn and Cu6Sn5 intermetallic compounds (IMCs) beside some of ZnO planes in
SSC-ZnO composite solder Field emission scanning electronic microscope (EF-SEM)
investigation of SSC-ZnO composite solder revealed a homogenous uniform distribution
size refinement of IMCs and -Sn grains Addition of ZnO nano-metric particles into the
plain SSC505 enhanced the yield stress YS by ~12 and improved the ultimate tensile
strength UTS by ~13 In addition adding ZnO nano-metric particles were found to be
effective for reducing ductility by 43 of the plain solder due to the refinement of -Sn
grains within SSC305-ZnO composite solder
Keywords Sn-5Sb solder composite lead free yield stress ultimate tensile stress
ManuscriptClick here to view linked References
2
1 Introduction
Sn based alloys is promising for advance electronics components connections as a
lead-free composite solder The substitution of toxic lead element (Pb) in the electronics
industry is one of the key issues in the current drive towards green ecology [1] Recently
high-temperature solders have been widely used in various types of applications like
assembling optoelectronic components automobile circuit boards circuit modules for
step soldering etc [2] Eutectic composition of goldndashtin (Au-20wt Sn) is the best
solder alloy for most applications in optoelectronic packaging because of its high creep
resistance wettability and good reliability Although goldndashtin solders have brittle phases
more expensive and has a melting point of 278 degC which is unacceptable for some
bonding applications [3 4] Certainly high soldering temperatures could damage the
properties of optical fibers and sensitive optoelectronics such as lasers light emitting
devices photodetectors or waveguide devices [5 2] To solve this problem great efforts
have been made to develop a new generation of solders with a low melting point
reasonable cost high dimension stability and supporting solder joints performance With
increasing miniaturization and more inputoutput terminals [6]
In high temperature applications Snndash5wt Sb solder is one of great potential
alternative material to push out the AundashSn solders and toxic Pb-rich solder alloys [7]
Snndash5wtSb solder has stable microstructure good mechanical properties highly creep
and corrosion resistance and good solderability (contact angle of about 43o) [7 8] To
enhance the performance of Tin-Antimony solders a third or more materials incorporated
as secondary phase with Sn-based matrix is one of the conventional approaches [9 10]
Micronano size metallic intermetallic or oxide particles are the most widely used in the
reinforcement of composite materials Consequently great numbers of researches focus
their study on the effect of adding reinforcement compound to lead free solder alloys
[11]
literature survey indicate that no attempt has been made to reinforce the binary
Sn-5wtSb solder or Sn-5wt Sb-05wt Cu solders by ZnO nanoparticle Meanwhile
a nano-size oxide intermetallic or ceramic particles are used to reinforce the composite
solders of Sn-Ag and Sn-Ag-Cu (SAC) Babaghorbani et al [12] added a different
3
addition of SnO2 nanopowders to Sn-35Ag lead-free solder alloy Taso et al [4] mixed a
different addition of TiO2 nano-size particles to Sn35Ag025Cu solder Their results
showed profound effects on the thermal characteristics of solder solidification and
reduction of the grain size Nai et al reported that the mechanical properties of the carbon
nano-tubescomposite solders improved significantly [11] However some efforts have
been made to reinforce Sn-35Ag solder with nanopowders of ZrO2 SiC Cu Co Ni Ag
and intermetallic particulates (Cu6Sn5 Ni3Sn4) using different processing methods
[612131415] Their results exhibit effective influence on the mechanical behavior
measurements indicated significant increases in yield strength ultimate tensile strength
and microhardness due to hinder the dislocation motion However the ductility decreased
with increasing amounts of nanoparticles additions Moreover the secondary phase must
be sufficiently fine bond well stable have a higher flow resistance than the alloy matrix
un-deformable and resist the fracture of solder joint
The literature survey revealed that no studies have been reported so far on lead-
free SSC505 solder joints containing nano-metric ZnO particles So the present work is
devoted for investigating the effect of addition of nano-metric ZnO particles on thermal
microstructure and tensile properties of Snndash5wt Sbndash05 wt Cu (SSC505) lead free
solder for trying to improve its microstructure and tensile properties
2 Experimental
Zinc oxide (ZnO) nanopowders were selected as a reinforcement oxide because of
its capability to form physical bond with metallic matrix Additionally the main
advantages of nano-sized ZnO particles are (i) it has density of (567 gcm3) which is
nearly close to density of Sn-5wtSb (7530 gcm3) (ii) high hardness when compared to
Sn-50Sb matrix (iii) chemical stability and (iv) low cost when compared to other
nanoparticles such as TiO2 Y2O3 SiC and ZrO2 [19]
A lead-free solder Sn-50 wt Sb-05 wt Cu (plain SSC505) solder alloy was
prepared by melting together Sn Sb and Cu ingots of 9999 purity SSC-ZnO
composite solder was prepared by mechanical mixing of 05 wt nano-metric ZnO
particles into plain SSC505 solder with subsequent remelting in a vacuum furnace at 300
oC for 2 hr to obtain a homogeneous composition A stainless steel mold was used for
4
casting then left to cool slowly to room temperature The two solder alloys in the form of
rods were cold drawn into a wire of 08 mm diameter A part of each alloy was rolled into
a sheet of 05 mm thick for microstructure investigations Specimens with a gauge length
of 50 mm were pulled for tensile testing Prior to the tensile testing all specimens were
heat-treated at a temperature of 150 oC for 2 h Then they cooled slowly to room
temperature in order to stabilize the microstructure and remove the residual defects which
produced during the cold drawn process The densities ) of plain and composite solders
were determined using Archimedesrsquo principle Polished samples taken from various
sections of the solidified rods were weighted in air and when immersed in distilled water
using an electronic balance (AampD HM-202) with an accuracy of plusmn 00001 g
For metallographic observations as-solidified specimens were prepared initially
by mounting in cold epoxy They were finely polished using 3m and 1m alumina
powder which suspended in distilled water as a lubricant Final polishing to near mirror-
like surface was achieved using 03m diamond paste The as-polished samples were
chemically etched in a solution of 80 glycerin 10 nitric acid and 10 acetic acid for
a few seconds
The etched surfaces of the solder samples were observed in an optical microscope
The surface morphology of the samples was characterized by using field emission
scanning electron microscopy (FESEM) SU8000 series equipped with energy dispersive
X-ray analysis EDX X-ray diffractometry (Philips diffractometer (40 kV) with Cu K1
radiation (λ = 015406 nm) was used for XRD measurements XRD patterns were
recorded in the 2θ range of 20ondash90deg (step size 002deg per 1 second)
The melting temperature and fusion heating of solders were analyzed using a
differential scanning calorimetry (DSC) Shimadzu DSC-50 DSC measurements were
carried out at heating rate of 5 oCmin and high purity nitrogen gas pass through heating
chamber to avoid oxidation of samples Tensile testing was performed by straining each
specimen to fracture under a strain rate of 47times10-3
s-1
and testing temperature of 27 oC
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
Dear Editor
Irsquom pleased to present our work titled
Influence of ZnO nano-particles addition on thermal analysis
microstructure evolution and tensile behavior of Sn-50 wt Sb-05 wt
Cu Lead-free solder alloy
The effect of adding ZnO nano-particles to Sn-5wtSb-05wtCu
(plain SSC505) were studied The variation in thermal behavior
microstructure and tensile characteristics associated with mixing of
05wt ZnO nano-metric particles to plain SSC505 solder were
investigated X-ray diffraction analysis of SSC-ZnO confirms the
existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure
observations revealed finer IMCs due to active surface area of ZnO
nanoparticles that supports the strong adsorption effect Improvement in
the tensile parameters was achieved because of presence of ZnO
nanopowders as reinforcement agent The nano-sized particles are
dispersed uniformly and homogeneously distributed in Sn matrix which
provide high barrier by impeding grain boundary sliding and dislocation
movement
The work is valuable to be published in Materials and Design
We here confirm that
1 The article is original
2 The article has been written by the stated authors who are ALL aware
of its content and approve its submission
3 The article has not been published previously
4 The article is not under consideration for publication elsewhere
5 No conflict of interest exists or if such conflict exists the exact nature
Cover Letter
of the conflict must be declared
6 If accepted the article will not be published elsewhere in the same
form in any language without the written consent of the publisher
Please accept my best regards
Dr E A Eid
Dr Aly Nabeih Fouda
1
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Highlights (for review)
1
Influence of ZnO nanoparticles addition on thermal analysis
microstructure evolution and tensile behavior of
Sn-50 wt Sb-05 wt Cu
Lead-free solder alloy
E A Eid a A N Fouda
b
(a) Basic Science Department Higher Technological Institute 44629 10th of Ramadan City Egypt
(b) Physics department Faculty of Science Suez-Canal University 41522 Ismailia Egypt
Abstract
Sn-5wtSb-05wtCu (plain SSC505) and Sn-5wtSb-05wtCu-05wt ZnO
(SSC-ZnO) composite solder alloys have been studied The variation in thermal behavior
