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8/10/2019 Lecture 11 Surface Characterization
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Lecture 11
Surface Characterization of Biomaterials in Vacuum
The structure and chemistry of a biomaterial surface greatly dictates thedegree of biocompatibility of an implant. Surface characterization isthus a central aspect of biomaterials research.
Surface chemistrycan be investigated directly using high vacuummethods:
Electron spectroscopy for Chemical Analysis (ESCA)/X-ray
Photoelectron Spectroscopy (XPS)
Auger Electron Spectroscopy (AES)
Secondary Ion Mass Spectroscopy (SIMS)
1. XPS/ESCA
Theoretical Basis:
Secondary electrons ejectedby x-ray bombardment from thesample near surface (0.5-10 nm)with characteristic energies
Analysisof the photoelectron energiesyields a quantitativemeasure of the surface composition
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23.051J/20.340JElectron energy analyzer
( = h)
(variable retardation voltage)
Lens
e
e
e
P 10-10Torr
X-ray source Detector
E
K
EF
LILII
LIII
Evac
EBenergy is characteristic
elementand
kin
Photoelectron binding
of thebonding environment
Chemical analysis!
Binding energy = incident x-ray energy photoelectron kinetic energy
EB= h- Ekin
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Quantitative Elemental Analysis
C1s
N1s
O1sIntensity
Low-resolution spectrum
500 300
Bindingenergy (eV)
Area under peakIi number of electrons ejected (& atoms present)Only electrons in the near surface region escape without losing
energy by inelastic collision
Sensitivity: depends on element. Elements present in concentrations>0.1 atom% are generally detectable (H & He undetected)
Quantification of atomic fraction Ci (of elements detected)
Ci =Ii / Si Siis the sensitivity factor:
Ij / Sjj -f(instrument & atomic parameters)
- can be calculated
sum over detectedelements
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High-resolution spectrumC1s
Intensity
PMMA
290 285
Bindingenergy (eV)
Ratio of peak areas gives a ratio of photoelectrons ejected from atomsin a particular bonding configuration (Si = constant)
Ex. PMMA5carbons in total H CH3
H CH3C C
3 C C (a) Lowest EBC1s
H C=O
H CEB 285.0 eV O
CH3
1 OCH3
(b) Intermediate EBC1sEB 286.8 eV
Why does core electron EBvary with valence shell
1C=O
O
(c) Highest EBC1sEB 289.0 eV
configuration?
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from carbon
Slight shift to 1s
Electronegative oxygen robs valence electrons(electron density higher toward O atoms)
Carbon core electrons held tighterto the + nucleus(less screening of + charge)
higher C binding energy
Similarly, different oxidation states of metals can be distinguished.
Ex. Fe FeO Fe3O4 Fe2O3
Fe2pbinding energy
XPS signal comes from first ~10 nm of sample surface.
What if the sample has a concentration gradient within this depth?
Surface-segregating species Adsorbed species
10nm
Multivalent oxide layer
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Depth-Resolved ESCA/XPS
The probability of a photoelectron escaping the sample without
undergoing inelastic collision is inversely related to its depth t withinthe sample:
t( ) ~ expP t
e
where e(typically ~ 5-30 ) is the electron inelastic mean-free path,which depends on the electron kinetic energy and the material.
(Physically, e= avg. distance traveled between inelastic collisions.)
For t= 3e P(t) = 0.05e
=90
95% of signalfrom t 3e
By varying the take-off angle (), the sampling depth can bedecreased, increasing surface sensitivity
e e
t =3 sine
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Ci
5 90
(degrees)
Variation of composition with angle may indicate:
- Preferential orientation at surface- Surface segregation- Adsorbed species (e.g., hydrocarbons)- etc.
