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Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys
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* Professor, Department of Mechanical Engineering, College of Industrial Technology, Nihon University
** Master’s Course, Mechanical Engineering, Graduate School of Industrial Technology, Nihon University
Structures and Mechanical Properties of Multilayer Friction
Surfaced Aluminum Alloys
Hiroshi TOKISUE*, Kazuyoshi KATOH*, Toshikatsu ASAHINA* and Toshio USHIYAMA**
( Received January 20, 2005 )
Abstract
5052 aluminum alloy plate used for substrate and both 5052 and 2017 aluminum alloys bar for coating
material, multilayer friction surfacing were done. Effects of phase value and phase direction of coating con-
sumable rod (coating material) on the structures and mechanical properties of multilayer surfaced material
were investigated. The second layer deposit of the surfaced material tended to incline toward the first layer
deposit side regardless of the direction of phase. And, the incomplete welded part of the edge in the first layer
deposit was disappeared by the second layer surfacing. Microstructure of deposit became finer than those of
the coating material and substrat regardless of the coating material. The surfacing efficiency of the second
layer deposit of the 5052 alloy surfaced material showed almost equal to that of the first layer deposit. In case
of using the 2017 alloy as a coating material, the surfacing efficiency of the second layer deposit showed
higher value than that of the first layer deposit. When the phase is given to the advancing side 15 mm showed
the highest surfacing efficiency of about 53%, and it’s showed remarkably higher than that of the 5052 alloy
surfaced material. Hardness of deposit of the 5052 alloy surfaced material was same value of substrate. But
the hardness of deposit of the 2017 alloy surfaced material showed a higher value than that of the substrate.
The width of the softening zone of all the surfaced materials was proportional to the total width of coating
consumable rod. Both tensile strength and elongation of the 5052 alloy surfaced material showed same value
to those of the substrate. Tensile strength of 2017 alloy surfaced material showed higher than that of the
substrate, but the elongation was inferior to the substrate. The elongation remarkably recognized the effect
of phase further than the tensile strength.
ISSN 0386-1678
Report of the Research Institute of Industrial Technology, Nihon UniversityNumber 78, 2005
1. Introduction
One type of the surface modification method that
allows highly functional materials to be adhered onto
the surface of the plate for enhanced functionality is
friction surfacing1), which is yet to be commercialized
but achieves hard deposits with relatively simple equip-
ment. The authors examined friction surfacing of both
5052 and 2017 aluminum alloys onto the surface of the
5052 aluminum alloy plate which observed the shape
and structure of the deposit and the mechanical proper-
ties 2), 3). As the results, the friction surfaced material
Hiroshi TOKISUE, Kazuyoshi KATOH, Toshikatsu ASAHINA and Toshio USHIYAMA
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using 5052 aluminum alloy bar was capable of form-
ing a deposit with the fine structure. The elongation of
surfaced material was obtained higher than that of the
substrate, but since the softening zone was found on
the substrate near the deposit, the tensile strength of
the surfaced material was reduced to about 90% of
the substrate. This means friction surfacing using this
material has no effectiveness in terms of strength.
Therefore, considering the known advantages of fric-
tion surfacing and the industrial significance of surface
modification, it is apparent that a type of material which
can produce added value, such as high hardness of the
surface of the substrate or enhanced strength of the sur-
faced material, should be used as a coating material.
According to research on some aluminum alloys
used for friction welding, a similar technique to fric-
tion surfacing, based on the effective use of frictional
heat 4) -7), the maximum temperature of the friction
welding process is slightly higher than that of the fric-
tion surfacing, although its heat cycle is similar to that
of the friction surfacing. For a friction welded 2017
aluminum alloy joint 4), when left at room temperature
after welding, the hardness of the softening zone is gen-
erally improved by natural aging to a level of the base
metal. This suggests that use of 2017 aluminum alloy
as a coating material may be able to ensure sufficient
strength in friction surfaced material even if no post
heat treatment is performed. It is concluded that the
2017 aluminum alloy is a raw material suited for coat-
ing material, also for save energy.