microstructure and tensile characteristics associated with mixing of 05wt ZnO nano-
metric particles to plain SSC505 solder were investigated A slight increment in the
melting temperature [Tm= 089 oC] was recorded using differential scanning calorimetry
(DSC) after addition of ZnO X-ray diffraction (XRD) analysis confirmed the existence
of -Sn SbSn and Cu6Sn5 intermetallic compounds (IMCs) beside some of ZnO planes in
SSC-ZnO composite solder Field emission scanning electronic microscope (EF-SEM)
investigation of SSC-ZnO composite solder revealed a homogenous uniform distribution
size refinement of IMCs and -Sn grains Addition of ZnO nano-metric particles into the
plain SSC505 enhanced the yield stress YS by ~12 and improved the ultimate tensile
strength UTS by ~13 In addition adding ZnO nano-metric particles were found to be
effective for reducing ductility by 43 of the plain solder due to the refinement of -Sn
grains within SSC305-ZnO composite solder
Keywords Sn-5Sb solder composite lead free yield stress ultimate tensile stress
ManuscriptClick here to view linked References
2
1 Introduction
Sn based alloys is promising for advance electronics components connections as a
lead-free composite solder The substitution of toxic lead element (Pb) in the electronics
industry is one of the key issues in the current drive towards green ecology [1] Recently
high-temperature solders have been widely used in various types of applications like
assembling optoelectronic components automobile circuit boards circuit modules for
step soldering etc [2] Eutectic composition of goldndashtin (Au-20wt Sn) is the best
solder alloy for most applications in optoelectronic packaging because of its high creep
resistance wettability and good reliability Although goldndashtin solders have brittle phases
more expensive and has a melting point of 278 degC which is unacceptable for some
bonding applications [3 4] Certainly high soldering temperatures could damage the
properties of optical fibers and sensitive optoelectronics such as lasers light emitting
devices photodetectors or waveguide devices [5 2] To solve this problem great efforts
have been made to develop a new generation of solders with a low melting point
reasonable cost high dimension stability and supporting solder joints performance With
increasing miniaturization and more inputoutput terminals [6]
In high temperature applications Snndash5wt Sb solder is one of great potential
alternative material to push out the AundashSn solders and toxic Pb-rich solder alloys [7]
Snndash5wtSb solder has stable microstructure good mechanical properties highly creep
and corrosion resistance and good solderability (contact angle of about 43o) [7 8] To
enhance the performance of Tin-Antimony solders a third or more materials incorporated
as secondary phase with Sn-based matrix is one of the conventional approaches [9 10]
Micronano size metallic intermetallic or oxide particles are the most widely used in the
reinforcement of composite materials Consequently great numbers of researches focus
their study on the effect of adding reinforcement compound to lead free solder alloys
[11]
literature survey indicate that no attempt has been made to reinforce the binary
Sn-5wtSb solder or Sn-5wt Sb-05wt Cu solders by ZnO nanoparticle Meanwhile
a nano-size oxide intermetallic or ceramic particles are used to reinforce the composite
solders of Sn-Ag and Sn-Ag-Cu (SAC) Babaghorbani et al [12] added a different
3
addition of SnO2 nanopowders to Sn-35Ag lead-free solder alloy Taso et al [4] mixed a
different addition of TiO2 nano-size particles to Sn35Ag025Cu solder Their results
showed profound effects on the thermal characteristics of solder solidification and
reduction of the grain size Nai et al reported that the mechanical properties of the carbon
nano-tubescomposite solders improved significantly [11] However some efforts have
been made to reinforce Sn-35Ag solder with nanopowders of ZrO2 SiC Cu Co Ni Ag
and intermetallic particulates (Cu6Sn5 Ni3Sn4) using different processing methods
[612131415] Their results exhibit effective influence on the mechanical behavior
measurements indicated significant increases in yield strength ultimate tensile strength
and microhardness due to hinder the dislocation motion However the ductility decreased
with increasing amounts of nanoparticles additions Moreover the secondary phase must
be sufficiently fine bond well stable have a higher flow resistance than the alloy matrix
un-deformable and resist the fracture of solder joint
The literature survey revealed that no studies have been reported so far on lead-
free SSC505 solder joints containing nano-metric ZnO particles So the present work is
devoted for investigating the effect of addition of nano-metric ZnO particles on thermal
microstructure and tensile properties of Snndash5wt Sbndash05 wt Cu (SSC505) lead free
solder for trying to improve its microstructure and tensile properties
2 Experimental
Zinc oxide (ZnO) nanopowders were selected as a reinforcement oxide because of
its capability to form physical bond with metallic matrix Additionally the main
advantages of nano-sized ZnO particles are (i) it has density of (567 gcm3) which is
nearly close to density of Sn-5wtSb (7530 gcm3) (ii) high hardness when compared to
Sn-50Sb matrix (iii) chemical stability and (iv) low cost when compared to other
nanoparticles such as TiO2 Y2O3 SiC and ZrO2 [19]
A lead-free solder Sn-50 wt Sb-05 wt Cu (plain SSC505) solder alloy was
prepared by melting together Sn Sb and Cu ingots of 9999 purity SSC-ZnO
composite solder was prepared by mechanical mixing of 05 wt nano-metric ZnO
particles into plain SSC505 solder with subsequent remelting in a vacuum furnace at 300
oC for 2 hr to obtain a homogeneous composition A stainless steel mold was used for
4
casting then left to cool slowly to room temperature The two solder alloys in the form of
rods were cold drawn into a wire of 08 mm diameter A part of each alloy was rolled into
a sheet of 05 mm thick for microstructure investigations Specimens with a gauge length
of 50 mm were pulled for tensile testing Prior to the tensile testing all specimens were
heat-treated at a temperature of 150 oC for 2 h Then they cooled slowly to room
temperature in order to stabilize the microstructure and remove the residual defects which
produced during the cold drawn process The densities ) of plain and composite solders
were determined using Archimedesrsquo principle Polished samples taken from various
sections of the solidified rods were weighted in air and when immersed in distilled water
using an electronic balance (AampD HM-202) with an accuracy of plusmn 00001 g
For metallographic observations as-solidified specimens were prepared initially
by mounting in cold epoxy They were finely polished using 3m and 1m alumina
powder which suspended in distilled water as a lubricant Final polishing to near mirror-
like surface was achieved using 03m diamond paste The as-polished samples were
chemically etched in a solution of 80 glycerin 10 nitric acid and 10 acetic acid for
a few seconds
The etched surfaces of the solder samples were observed in an optical microscope
The surface morphology of the samples was characterized by using field emission
scanning electron microscopy (FESEM) SU8000 series equipped with energy dispersive
X-ray analysis EDX X-ray diffractometry (Philips diffractometer (40 kV) with Cu K1
radiation (λ = 015406 nm) was used for XRD measurements XRD patterns were
recorded in the 2θ range of 20ondash90deg (step size 002deg per 1 second)
The melting temperature and fusion heating of solders were analyzed using a
differential scanning calorimetry (DSC) Shimadzu DSC-50 DSC measurements were
carried out at heating rate of 5 oCmin and high purity nitrogen gas pass through heating
chamber to avoid oxidation of samples Tensile testing was performed by straining each
specimen to fracture under a strain rate of 47times10-3
s-1
and testing temperature of 27 oC
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
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13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
of the conflict must be declared
6 If accepted the article will not be published elsewhere in the same
form in any language without the written consent of the publisher
Please accept my best regards
Dr E A Eid
Dr Aly Nabeih Fouda
1
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Highlights (for review)
1
Influence of ZnO nanoparticles addition on thermal analysis
microstructure evolution and tensile behavior of
Sn-50 wt Sb-05 wt Cu
Lead-free solder alloy
E A Eid a A N Fouda
b
(a) Basic Science Department Higher Technological Institute 44629 10th of Ramadan City Egypt
(b) Physics department Faculty of Science Suez-Canal University 41522 Ismailia Egypt
Abstract
Sn-5wtSb-05wtCu (plain SSC505) and Sn-5wtSb-05wtCu-05wt ZnO
(SSC-ZnO) composite solder alloys have been studied The variation in thermal behavior
microstructure and tensile characteristics associated with mixing of 05wt ZnO nano-
metric particles to plain SSC505 solder were investigated A slight increment in the
melting temperature [Tm= 089 oC] was recorded using differential scanning calorimetry
(DSC) after addition of ZnO X-ray diffraction (XRD) analysis confirmed the existence
of -Sn SbSn and Cu6Sn5 intermetallic compounds (IMCs) beside some of ZnO planes in
SSC-ZnO composite solder Field emission scanning electronic microscope (EF-SEM)
investigation of SSC-ZnO composite solder revealed a homogenous uniform distribution
size refinement of IMCs and -Sn grains Addition of ZnO nano-metric particles into the
plain SSC505 enhanced the yield stress YS by ~12 and improved the ultimate tensile
strength UTS by ~13 In addition adding ZnO nano-metric particles were found to be
effective for reducing ductility by 43 of the plain solder due to the refinement of -Sn
grains within SSC305-ZnO composite solder