Quantifying composition as a function of depth
The area under thejth peak of element i is the integral of attenuatedcontributions from all sample depthsz:
z (Iij =CinstT Ekin )Lijij n (z) exp dzi
sine
L
Cinst= instrument constantT(Ekin) = analyzer transmission function
ij= angular asymmetry factor for orbitaljof element i
ijis the photoionization cross-sectionni(z) is the atomic concen. of iat a depthz(atoms/vol)
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where:
MW 1/ 3
a= monolayer thickness (nm) a =107
NAv
MW = molar mass (g/mol)= density (g/cm3)
Ekin= electron kinetic energy (eV)
Ex: efor C1susing a Mg Kx-ray source:
EB= h- Ekin
For Mg Kx-rays: h= 1254 eVEkin= 970 eVFor C1s: EB= 284 eV
1 2 0.5 (nm) = (
49E +0.11Ekin ) Assume = 1.1 g/cm3e kin
e= 3.1 nm
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For non-uniform samples, signal intensity must be deconvolutedtoobtain a quantitative analysis of concentration vs. depth.
Case Example: a sample comprising two layers (layer 2 semi-infinite):
1 d
2
z (Iij = Cins T kin )Lijij ni (z)exp sin
dze
ij ij o i,1 e,1
ij ,o i,2 e,2 e,1 sin,
e,1 sin
(1)
d (2) d or Iij =Iij ,
1 exp
e,1 sin
+Iij ,exp
e,1 sin
(1)
z Iij = Iij,oni,1 sin exp
sin
ee
I =I (1) n sin1 exp
d
d
(2)
z I ij oni,2 sin exp
sin
, ee0 d
+I (2)n sinexp
d
Why e,1? Electrons originating insemi-infinite layer 2 are attenuatedby overlayer 1
( )where Iij
i
, = measured peak area from a uniform, semi-infinite sample
of material i.
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Methods to solve ford
Scenario 1: ni,2=0(ex., C1speak of a polymer adsorbed on an oxide):
d d 1(1)
Iij =Iij ,
1 exp
sin
e,1 2
(1)measure a bulk sample of the upper layer material Iij ,
Iij
dln 1 (1)I ij,
=
e,1 sin
obtain slope of ln 1
I (1
ij
) vs. csc d/e,1 Iij ,
for a fixed :
d = e,1 sinln 1I
(1
ij
)
Iij ,
substitute a calculated or measured e,1to obtain d
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Scenario 2: ni,1=0(ex., M2ppeak from underlying metal oxide (MOx):
d(2)
d 1Iij =Iij ,exp
e,1 sin
2
measure Iijfor same peak at different take-off angles (1, 2)
(2) d
I ni,2e,2 sin exp Iij ,ij o 1,
e,1 sin11 = d
2 (2)Iij , I ni,2e,2 sin exp ij o 2,e,1 sin2
d 1
Iij , =sin1 exp (csc csc2 )Iij ,
sin2 e,11
2
1 Iij ,
sin21d = (csc csc )
ln Iij , sin
e,1 2 12 1
substitute a calculated or measured e,1to obtain d
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Scenario 3: element present in distinguishable bonding configurations inlayers 1 & 2 (ex., O1speak from -C-O-C- and MOx):
(1)
d (2) d
Iij =Iij ,1 exp
e,1 sin
+Iij,
exp e,1 sin
(2 ) d
I ni,2e,2 sinexp 1 dIij(2) ij o,
e,1 sin=(1) d Iij (1)
2I ni,1e,1 sin
1exp
e,1 sin
,ij o
(1) (2)measure element peak areasIij and Iij
(1)
(2), ,for same element and orbital: Iij o =Iij o
ni,2 Ci,2=for same element and orbital: ni,1 Ci,1
I
d
ij
(2)C
i,2e,2 exp e,1 sin
I =
ij
d
(1)
Ci,1e,1 1 exp
e,1 sin
solve numerically for d, substituting calculated values of e,2& e,1
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if d
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Ion Etching
Depth profiling for depths > 10 nm (100 nm 1 m)
Ar+, Xe+or He+ions etch surface layer
Signal
Intensity
6(OH)2) coatingHydroxyapatite (Ca10(PO4)
P2pTi2p
XPS spectra re-recorded
on Ti implant
sputter time
Calibration of sputter rates: time depth
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2. Auger Electron Spectroscopy
Theoretical Basis:
Auger electrons createdby electron bombardment of sample areejected from near surface (1-3 nm)with characteristic energies
Analysisof the Auger electron energiesyields a quantitativemeasure of the surface composition