To realize improved functionality of the material
surface, which is one of the purposes of friction surfac-
ing, wider deposits are often necessary to achieve that
purpose from the surface efficiency. It would appear at
first glance that increasing the diameter of the coating
material would increase the surface area of the deposit;
however, it actually results in an increase in frictional
force during surfacing process, which is detrimental to
the equipment employed. Another method that has po-
tential is multilayer friction surfacing; a technique that
involves repeated friction surfacing. However, there
are currently almost no reports on this type of surfac-
ing technique.
In this study, the multilayer friction surfacing was
conducted with 5052 aluminum alloy plate as a sub-
strate and both 5052 and 2017 aluminum alloys bar
which has different compositions as a coating material,
and examined the surfacing conditions, particularly fo-
cusing on the effects of phase applied to the coating
material on the structures and mechanical properties of
the multilayer friction surfaced materials.
2. Materials and Experimental Procedure
5052P-H34 aluminum alloy plate of 5mm thick-
ness as a substrate was machined by cutting down to
50mm in width and 150mm in length. And, as coating
rod which is a coating material, both 5052 BDS-F and
2017BE-T4 aluminum alloys bar of 20mm in diameter
were used machining it down to 100mm in length. These
friction surfaced materials made from their coating rods
are hereinafter respectively referred to as 5052 alloy
surfaced material and 2017 alloy surfaced material. The
chemical compositions and mechanical properties of
these base metals are shown in Table 1 and Table 2,
respectively.
The friction surfacing was conducted by restrict-
ing the length of the coating rod (i.e., the surfacing
operation was terminated when 30 mm of the coating
rod had been consumed) 2),3). The friction surfacing was
performed under the surfacing conditions shown in Table
3, using a surfacing device equipped on the pressure
part of numerically controlled full automatic friction
welding machine. The schematic illustration of friction
Materials
A5052 plate
A5052 rod
A2017 rod
Si
0.09
0.13
0.44
Fe
0.26
0.15
0.25
Cu
0.04
0.03
3.80
Mn
0.04
0.04
0.68
Mg
2.55
2.24
0.56
Cr
0.20
0.15
0.02
Zn
0.01
0.02
0.02
Al
bal.
bal.
bal.
Table 1 Chemical compositions of base metals. (mass %)
Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys
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center of the coating rod for the second layer was phase
to the rotational center of the coating rod for the first
layer by the distance shown in Table 3, in the same
direction as the rotational direction of the coating rod
and the surfacing direction (advancing side; AS) and in
the direction opposite to them (retreating side; RS).
Hereinafter, the phase is shown as a combination of
direction and distance, as in AS10 or RS10. The fric-
tion surfacing was performed by maintaining contact
between substrate and coating rod for 1 second and then
moving substrate. For multilayer friction surfacing, after
surfacing the first layer, the surfaced material was cooled
down to room temperature, after which surfacing of the
second layer was conducted.
Observation of the outside appearance and struc-
tures, hardness measurement and tensile tests of the de-
posit and surfaced material were conducted at the room
temperature. For the 2017 alloy surfaced material, these
tests were applied to the monolayer friction surfaced
material3) on the 14th days after surfacing when no fur-
ther change in hardness was observed. The tensile test
specimen, which were taken from the gauge part at the
position of the surfaced material shown in Fig. 2 in the
same shape as that described in previous report2), 3.5mm
in thickness, 10mm in width and 40mm in length. The
Fig. 1 Schematic illustration of friction surfacing.
Table 2 Mechanical properties of base metals.
Materials
A5052 plate
A5052 rod
A2017 rod
Tensile strength(MPa)
256
245
414
Elongation(%)
28.0
16.2
26.3
Hardness(HV0.1)
79.7
81.0
134.7
Coating material
Friction pressure P(MPa)
Rotational speed N(s-1)
Traverse speed f(mm/s)
Phase of 2nd layer G(mm)
5052 rod
30
41.7
13
2017 rod
30
20
9
0, 5, 10, 15
Table 3 Friction surfacing conditions.