Keywords Sn-5Sb solder composite lead free yield stress ultimate tensile stress
ManuscriptClick here to view linked References
2
1 Introduction
Sn based alloys is promising for advance electronics components connections as a
lead-free composite solder The substitution of toxic lead element (Pb) in the electronics
industry is one of the key issues in the current drive towards green ecology [1] Recently
high-temperature solders have been widely used in various types of applications like
assembling optoelectronic components automobile circuit boards circuit modules for
step soldering etc [2] Eutectic composition of goldndashtin (Au-20wt Sn) is the best
solder alloy for most applications in optoelectronic packaging because of its high creep
resistance wettability and good reliability Although goldndashtin solders have brittle phases
more expensive and has a melting point of 278 degC which is unacceptable for some
bonding applications [3 4] Certainly high soldering temperatures could damage the
properties of optical fibers and sensitive optoelectronics such as lasers light emitting
devices photodetectors or waveguide devices [5 2] To solve this problem great efforts
have been made to develop a new generation of solders with a low melting point
reasonable cost high dimension stability and supporting solder joints performance With
increasing miniaturization and more inputoutput terminals [6]
In high temperature applications Snndash5wt Sb solder is one of great potential
alternative material to push out the AundashSn solders and toxic Pb-rich solder alloys [7]
Snndash5wtSb solder has stable microstructure good mechanical properties highly creep
and corrosion resistance and good solderability (contact angle of about 43o) [7 8] To
enhance the performance of Tin-Antimony solders a third or more materials incorporated
as secondary phase with Sn-based matrix is one of the conventional approaches [9 10]
Micronano size metallic intermetallic or oxide particles are the most widely used in the
reinforcement of composite materials Consequently great numbers of researches focus
their study on the effect of adding reinforcement compound to lead free solder alloys
[11]
literature survey indicate that no attempt has been made to reinforce the binary
Sn-5wtSb solder or Sn-5wt Sb-05wt Cu solders by ZnO nanoparticle Meanwhile
a nano-size oxide intermetallic or ceramic particles are used to reinforce the composite
solders of Sn-Ag and Sn-Ag-Cu (SAC) Babaghorbani et al [12] added a different
3
addition of SnO2 nanopowders to Sn-35Ag lead-free solder alloy Taso et al [4] mixed a
different addition of TiO2 nano-size particles to Sn35Ag025Cu solder Their results
showed profound effects on the thermal characteristics of solder solidification and
reduction of the grain size Nai et al reported that the mechanical properties of the carbon
nano-tubescomposite solders improved significantly [11] However some efforts have
been made to reinforce Sn-35Ag solder with nanopowders of ZrO2 SiC Cu Co Ni Ag
and intermetallic particulates (Cu6Sn5 Ni3Sn4) using different processing methods
[612131415] Their results exhibit effective influence on the mechanical behavior
measurements indicated significant increases in yield strength ultimate tensile strength
and microhardness due to hinder the dislocation motion However the ductility decreased
with increasing amounts of nanoparticles additions Moreover the secondary phase must
be sufficiently fine bond well stable have a higher flow resistance than the alloy matrix
un-deformable and resist the fracture of solder joint
The literature survey revealed that no studies have been reported so far on lead-
free SSC505 solder joints containing nano-metric ZnO particles So the present work is
devoted for investigating the effect of addition of nano-metric ZnO particles on thermal
microstructure and tensile properties of Snndash5wt Sbndash05 wt Cu (SSC505) lead free
solder for trying to improve its microstructure and tensile properties
2 Experimental
Zinc oxide (ZnO) nanopowders were selected as a reinforcement oxide because of
its capability to form physical bond with metallic matrix Additionally the main
advantages of nano-sized ZnO particles are (i) it has density of (567 gcm3) which is
nearly close to density of Sn-5wtSb (7530 gcm3) (ii) high hardness when compared to
Sn-50Sb matrix (iii) chemical stability and (iv) low cost when compared to other
nanoparticles such as TiO2 Y2O3 SiC and ZrO2 [19]
A lead-free solder Sn-50 wt Sb-05 wt Cu (plain SSC505) solder alloy was
prepared by melting together Sn Sb and Cu ingots of 9999 purity SSC-ZnO
composite solder was prepared by mechanical mixing of 05 wt nano-metric ZnO
particles into plain SSC505 solder with subsequent remelting in a vacuum furnace at 300
oC for 2 hr to obtain a homogeneous composition A stainless steel mold was used for
4
casting then left to cool slowly to room temperature The two solder alloys in the form of
rods were cold drawn into a wire of 08 mm diameter A part of each alloy was rolled into
a sheet of 05 mm thick for microstructure investigations Specimens with a gauge length
of 50 mm were pulled for tensile testing Prior to the tensile testing all specimens were
heat-treated at a temperature of 150 oC for 2 h Then they cooled slowly to room
temperature in order to stabilize the microstructure and remove the residual defects which
produced during the cold drawn process The densities ) of plain and composite solders
were determined using Archimedesrsquo principle Polished samples taken from various
sections of the solidified rods were weighted in air and when immersed in distilled water
using an electronic balance (AampD HM-202) with an accuracy of plusmn 00001 g
For metallographic observations as-solidified specimens were prepared initially
by mounting in cold epoxy They were finely polished using 3m and 1m alumina
powder which suspended in distilled water as a lubricant Final polishing to near mirror-
like surface was achieved using 03m diamond paste The as-polished samples were
chemically etched in a solution of 80 glycerin 10 nitric acid and 10 acetic acid for
a few seconds
The etched surfaces of the solder samples were observed in an optical microscope
The surface morphology of the samples was characterized by using field emission
scanning electron microscopy (FESEM) SU8000 series equipped with energy dispersive
X-ray analysis EDX X-ray diffractometry (Philips diffractometer (40 kV) with Cu K1
radiation (λ = 015406 nm) was used for XRD measurements XRD patterns were
recorded in the 2θ range of 20ondash90deg (step size 002deg per 1 second)
The melting temperature and fusion heating of solders were analyzed using a
differential scanning calorimetry (DSC) Shimadzu DSC-50 DSC measurements were
carried out at heating rate of 5 oCmin and high purity nitrogen gas pass through heating
chamber to avoid oxidation of samples Tensile testing was performed by straining each
specimen to fracture under a strain rate of 47times10-3
s-1
and testing temperature of 27 oC
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
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[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
1
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Highlights (for review)
1
Influence of ZnO nanoparticles addition on thermal analysis
microstructure evolution and tensile behavior of
Sn-50 wt Sb-05 wt Cu
Lead-free solder alloy
E A Eid a A N Fouda
b
(a) Basic Science Department Higher Technological Institute 44629 10th of Ramadan City Egypt
(b) Physics department Faculty of Science Suez-Canal University 41522 Ismailia Egypt
Abstract
Sn-5wtSb-05wtCu (plain SSC505) and Sn-5wtSb-05wtCu-05wt ZnO
(SSC-ZnO) composite solder alloys have been studied The variation in thermal behavior
microstructure and tensile characteristics associated with mixing of 05wt ZnO nano-
metric particles to plain SSC505 solder were investigated A slight increment in the
melting temperature [Tm= 089 oC] was recorded using differential scanning calorimetry
(DSC) after addition of ZnO X-ray diffraction (XRD) analysis confirmed the existence
of -Sn SbSn and Cu6Sn5 intermetallic compounds (IMCs) beside some of ZnO planes in
SSC-ZnO composite solder Field emission scanning electronic microscope (EF-SEM)
investigation of SSC-ZnO composite solder revealed a homogenous uniform distribution
size refinement of IMCs and -Sn grains Addition of ZnO nano-metric particles into the
plain SSC505 enhanced the yield stress YS by ~12 and improved the ultimate tensile
strength UTS by ~13 In addition adding ZnO nano-metric particles were found to be
effective for reducing ductility by 43 of the plain solder due to the refinement of -Sn
grains within SSC305-ZnO composite solder
Keywords Sn-5Sb solder composite lead free yield stress ultimate tensile stress
ManuscriptClick here to view linked References
2
1 Introduction
Sn based alloys is promising for advance electronics components connections as a
lead-free composite solder The substitution of toxic lead element (Pb) in the electronics
industry is one of the key issues in the current drive towards green ecology [1] Recently
high-temperature solders have been widely used in various types of applications like
assembling optoelectronic components automobile circuit boards circuit modules for
step soldering etc [2] Eutectic composition of goldndashtin (Au-20wt Sn) is the best
solder alloy for most applications in optoelectronic packaging because of its high creep
resistance wettability and good reliability Although goldndashtin solders have brittle phases
more expensive and has a melting point of 278 degC which is unacceptable for some
bonding applications [3 4] Certainly high soldering temperatures could damage the
properties of optical fibers and sensitive optoelectronics such as lasers light emitting
devices photodetectors or waveguide devices [5 2] To solve this problem great efforts