ejected core electron
EK EM= EN+ Ekin EvacAuger electronNEkin = EK EM ENM
ELIII
xyz (ECVVor ECCV)
LLII
I
ejection from x shell
electronic transition yx K
release of z-level Auger with Ekin
INFORMATION: Exyzis characteristic to element & bonding
AES vs. XPS
Advantages Disadvantages
- focused e-beam gives highx,y spatial resolution(5 nm vs. ~1 m)
- charging effects onnonconductive samples(unsuitable)
- larger bonding effects - degradation of organics
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3. Secondary Ion Mass Spectroscopy (SIMS)
Experimental Approach:
Energetic ions (1-15 keV)bombard sample surface
Secondary ions/charged fragmentsare ejected from surface anddetected
ion gun
filter mass filter
ionenergy
detector
sample
Ion Guns
Nobel gas: Ar+, Xe+
liquid metal ion: Ga+, Cs+(~1nm beam size x,y mapping)types
pulsed LMI (time-of-flight source)
low currents used: 10-8-10-11A/cm2
Ion beam current(A/cm2)
surface monolayerlifetime (s)
10-5 16
10-7 160010-9 1.6105
10-11 1.6107
1 Amp = 6.21018 ions/sec
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Detectors
sensitive to the ratio of mass/charge (m/z)
resolution defined as m/m (larger = better!)
Quadrupole (RF-DC): resol. m/m~ 2000; detects m< 103amu
Oscillating RF fielddestabilizes ions: only ionswith specified m/zcan pass
Magnetic sector: m> 104amu; m/m~ 10,000
R
Applied B-field results incircular trajectory (radius=R)of charged particles
1 2mV1/ 2
R =
B
z
acceleratingvoltage
Time-of-flight (TOF): m~ 103-104amu; m/m~ 10,000
Pulsed primary beamgenerates secondary ion
m 1/ 2
pulses detected at distance Ltime =
2zV
L
flight tubelength
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Modes of Operation
Static SIMS
low energy ions: 1-2 keV; penetration ~5-10
low ion doses: < 1013ions/cm2sec 1 cm2 1015 atoms
195% of signal from
statomic layer!
Information:
surface composition
surface bonding chemistry (sputtered fragments)
Example: SIMS of silica powderNegative spectrum
Intensity(arb. units)
O
OH
SiO2
SiO2H
SiO3 SiO3H
(SiO2)2OH
16 17 60 61 76 77 137
m/z
OH HO OHWhich structure is
suggested from SIMS? SiSiOO O O
O
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Positive spectrum
Intensity(arb. units) O+
CH3+
H2O+
OH
+
15 16 17 18
SIMS suggests presence m/zof adsorbed methanol
SIMS vs. XPS/AES
Advantages Disadvantages
- high sensitivity (ppm ppb) - not quantitative
- more sensitive to top surface
- applicable to any solid
Dynamic SIMS
1-20 keV primary beam
rastered beam sputters a crater in sample
secondary ions gives depth profiling
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beam pathprimary
10-100 m
10-100 m
N
Signal
Intensity
N ion-implanted Ti (for wear resistance)
sputter time
References
J.C. Vickerman, Ed., Surface AnalysisThe Principle Techniques,J. Wiley & Sons: New York,NY, 1997, Chapters 3, 4 & 5.
D. Briggs, Surface Analysis of Polymers by XPS and Static SIMS, Cambridge University Press:United Kingdom, 1998.
C.-M. Chan, Polymer Surface Modification and Characterization,Hanson: Cincinnati, OH:1994, Chapters 3 & 4.
P.J. Cumpson, Angle-resolved XPS and AES: depth-resolution limits and a general comparisonof properties of depth-profile reconstruction methods,J. Electron Spectroscopy 73(1995) 25
52.
B. Elsener and A. Rossi, XPS investigation of passive films on amorphous Fe-Cr alloys,Electrochimica Acta 37(1992) 2269-2276.
A.M. Belu, D.J. Graham and D.G. Castner, Time-of-flight secondary ion mass spectroscopy:techniques and applications for the characterization of biomaterial surfaces, Biomaterials 24,(2003) 3635-3653.