have been made to develop a new generation of solders with a low melting point
reasonable cost high dimension stability and supporting solder joints performance With
increasing miniaturization and more inputoutput terminals [6]
In high temperature applications Snndash5wt Sb solder is one of great potential
alternative material to push out the AundashSn solders and toxic Pb-rich solder alloys [7]
Snndash5wtSb solder has stable microstructure good mechanical properties highly creep
and corrosion resistance and good solderability (contact angle of about 43o) [7 8] To
enhance the performance of Tin-Antimony solders a third or more materials incorporated
as secondary phase with Sn-based matrix is one of the conventional approaches [9 10]
Micronano size metallic intermetallic or oxide particles are the most widely used in the
reinforcement of composite materials Consequently great numbers of researches focus
their study on the effect of adding reinforcement compound to lead free solder alloys
[11]
literature survey indicate that no attempt has been made to reinforce the binary
Sn-5wtSb solder or Sn-5wt Sb-05wt Cu solders by ZnO nanoparticle Meanwhile
a nano-size oxide intermetallic or ceramic particles are used to reinforce the composite
solders of Sn-Ag and Sn-Ag-Cu (SAC) Babaghorbani et al [12] added a different
3
addition of SnO2 nanopowders to Sn-35Ag lead-free solder alloy Taso et al [4] mixed a
different addition of TiO2 nano-size particles to Sn35Ag025Cu solder Their results
showed profound effects on the thermal characteristics of solder solidification and
reduction of the grain size Nai et al reported that the mechanical properties of the carbon
nano-tubescomposite solders improved significantly [11] However some efforts have
been made to reinforce Sn-35Ag solder with nanopowders of ZrO2 SiC Cu Co Ni Ag
and intermetallic particulates (Cu6Sn5 Ni3Sn4) using different processing methods
[612131415] Their results exhibit effective influence on the mechanical behavior
measurements indicated significant increases in yield strength ultimate tensile strength
and microhardness due to hinder the dislocation motion However the ductility decreased
with increasing amounts of nanoparticles additions Moreover the secondary phase must
be sufficiently fine bond well stable have a higher flow resistance than the alloy matrix
un-deformable and resist the fracture of solder joint
The literature survey revealed that no studies have been reported so far on lead-
free SSC505 solder joints containing nano-metric ZnO particles So the present work is
devoted for investigating the effect of addition of nano-metric ZnO particles on thermal
microstructure and tensile properties of Snndash5wt Sbndash05 wt Cu (SSC505) lead free
solder for trying to improve its microstructure and tensile properties
2 Experimental
Zinc oxide (ZnO) nanopowders were selected as a reinforcement oxide because of
its capability to form physical bond with metallic matrix Additionally the main
advantages of nano-sized ZnO particles are (i) it has density of (567 gcm3) which is
nearly close to density of Sn-5wtSb (7530 gcm3) (ii) high hardness when compared to
Sn-50Sb matrix (iii) chemical stability and (iv) low cost when compared to other
nanoparticles such as TiO2 Y2O3 SiC and ZrO2 [19]
A lead-free solder Sn-50 wt Sb-05 wt Cu (plain SSC505) solder alloy was
prepared by melting together Sn Sb and Cu ingots of 9999 purity SSC-ZnO
composite solder was prepared by mechanical mixing of 05 wt nano-metric ZnO
particles into plain SSC505 solder with subsequent remelting in a vacuum furnace at 300
oC for 2 hr to obtain a homogeneous composition A stainless steel mold was used for
4
casting then left to cool slowly to room temperature The two solder alloys in the form of
rods were cold drawn into a wire of 08 mm diameter A part of each alloy was rolled into
a sheet of 05 mm thick for microstructure investigations Specimens with a gauge length
of 50 mm were pulled for tensile testing Prior to the tensile testing all specimens were
heat-treated at a temperature of 150 oC for 2 h Then they cooled slowly to room
temperature in order to stabilize the microstructure and remove the residual defects which
produced during the cold drawn process The densities ) of plain and composite solders
were determined using Archimedesrsquo principle Polished samples taken from various
sections of the solidified rods were weighted in air and when immersed in distilled water
using an electronic balance (AampD HM-202) with an accuracy of plusmn 00001 g
For metallographic observations as-solidified specimens were prepared initially
by mounting in cold epoxy They were finely polished using 3m and 1m alumina
powder which suspended in distilled water as a lubricant Final polishing to near mirror-
like surface was achieved using 03m diamond paste The as-polished samples were
chemically etched in a solution of 80 glycerin 10 nitric acid and 10 acetic acid for
a few seconds
The etched surfaces of the solder samples were observed in an optical microscope
The surface morphology of the samples was characterized by using field emission
scanning electron microscopy (FESEM) SU8000 series equipped with energy dispersive
X-ray analysis EDX X-ray diffractometry (Philips diffractometer (40 kV) with Cu K1
radiation (λ = 015406 nm) was used for XRD measurements XRD patterns were
recorded in the 2θ range of 20ondash90deg (step size 002deg per 1 second)
The melting temperature and fusion heating of solders were analyzed using a
differential scanning calorimetry (DSC) Shimadzu DSC-50 DSC measurements were
carried out at heating rate of 5 oCmin and high purity nitrogen gas pass through heating
chamber to avoid oxidation of samples Tensile testing was performed by straining each
specimen to fracture under a strain rate of 47times10-3
s-1
and testing temperature of 27 oC
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
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[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
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(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
1
Influence of ZnO nanoparticles addition on thermal analysis
microstructure evolution and tensile behavior of
Sn-50 wt Sb-05 wt Cu
Lead-free solder alloy
E A Eid a A N Fouda
b
(a) Basic Science Department Higher Technological Institute 44629 10th of Ramadan City Egypt
(b) Physics department Faculty of Science Suez-Canal University 41522 Ismailia Egypt
Abstract
Sn-5wtSb-05wtCu (plain SSC505) and Sn-5wtSb-05wtCu-05wt ZnO
(SSC-ZnO) composite solder alloys have been studied The variation in thermal behavior
microstructure and tensile characteristics associated with mixing of 05wt ZnO nano-
metric particles to plain SSC505 solder were investigated A slight increment in the
melting temperature [Tm= 089 oC] was recorded using differential scanning calorimetry
(DSC) after addition of ZnO X-ray diffraction (XRD) analysis confirmed the existence
of -Sn SbSn and Cu6Sn5 intermetallic compounds (IMCs) beside some of ZnO planes in
SSC-ZnO composite solder Field emission scanning electronic microscope (EF-SEM)
investigation of SSC-ZnO composite solder revealed a homogenous uniform distribution
size refinement of IMCs and -Sn grains Addition of ZnO nano-metric particles into the
plain SSC505 enhanced the yield stress YS by ~12 and improved the ultimate tensile
strength UTS by ~13 In addition adding ZnO nano-metric particles were found to be
effective for reducing ductility by 43 of the plain solder due to the refinement of -Sn
grains within SSC305-ZnO composite solder
Keywords Sn-5Sb solder composite lead free yield stress ultimate tensile stress
ManuscriptClick here to view linked References
2
1 Introduction
Sn based alloys is promising for advance electronics components connections as a
lead-free composite solder The substitution of toxic lead element (Pb) in the electronics
industry is one of the key issues in the current drive towards green ecology [1] Recently
high-temperature solders have been widely used in various types of applications like
assembling optoelectronic components automobile circuit boards circuit modules for
step soldering etc [2] Eutectic composition of goldndashtin (Au-20wt Sn) is the best
solder alloy for most applications in optoelectronic packaging because of its high creep
resistance wettability and good reliability Although goldndashtin solders have brittle phases
more expensive and has a melting point of 278 degC which is unacceptable for some
bonding applications [3 4] Certainly high soldering temperatures could damage the
properties of optical fibers and sensitive optoelectronics such as lasers light emitting
devices photodetectors or waveguide devices [5 2] To solve this problem great efforts
have been made to develop a new generation of solders with a low melting point
reasonable cost high dimension stability and supporting solder joints performance With
increasing miniaturization and more inputoutput terminals [6]
In high temperature applications Snndash5wt Sb solder is one of great potential
alternative material to push out the AundashSn solders and toxic Pb-rich solder alloys [7]
Snndash5wtSb solder has stable microstructure good mechanical properties highly creep
and corrosion resistance and good solderability (contact angle of about 43o) [7 8] To
enhance the performance of Tin-Antimony solders a third or more materials incorporated
as secondary phase with Sn-based matrix is one of the conventional approaches [9 10]
Micronano size metallic intermetallic or oxide particles are the most widely used in the
reinforcement of composite materials Consequently great numbers of researches focus
their study on the effect of adding reinforcement compound to lead free solder alloys
[11]
literature survey indicate that no attempt has been made to reinforce the binary
Sn-5wtSb solder or Sn-5wt Sb-05wt Cu solders by ZnO nanoparticle Meanwhile
a nano-size oxide intermetallic or ceramic particles are used to reinforce the composite
solders of Sn-Ag and Sn-Ag-Cu (SAC) Babaghorbani et al [12] added a different
3
addition of SnO2 nanopowders to Sn-35Ag lead-free solder alloy Taso et al [4] mixed a
different addition of TiO2 nano-size particles to Sn35Ag025Cu solder Their results
showed profound effects on the thermal characteristics of solder solidification and
reduction of the grain size Nai et al reported that the mechanical properties of the carbon
nano-tubescomposite solders improved significantly [11] However some efforts have
been made to reinforce Sn-35Ag solder with nanopowders of ZrO2 SiC Cu Co Ni Ag
and intermetallic particulates (Cu6Sn5 Ni3Sn4) using different processing methods
[612131415] Their results exhibit effective influence on the mechanical behavior
measurements indicated significant increases in yield strength ultimate tensile strength
and microhardness due to hinder the dislocation motion However the ductility decreased
with increasing amounts of nanoparticles additions Moreover the secondary phase must
be sufficiently fine bond well stable have a higher flow resistance than the alloy matrix
un-deformable and resist the fracture of solder joint
The literature survey revealed that no studies have been reported so far on lead-
free SSC505 solder joints containing nano-metric ZnO particles So the present work is
devoted for investigating the effect of addition of nano-metric ZnO particles on thermal
microstructure and tensile properties of Snndash5wt Sbndash05 wt Cu (SSC505) lead free
solder for trying to improve its microstructure and tensile properties
2 Experimental
Zinc oxide (ZnO) nanopowders were selected as a reinforcement oxide because of
its capability to form physical bond with metallic matrix Additionally the main
advantages of nano-sized ZnO particles are (i) it has density of (567 gcm3) which is
nearly close to density of Sn-5wtSb (7530 gcm3) (ii) high hardness when compared to
Sn-50Sb matrix (iii) chemical stability and (iv) low cost when compared to other
nanoparticles such as TiO2 Y2O3 SiC and ZrO2 [19]
A lead-free solder Sn-50 wt Sb-05 wt Cu (plain SSC505) solder alloy was
prepared by melting together Sn Sb and Cu ingots of 9999 purity SSC-ZnO
composite solder was prepared by mechanical mixing of 05 wt nano-metric ZnO
particles into plain SSC505 solder with subsequent remelting in a vacuum furnace at 300
oC for 2 hr to obtain a homogeneous composition A stainless steel mold was used for
4
casting then left to cool slowly to room temperature The two solder alloys in the form of
rods were cold drawn into a wire of 08 mm diameter A part of each alloy was rolled into
a sheet of 05 mm thick for microstructure investigations Specimens with a gauge length
of 50 mm were pulled for tensile testing Prior to the tensile testing all specimens were
heat-treated at a temperature of 150 oC for 2 h Then they cooled slowly to room
temperature in order to stabilize the microstructure and remove the residual defects which
produced during the cold drawn process The densities ) of plain and composite solders
were determined using Archimedesrsquo principle Polished samples taken from various
sections of the solidified rods were weighted in air and when immersed in distilled water
using an electronic balance (AampD HM-202) with an accuracy of plusmn 00001 g
For metallographic observations as-solidified specimens were prepared initially
by mounting in cold epoxy They were finely polished using 3m and 1m alumina
powder which suspended in distilled water as a lubricant Final polishing to near mirror-
like surface was achieved using 03m diamond paste The as-polished samples were
chemically etched in a solution of 80 glycerin 10 nitric acid and 10 acetic acid for
a few seconds
The etched surfaces of the solder samples were observed in an optical microscope
The surface morphology of the samples was characterized by using field emission
scanning electron microscopy (FESEM) SU8000 series equipped with energy dispersive
X-ray analysis EDX X-ray diffractometry (Philips diffractometer (40 kV) with Cu K1
radiation (λ = 015406 nm) was used for XRD measurements XRD patterns were
recorded in the 2θ range of 20ondash90deg (step size 002deg per 1 second)
The melting temperature and fusion heating of solders were analyzed using a
differential scanning calorimetry (DSC) Shimadzu DSC-50 DSC measurements were
carried out at heating rate of 5 oCmin and high purity nitrogen gas pass through heating
chamber to avoid oxidation of samples Tensile testing was performed by straining each
specimen to fracture under a strain rate of 47times10-3
s-1
and testing temperature of 27 oC
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
2
1 Introduction
Sn based alloys is promising for advance electronics components connections as a
lead-free composite solder The substitution of toxic lead element (Pb) in the electronics
industry is one of the key issues in the current drive towards green ecology [1] Recently
high-temperature solders have been widely used in various types of applications like
assembling optoelectronic components automobile circuit boards circuit modules for
step soldering etc [2] Eutectic composition of goldndashtin (Au-20wt Sn) is the best
solder alloy for most applications in optoelectronic packaging because of its high creep
resistance wettability and good reliability Although goldndashtin solders have brittle phases
more expensive and has a melting point of 278 degC which is unacceptable for some
bonding applications [3 4] Certainly high soldering temperatures could damage the
properties of optical fibers and sensitive optoelectronics such as lasers light emitting
devices photodetectors or waveguide devices [5 2] To solve this problem great efforts
have been made to develop a new generation of solders with a low melting point
reasonable cost high dimension stability and supporting solder joints performance With
increasing miniaturization and more inputoutput terminals [6]
In high temperature applications Snndash5wt Sb solder is one of great potential
alternative material to push out the AundashSn solders and toxic Pb-rich solder alloys [7]
Snndash5wtSb solder has stable microstructure good mechanical properties highly creep
and corrosion resistance and good solderability (contact angle of about 43o) [7 8] To
enhance the performance of Tin-Antimony solders a third or more materials incorporated
as secondary phase with Sn-based matrix is one of the conventional approaches [9 10]
Micronano size metallic intermetallic or oxide particles are the most widely used in the
reinforcement of composite materials Consequently great numbers of researches focus
their study on the effect of adding reinforcement compound to lead free solder alloys
[11]
literature survey indicate that no attempt has been made to reinforce the binary
Sn-5wtSb solder or Sn-5wt Sb-05wt Cu solders by ZnO nanoparticle Meanwhile
a nano-size oxide intermetallic or ceramic particles are used to reinforce the composite
solders of Sn-Ag and Sn-Ag-Cu (SAC) Babaghorbani et al [12] added a different
3
addition of SnO2 nanopowders to Sn-35Ag lead-free solder alloy Taso et al [4] mixed a
different addition of TiO2 nano-size particles to Sn35Ag025Cu solder Their results
showed profound effects on the thermal characteristics of solder solidification and
reduction of the grain size Nai et al reported that the mechanical properties of the carbon
nano-tubescomposite solders improved significantly [11] However some efforts have
been made to reinforce Sn-35Ag solder with nanopowders of ZrO2 SiC Cu Co Ni Ag
and intermetallic particulates (Cu6Sn5 Ni3Sn4) using different processing methods
[612131415] Their results exhibit effective influence on the mechanical behavior
measurements indicated significant increases in yield strength ultimate tensile strength
and microhardness due to hinder the dislocation motion However the ductility decreased
with increasing amounts of nanoparticles additions Moreover the secondary phase must
be sufficiently fine bond well stable have a higher flow resistance than the alloy matrix
un-deformable and resist the fracture of solder joint
The literature survey revealed that no studies have been reported so far on lead-
free SSC505 solder joints containing nano-metric ZnO particles So the present work is
devoted for investigating the effect of addition of nano-metric ZnO particles on thermal
microstructure and tensile properties of Snndash5wt Sbndash05 wt Cu (SSC505) lead free
solder for trying to improve its microstructure and tensile properties
2 Experimental
Zinc oxide (ZnO) nanopowders were selected as a reinforcement oxide because of
its capability to form physical bond with metallic matrix Additionally the main
advantages of nano-sized ZnO particles are (i) it has density of (567 gcm3) which is
nearly close to density of Sn-5wtSb (7530 gcm3) (ii) high hardness when compared to
Sn-50Sb matrix (iii) chemical stability and (iv) low cost when compared to other
nanoparticles such as TiO2 Y2O3 SiC and ZrO2 [19]
A lead-free solder Sn-50 wt Sb-05 wt Cu (plain SSC505) solder alloy was
prepared by melting together Sn Sb and Cu ingots of 9999 purity SSC-ZnO
composite solder was prepared by mechanical mixing of 05 wt nano-metric ZnO
particles into plain SSC505 solder with subsequent remelting in a vacuum furnace at 300
oC for 2 hr to obtain a homogeneous composition A stainless steel mold was used for
4
casting then left to cool slowly to room temperature The two solder alloys in the form of
rods were cold drawn into a wire of 08 mm diameter A part of each alloy was rolled into
a sheet of 05 mm thick for microstructure investigations Specimens with a gauge length
of 50 mm were pulled for tensile testing Prior to the tensile testing all specimens were
heat-treated at a temperature of 150 oC for 2 h Then they cooled slowly to room
temperature in order to stabilize the microstructure and remove the residual defects which
produced during the cold drawn process The densities ) of plain and composite solders
were determined using Archimedesrsquo principle Polished samples taken from various
sections of the solidified rods were weighted in air and when immersed in distilled water
using an electronic balance (AampD HM-202) with an accuracy of plusmn 00001 g
For metallographic observations as-solidified specimens were prepared initially
by mounting in cold epoxy They were finely polished using 3m and 1m alumina
powder which suspended in distilled water as a lubricant Final polishing to near mirror-
like surface was achieved using 03m diamond paste The as-polished samples were
chemically etched in a solution of 80 glycerin 10 nitric acid and 10 acetic acid for
a few seconds
The etched surfaces of the solder samples were observed in an optical microscope
The surface morphology of the samples was characterized by using field emission
scanning electron microscopy (FESEM) SU8000 series equipped with energy dispersive
X-ray analysis EDX X-ray diffractometry (Philips diffractometer (40 kV) with Cu K1
radiation (λ = 015406 nm) was used for XRD measurements XRD patterns were
recorded in the 2θ range of 20ondash90deg (step size 002deg per 1 second)
The melting temperature and fusion heating of solders were analyzed using a
differential scanning calorimetry (DSC) Shimadzu DSC-50 DSC measurements were
carried out at heating rate of 5 oCmin and high purity nitrogen gas pass through heating
chamber to avoid oxidation of samples Tensile testing was performed by straining each
specimen to fracture under a strain rate of 47times10-3
s-1
and testing temperature of 27 oC
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
3
addition of SnO2 nanopowders to Sn-35Ag lead-free solder alloy Taso et al [4] mixed a
different addition of TiO2 nano-size particles to Sn35Ag025Cu solder Their results
showed profound effects on the thermal characteristics of solder solidification and
reduction of the grain size Nai et al reported that the mechanical properties of the carbon
nano-tubescomposite solders improved significantly [11] However some efforts have
been made to reinforce Sn-35Ag solder with nanopowders of ZrO2 SiC Cu Co Ni Ag
and intermetallic particulates (Cu6Sn5 Ni3Sn4) using different processing methods
[612131415] Their results exhibit effective influence on the mechanical behavior
measurements indicated significant increases in yield strength ultimate tensile strength
and microhardness due to hinder the dislocation motion However the ductility decreased
with increasing amounts of nanoparticles additions Moreover the secondary phase must
be sufficiently fine bond well stable have a higher flow resistance than the alloy matrix
un-deformable and resist the fracture of solder joint
The literature survey revealed that no studies have been reported so far on lead-
free SSC505 solder joints containing nano-metric ZnO particles So the present work is
devoted for investigating the effect of addition of nano-metric ZnO particles on thermal
microstructure and tensile properties of Snndash5wt Sbndash05 wt Cu (SSC505) lead free
solder for trying to improve its microstructure and tensile properties
2 Experimental
Zinc oxide (ZnO) nanopowders were selected as a reinforcement oxide because of
its capability to form physical bond with metallic matrix Additionally the main
advantages of nano-sized ZnO particles are (i) it has density of (567 gcm3) which is
nearly close to density of Sn-5wtSb (7530 gcm3) (ii) high hardness when compared to
Sn-50Sb matrix (iii) chemical stability and (iv) low cost when compared to other
nanoparticles such as TiO2 Y2O3 SiC and ZrO2 [19]
A lead-free solder Sn-50 wt Sb-05 wt Cu (plain SSC505) solder alloy was
prepared by melting together Sn Sb and Cu ingots of 9999 purity SSC-ZnO
composite solder was prepared by mechanical mixing of 05 wt nano-metric ZnO
particles into plain SSC505 solder with subsequent remelting in a vacuum furnace at 300
oC for 2 hr to obtain a homogeneous composition A stainless steel mold was used for
4
casting then left to cool slowly to room temperature The two solder alloys in the form of
rods were cold drawn into a wire of 08 mm diameter A part of each alloy was rolled into
a sheet of 05 mm thick for microstructure investigations Specimens with a gauge length
of 50 mm were pulled for tensile testing Prior to the tensile testing all specimens were
heat-treated at a temperature of 150 oC for 2 h Then they cooled slowly to room
temperature in order to stabilize the microstructure and remove the residual defects which
produced during the cold drawn process The densities ) of plain and composite solders
were determined using Archimedesrsquo principle Polished samples taken from various
sections of the solidified rods were weighted in air and when immersed in distilled water
using an electronic balance (AampD HM-202) with an accuracy of plusmn 00001 g
For metallographic observations as-solidified specimens were prepared initially
by mounting in cold epoxy They were finely polished using 3m and 1m alumina
powder which suspended in distilled water as a lubricant Final polishing to near mirror-
like surface was achieved using 03m diamond paste The as-polished samples were
chemically etched in a solution of 80 glycerin 10 nitric acid and 10 acetic acid for
a few seconds
The etched surfaces of the solder samples were observed in an optical microscope
The surface morphology of the samples was characterized by using field emission
scanning electron microscopy (FESEM) SU8000 series equipped with energy dispersive
X-ray analysis EDX X-ray diffractometry (Philips diffractometer (40 kV) with Cu K1
radiation (λ = 015406 nm) was used for XRD measurements XRD patterns were
recorded in the 2θ range of 20ondash90deg (step size 002deg per 1 second)
The melting temperature and fusion heating of solders were analyzed using a
differential scanning calorimetry (DSC) Shimadzu DSC-50 DSC measurements were
carried out at heating rate of 5 oCmin and high purity nitrogen gas pass through heating
chamber to avoid oxidation of samples Tensile testing was performed by straining each
specimen to fracture under a strain rate of 47times10-3
s-1
and testing temperature of 27 oC
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
4
casting then left to cool slowly to room temperature The two solder alloys in the form of
rods were cold drawn into a wire of 08 mm diameter A part of each alloy was rolled into
a sheet of 05 mm thick for microstructure investigations Specimens with a gauge length
of 50 mm were pulled for tensile testing Prior to the tensile testing all specimens were
heat-treated at a temperature of 150 oC for 2 h Then they cooled slowly to room
temperature in order to stabilize the microstructure and remove the residual defects which
produced during the cold drawn process The densities ) of plain and composite solders
were determined using Archimedesrsquo principle Polished samples taken from various
sections of the solidified rods were weighted in air and when immersed in distilled water
using an electronic balance (AampD HM-202) with an accuracy of plusmn 00001 g
For metallographic observations as-solidified specimens were prepared initially
by mounting in cold epoxy They were finely polished using 3m and 1m alumina
powder which suspended in distilled water as a lubricant Final polishing to near mirror-
like surface was achieved using 03m diamond paste The as-polished samples were
chemically etched in a solution of 80 glycerin 10 nitric acid and 10 acetic acid for
a few seconds
The etched surfaces of the solder samples were observed in an optical microscope
The surface morphology of the samples was characterized by using field emission
scanning electron microscopy (FESEM) SU8000 series equipped with energy dispersive
X-ray analysis EDX X-ray diffractometry (Philips diffractometer (40 kV) with Cu K1
radiation (λ = 015406 nm) was used for XRD measurements XRD patterns were
recorded in the 2θ range of 20ondash90deg (step size 002deg per 1 second)
The melting temperature and fusion heating of solders were analyzed using a
differential scanning calorimetry (DSC) Shimadzu DSC-50 DSC measurements were
carried out at heating rate of 5 oCmin and high purity nitrogen gas pass through heating
chamber to avoid oxidation of samples Tensile testing was performed by straining each
specimen to fracture under a strain rate of 47times10-3
s-1
and testing temperature of 27 oC
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
5
3 Results and Discussion
31 Thermal analysis
For the soldering process the melting temperature of solders is a crucial
parameter because it is main factor in deciding the process temperature The melting
point of the prepared plain and composite solders was accurately determined by DSC
thermograms Fig 1(a-b) shows the endothermic peak as a function of temperature of the
prepared solders during the heating rate of 5 oCmin The melting temperature of the plain
and composite solders is 23738 and 23827 oC respectively This result is agree with
other previous studies on SAC composite solders [4 20 21] The slightly increase in
melting point of the SAC355 composite solder can be attributed to the effect of the nano-
sized ZnO particles on the rate of solidification Such particles may serve as retardation
sites for the solidification process of the IMCs [22]
Additionally The endothermic peak of DSC curve in Fig 1 is initiated at solidus
temperature Ts and ended at liquidus temperature TL that are estimated by using intersection
point between the horizontal tangent of baseline and the tangent line for each side of
endothermic peak The features of endothermic peak of synthesized solder alloys are
summarized in Table 1 For plain SSC505 and composite solders there is a significant
difference between solidus temperatures Ts = 211oC) and a negligible difference
between liquidus temperatures TL = 013 oC) For any alloy to be worthwhile as a solder
for electronics industry it must possess certain specific quantities like melting range or pasty
range which is an essential parameter to estimates the time required for finishing the soldering
process The pasty range of plain and composite solder alloys are 2388 and 2190 degC
respectively The results reflect that the solidus and liquidus temperature of the synthesized
solder alloys are lower than Sn-5wt Sb binary solder alloy On the other hand Sn-5wt Sb
has the smallest pasty range of 100 degC and a higher melting temperature of 246 oC that
provides a useful compromise between them [9 23]
The calculated values of fusion heat of both solder alloys are tabulated in table 1 The
heat of fusion of plain is higher than composite solder alloy [HSSC505 ndash HSSC-ZnO = 3656 Jg)
Indeed The heat of fusion H) plays an important role in packaging technology Therefore
SSC-ZnO composite solder alloy is considered as a promising solder for saving energy
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
6
andor the consumed energy for its melting process is lower than Sn-5wt Sb HSn-5Sb = 1405 Jg)
by 37 [9]
32 Microstructure evolution
321 XRD analysis
Representative x-ray diffraction of plain solder and composite solders are shown in Fig
2a-b The diffraction pattern exhibits sharp peaks which are attributed to the crystalline
nature of the two samples The qualitative analysis of the peaks reflects the existence of
the body center tetragonal β-Sn-rich phase The diffraction planes (101) (110) (021) and
(202) at angles of (2 293o 419
o 423
o and 605
o) respectively confirm the existence
of cubic SbSn IMC Regarding to Fig 2b it consists of the same phases which exist in
the plain solder (Fig 2a) On the other hand the emergence of (101) and (002) peaks at
angles 327 o
and 343 o
of ZnO is an evident of ZnO nanoparticles dispersion within -Sn
matrix Moreover the disappearance of some ZnO peaks can be attributed to interfere of
its peaks with the peaks of -Sn phases However a slow speed scan (002 degs)
conducted on the plain and composite solders revealed several peaks at angles of (2=
3036 4288o 5365 5758 6233 and 7971) that corresponding to Cu6Sn5 IMC The
small peaks of Cu6Sn5 IMC assigned to the low volume fraction of the copper in the
solder matrix Fig 3 shows a comparison between diffraction peaks (200) and (101) of
-Sn for plain and composite solders One can observe that the diffraction lines are
slightly shifted towards lower angles indicating a refinement of -Sn grain size with
addition of ZnO nano-metric particles [24 25]
It is well known that the broadening of XRD peaks of an alloy is caused not only by the
small grain size but also by the lattice micro-deformations of the alloy [15] The
crystallite size d and an approximate upper limit of the lattice strain can be evaluated by
XRD peaks analysis according to the Williamson-Hall formula [25]
sin2cos d
K (1)
where β is the peak width at half the maximum intensity (FWHM) in radian of the main
peak θ is the Bragg angle K is the Scherrer constant (09) η is average of lattice strain
and λ is the X-ray wavelength (λCu = 0154056 nm)
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
7
When β cosθ was plotted against sinθ using main peaks of -Sn a straight line is
obtained with the slope of 2η and the intercept as (09λd) Results of linear fitting of
extracting data summarized in table 2 The crystallite size of Sn-based supersaturated
solid solution was measured to be 116 and 99 nm for the plain and composite solders
respectively From table 2 one observed that the average of lattice strain of -Sn phase
for SSC-ZnO composite solder was higher than plain solder The lattice strains observed
in the solid-solution phases during solidification are caused not only by defect formation
but also by another factor this strain was originally introduced during sample
preparation particularly in crushing of the sample [26] The peaks in the X-ray
diffraction (XRD) patterns for composite solder broadened This broadening was
supposed to be due to lattice strain Moreover lattice strain is introduced upon phase
transition from coarsen -Sn phase to refinement phase The anisotropic strain in the
diffraction peaks has the same orientation as the Burgers dislocation vectors [24] That
indicating the strain is accompanied by density dislocations which is closely related to
defect formation
3 2 2 Metallographic Analysis
Results of microstructural characteristics of the plain and composite solders are discussed
in terms of (i) grain morphology size and homogenous distribution (ii) the presence
distribution and morphology of the second phase particles and (iii) percentage of
porosity cracks and voids Fig 4 shows two optical images (OM) with same powers of
magnification for the as-cast plain and composite solders that solidified at cooling rate of
2 oCmin Results revealed the plain solder composed of larger non-equiaxed grains non-
uniform solidification microstructure the large dark islands are rich-Sn grains with grain
size in the range of 100-140 m The bright region between Sn grains actually consists of
mixture of lamellar phases of Sn matrix phase (dark phase) and the circular bright dot
phase termed as SnSb IMC Moreover the finer rich-Sn grains within composite solder
reveal near-equiaxed grains with average grain size in the range of 90-50 m
approximately homogenous distribution and narrower dendrites are shown in Fig 4b
The decrement of average grain size of -Sn phase with addition of 05 wt Zinc nano-
metric particles can be attributed to its pinning action on grain boundaries and by the
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
8
second phases resulting in limited grain growth [18] In Fig 4b the -Sn phase is not
only composed of pure Sn crystals but rather contain several of tiny intermetallic particles
that scattered throughout Sn matrix Furthermore with higher magnification of field
emission scanning electronic microscope (FE-SEM) the precipitated particles like as
platelets or scallop morphology of the Cu6Sn5 IMC are observed in both solders (see Fig 5a-b)
The precipitation of IMCs within -Sn matrix is confirmed by utilizing energy
dispersion X-ray (EDX) analysis the eutectic areas were found to contain Zn O Cu Sb
and Sn elements in composite solder Thus it can be concluded that the network eutectic
areas are Cu6Sn5 and SbSn besides the ZnO particles as shown in Figs 6a-c Stichometric
analysis of EDX data implies the existence of Sn Sb and Cu atoms and termed IMCs
according to the atomic ratio of each element in compound [see table 3] An identified
reduction in size of SbSn Cu6Sn5 IMCs was confirmed by FE-SEM images (see Fig5a-
b) This was assigned to ZnO nanoparticles which incorporated into the solder matrix
According to the adsorption theory increasing the adsorption of elements could decrease
the surface energy andor decrease the growth of IMCs size [14] For the composite
solder the micro-size of SbSn and Cu6Sn5 IMCs are larger than the size of the ZnO nano-
metric particles Therefore the incorporation of active surface ZnO nano-metric particles
refines the size of IMCs Previously similar behavior has been reported [20 22]
The Curve of EDX analyses of a selected area (+) in Fig 6b shows that the
Cu6Sn5 IMC contain 701 at of Sb element [see table 3] The existence of antimony
atoms inside the Cu6Sn5 grain confirms that tin-antimony intermetallic compound might
be the nucleating agent acting as a heterogeneous nucleation of Cu6Sn5 grains The
proposed mechanism for the effect of Sb on IMC formation can be summarized as
follows because Sb has higher affinity to the constituent element of Sn in SnndashCundashSb
ternary system it will reduce the activity of Sn at the Sn-Cu interface by forming SnSb
compound resulting in a decreased driving force for CundashSn IMC formation [27] SnSb
particles may be initially formed and finely dispersed in the molten solder and then some
of them precipitate and become the heterogeneous nucleation sites of Cu6Sn5 IMC
According to the theory of heterogeneous nucleation the Cu6Sn5 phase prefers to
nucleate on the SnSb surface in order to reduce the thermodynamic barrier [28] The
increase in nucleation probability of Cu6Sn5 grains consequently lends to the refinement
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
9
of the grains As a result the small and uniform grains obtained in the composite solder
slow down the ripening rate and the refinement effect is achieved
33 Density measurement
The results of density measurements were conducted on the solidified plain and
composite solders In Table 4 all the density values were very close which is predicted
because of the slight difference in density between Sn and ZnO The porosity
measurement was theoretically calculated [12 24] The value of porosity implied that the
higher percentage of pores exists in the case of SSC-ZnO composite solder
34 Strengthening effect
Fig 7 shows the typical tensile stressndashstrain curves of plain and composite solders
stretched with constant strain rate of 74times10-3
s-1
and performed 27oC The stressndashstrain
obtained curves exhibited plateau shaped with steady stable flow stress of the two solder
alloys It was found to be strongly dependent on alloy composition of the tested material
Furthermore steady state flow of composite solder was higher than plain solder by ~12
This observation can be explained as during plastic deformation the solder alloy suffers
from simultaneous work hardening and dynamic recovery [17] They have contrary
influences on the mechanical deformation of the alloy Hence the steady stable stresses
seem to be represented equal combination effects for those Additionally existences of
the ZnO nanoparticles must increase dislocation densities because of their restrict effect
for the motion of dislocation besides the dispersion hardening mechanism of the IMCs
Therefore the dislocations have much less freedom that cant pass through climb and
cross slip planes that lead to increase the flow stresses [20]
The average values of Young modulus E ultimate tensile strength UTS yield
stress YS fracture stress f and ductility ɛ of the synthesized solder alloys were tabulated
in Table 5 Addition of 05 wt ZnO nanopowders was found to have a significant effect
on the tensile parameters Detectable increments in E by 52 UTS by 11 and in YS by
13 were recorded However the ductility of SSC-ZnO composite solder was less than
plain solder by 43 Improvement in the tensile parameters was achieved because of
presence of ZnO nanopowders as reinforcement agent The nano-sized particles are
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
10
dispersed uniformly and homogeneously distributed in Sn matrix which provide high
barrier by impeding grain boundary sliding and dislocation movement
The reinforcement nanoparticles play two different roles They may strengthen the
alloy matrix and enhance the formation of large dislocation pile-ups at grain boundaries
Simultaneously the higher friction of nanoparticles generates microcracks nucleation at
the interface between Sn matrix and IMCs which speed up the failure process [29 30]
So ductility decreased because of a large amount of microporosity throughout grain
boundaries and crack nucleation sites in the form of hard and brittle ZnO nanopowders
[20 24 31]
Eventually the influence of the nano-metric size particles can be summarized in
(i) pinning grain boundaries and thus impeding sliding of the grain boundaries (ii) the
increase of dislocation densities and obstacles to restrict the motion of dislocation and
(iii) the dispersion hardening mechanism of the IMCs and ZnO nanopowders [30 32]
4 Conclusion
ZnO nanoparticles dissolve and react with the molten SSC505 solder at 600 oC during the
fabrication of SSC-ZnO composite solder Thermal behavior microstructure and
mechanical characteristics were discussed The melting point of SSC505 solder is slightly
increased after the addition of ZnO nanoparticles X-ray diffraction analysis of SSC-ZnO
confirms the existence of SbSn Cu6Sn5 IMCs and ZnO The microstructure observations
revealed finer IMCs due to active surface area of ZnO nanoparticles that supports the
strong adsorption effect According to the tensile measurements an improvement in UTS
and YS were established However the ductility of SSC-ZnO composite solder was
decreased The variation in tensile properties is attributed to ZnO pinning effect which
obstructed dislocations and migration of grain boundaries
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
11
5 Reference
[1] M Abtew G Selvaduray Mater Sci Eng 27 (2000) 95-141
[2] V Chidambaram J Hattle J Hald Microelectronic Engineering 88 (2011) 981- 989
[3] H Mavoori S Jin J Electron Mater 27 No (11) (1998) 1216-1222
[4] LC Tsao SY Chang Materials and Design 31 (2010) 990-993
[5] H Mavoori JOM 52 No 6 (2000) 29
[6] J Shen Y C Chan Microelectronic Reliability 49 (2009) 223-234
[7] J Rodney McCabe and E Morris Fine Metallurgical and Materials Transactions A
No 33A (2002) 1531-1593
[8] M D Mathew H Yang S Movva and K L Morty Metallurgical and Materials
Transactions A No 36A (2005) 99-105
[9] A A El-Daly Y Swilem A E Hammad Journal of Alloy and Compounds 471
(2009) 98-104
[10] H Mavoori S Jin JOM 52 No 6 (2000) 30-32
[11] S M L Nai J Weib M Gupta Material Science and Engineering A No 423A
(2006) 166-169
[12] P Babaghorbani S M L Nai M Gupta Journal of Material Science Mater
Electron 20 (2009) 571-576
[14] J Shen Y C Chan Journal of Alloys and Compounds 477 (2009) 552-559
[15] J Shen Y C Liu Y J Han Y M Tian and H X Gao Journal of electronic
material 35 No 8 (2006) 1672-1679
[16] P Babaghorbani S M L Nai M Gupta Journal of Alloys and Compounds 478
(2009) 458-461
[17] A A El-Daly G S Al-Ganainy A Fawzy M J Younis Materials and Design 55
(2014) 837-845
[18] M E Alam S M L Nai and M Gupta Journal of Alloys and Compounds 476
(2009) 199-206
[19] Hadis Morkoccedil and Uumlmit Oumlzguumlr Zinc Oxide Fundamentals Materials and Device
Technology WILEY-VCH Verlag GmbH amp Co KGaA Weinheim (2009)
ISBN978-3-527-40813-9
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
12
[20] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Journal of
Material Science Mater Electron 24 (2013) 3210-3218
[21] L C Tsao S Y Chang C I Lee W H Sun C H Huang Material and Design
31 (2010) 990-993
[22] A Fawzy S A Fayek M Sobhy E Nassr M M Mousa G Saad Materials Science and
Engineering A 603 (2014) 1-10
[23] M M EL-Bahay M E EL-Mossalamy M Mahdy and A A Bahga phys stat sol
(a) 198 No 1 (2003) 76-90
[24] B D Cullity Elements of X-ray Diffraction (second edition) Addison-Wesley
Publishing Company Inc MA USA (1978)
[25] N Hosseini M H Abbasi F Karimzadeh M H Enayati Materials Science and
Engineering A 525 (2009) 107-111
[26] S Yamazaki J Nakamura K Sakaki Y Nakamura and E Akiba Materials
Transactions 52 No 4 (2011) 586-590
[27] B L Chen G Y Li Thin Solid Films 462-463 (2004) 395-401
[28] W Juumlrn P Schmelzer Nucleation Theory and Applications WILEY-VCH Verlag
GmbH amp Co (2005) ISBN-13 978-3-527-40469-8 ISBN-10 3-527-40469-4
[29] K S Tun M Gupta Composite Science Technology 67 (2007) 2657
[30] S M L Nai J Wei M Gupta Thin Solid Films 504 (2006) 401-404
[31] S M L Nai J Wei M Gupta Journal Electronic Material 35 No 7 (2006) 1518-
1522
[32] S Ugandhar N Srikanth M Gupta S K Sinha Advanced Engineering Material 6
No 12 (2004) 957-964
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
13
Figure caption
Fig 1 DSC curves of (a) SSC505 and (b) SSC-ZnO composite solder alloys
Fig 2 XRD profiles of (a) SSC505 solder and (b) SSC-ZnO composite solder alloys
Fig 3 Comparison between diffraction peaks of (200) and (101) of -Sn for plain and
composite solders
Fig4 Optical images showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 5 FE-SEM micrographs showing the grains of (a) SSC505 solder and (b) SSC-ZnO
composite solder alloys
Fig 6 High-magnification FE-SEM micrographs with corresponding EDX of
intermetallic compound of (a) SbSn (b) Cu6Sn5 (c) eutectic region in SSC-ZnO
composite solder
Fig 7 StressndashStrain curves showing the effect of adding 05 wt ZnO nanoparticles to
SSC505 plain solder alloy
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
14
Highlights
1- Melting point of SSC505-ZnO composite solder is slightly increased by 089 0C
compared with the plain SSC505 solder
2- XRD and EDX analysis reflect the presence of SbSn Cu6Sn5 IMCs
3- EF-SEM images of SSC-ZnO composite solder revealed homogenous uniform
distribution of -Sn grains and fine IMC particles
4- A detectable improvement in the Young modulus ultimate tensile strength and
yield strength were observed after addition of 05wt ZnO nano-metric particles
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
Table1 Comparison of melting temperatures(Tm) solidus temperature (Ts)
liquidus temperature (TL) pasty range T) and heat of fusion ( H) for various
solder alloys
Material Tm oC Ts
oC TL
oC T= TL-TS
oC
H
(kJkg)
Reference
Sn-5Sb
SSC505
SSC-ZnO
246
23738
23827
240
22345
22556
249
24733
24746
90
2388
2190
141
12552
8896
El-Dally[9]
This study
This study
Table 2 The average crystallite size (d) and lattice strain () for plain SSC505 solder
SSC-ZnO composite solder and SbSn Cu6Sn5 IMCs
-Sn (Matrix) SbSn (IMC)
Cu6Sn5 (IMC)
SSC505
(R2 = 0042)
R2
R
R
SSC-ZnO
(R2 = 0061)
SSC505
(R2 = 03337)
SSC-ZnO
(R2 = 06108)
SSC505
(R2= 04255)
SSC-ZnO
(R2= 07218)
d(nm) times d(nm)
(nm)
times d (nm) times
d(nm) times
d(nm) times
d (nm) times
116 10 99 55 693 300 116 565 754 346 205 588
Table
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
Table 3 Energy dispersive R-Ray (EDX) analysis
Zone
Composition Phase
identification Sn Sb Cu Zn O2
Wt At Wt At Wt At Wt At At Wt
+ (See fig 6a)
+ (See fig 6b)
+ (See fig 6c)
6543
7276
8359
6601
6161
4053
3457
368
875
3399
701
661
-------
2356
206
-------
2737
298
------
-------
351
-------
-------
494
-------
-------
360
-------
-------
1308
SnSb
Cu6Sn5
Eutectic
Table 4 Results of density and porosity
Material Density (gcm3)a Porosity (gcm
3) Reference
Sn-5wt Sb
SSC505
SSC-ZnO
7526plusmn0005
7553plusmn0006
7533plusmn0006
050
075plusmn017
087plusmn020
M El-Bahay [23]
This study
This study
Table 5 Tensile Results at room temperature and strain rate of 47 x 10-3
s-1
Material E (GPa) UTS (MPa) YS (MPa) f (MPa) f Reference
Sn-5wt Sb
SSC505
SSC-ZnO
445
434
603
3550
7748
8635
2570
6468
7310
---
4259
7280
22
170
97
El-daly [9]
This study
This study
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
1
0 100 200 300 400 500
23738 0C
23827 oC
TEMPERATURE (C)
SSC505
SSC-ZnOH
EA
T F
LO
W (
mW
)
Fig1 Eid etal
Figure
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
2
30 40 50 60 70 80
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Cu
6S
n5
Zn
O(0
02
)Z
nO
(10
1)
Sn
(31
2)
Sn
Sb
(10
4)
Sn
(41
1)
Sn
(42
0)
Sb
Sn
(11
3)
Sn
(32
1)
Sn
(40
0)
Sn
(11
2)
Sb
Sn
(20
2)
Sn
(30
1)
Sb
Sn
(00
3)
Cu
6S
n5
Sn
(21
1)
Sb
Sn
(11
0)
Sn
(10
1) a)SSC505
INT
EN
SIT
Y (
arb
un
its
)
2 (degree)
Sn
(20
0)
Sn
(22
0)
Sb
Sn
(01
0)
IN
TE
NS
ITY
(a
rbu
nit
s)
b) SSC-ZnO
Fig2 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
3
302 304 306 308 31 312 314 316 318 32 322 324 326
2 (degree)
Inte
ns
ity
(a
rbu
nt)
SSC505 SSC-ZnO
Fig3 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
4
Fig4 Eid et al
-Sn
-Sn
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
5
Fig5 Eid et al
Cu6Sn5
SbSn
Cu6Sn5
SbSn
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
6
0 1 2 3 4 5 6 7 8 9 10
Energy (keV)
Sn
Sn
SnSn
Sn
Sb
Sb
Sb
SbSn
+
+
(a)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
SnCuCu
Cu
Cu6Sn5
BA
+
Sn
(b)
0 1 2 3 4 5 6 7 8 9 10Energy (keV)
Sn
Sb
Sn
Sn
CuZn
Sn
(C)
CuO2
+
Fig6a-c Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al
7
000 005 010 015 0200
20
40
60
80
100
SSC505
ST
RE
SS
(M
Pa
)
STRAIN
SSC-ZnO
Room temperature
=4710
-4 s
-1
Fig7 Eid et al