Fig. 2 Sampling position of tensile test specimen.
surfacing is shown in Fig. 1. The surfacing conditions
in multilayer surfacing may vary depending on the cor-
relation between the rotational direction of the coating
rod and the surfacing direction. Thus, the rotational
Hiroshi TOKISUE, Kazuyoshi KATOH, Toshikatsu ASAHINA and Toshio USHIYAMA
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surfaced material was machined such that the propor-
tion of the deposit to the thickness of the gauge part was
40% of the plate thickness.
3. Experiment Results and Discussion
3.1 Observation of the deposit
The appearances of the multilayer friction surfaced
material are shown in Fig. 3. For the 5052 alloy sur-
faced material, circularly patterns made by rotation of
the coating rod were clearly seen on the surface of the
second layer, regardless of both degree and direction
of the phase. These patterns are similar to those that
appeared on the surface of the monolayer friction sur-
faced material, combining 5052 alloy plate and bar2) or
friction surfaced mild steel8). Regardless of the direc-
tion of the phase applied to the coating rod, however,
some parts could be observed where the width of the
second layer changes irregularly. These width changes
were particularly noticeable in cases with AS phase.
This phenomenon, which was also observed for the
monolayer friction surfaced material2), it believe to be
caused by the deposit being more likely to be located
towards the AS and to be pushed toward the first layer
side due to the presence of the first layer.
Generally the second layer is prone to be moved
more to the first layer side, and this tendency is greater
Fig. 3 Appearances of multilayer deposit.: Center of 1st coating rod, : Center of 2nd coating rod
Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys
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be predicted from the facts that the high temperature
strength of the 2017 alloy is greater than that of the 5052
alloy, and that the deviation of deposit using the 2017
alloy3), is smaller than when 5052 alloy used as the coat-
ing material. For the 2017 alloy surfaced material, the
degree of phase had almost no influence on the devia-
tion of the deposit when the RS phase was applied.
For multilayer friction surfaced material, there was
no clear difference visible in the deposit length between
the first layer and second layer, regardless of the type
of coating material. Therefore, the shape of the de-
posit was evaluated according to the thickness and width
of the deposit. The measurement results are shown in
Fig. 4, in which the results are shown as the average of
entire deposits.
For the 5052 alloy surfaced material, when the AS
phase was applied, no difference either in thickness or
width of the deposit dependent on the degree of phase
was observed. For the RS phase, it was observed that
the thickness of deposit was affected by the phase and
that the AS part of the second layer tended to be the
thickest. The width of the deposit of second layer was
almost equal to that of the monolayer surfaced mate-
rial2). The width of the deposit is seen to increase with
increased phase, regardless of the phase direction.
when the phase is applied to the RS. It considered that
this phenomenon appears because the correlation be-
tween rotational direction of the coating rod and direc-
tion of surfacing caused the coating rod to be moved
more to the AS, and, in addition, because of the pres-
ence of the first layer at the AS.
On the deposit of the 2017 alloy surfaced material,
circular patterns similar to that on the 5052 alloy sur-
faced material were clearly seen, and the clear differ-
ence was not observed between the first and second layer.
From observation of the appearance of deposit, the ef-
fect of the second layer deposit on the first layer deposit
could not be recognized. Almost no irregular changes
in the deposit width of the second layer were observed
for the 2017 alloy surfaced material, whereas they had
been found for the 5052 alloy surfaced material.
Under conditions where phase was applied during
surfacing of the second layer, some deviation was ob-
served for the second layer, but the degree of deviation
was smaller than in case of the 5052 alloy surfaced
material. Regardless of the phase direction of the coat-
ing rod, the second layer is shown inclined to be formed
closer to the first layer side. Deviation increases in cases
where the AS phase was applied, while it becomes
smaller when a larger phase is applied. This result may
Fig. 4 Relation between phase of 2nd layer and thickness, width of multilayer deposit.
Hiroshi TOKISUE, Kazuyoshi KATOH, Toshikatsu ASAHINA and Toshio USHIYAMA
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The deposit of the 2017 alloy surfaced material
tends to be thicker for cases with 5mm and 10 mm phase
than without the phase, regardless of the measuring
positions, and to be slightly thinner than the 15mm
phase. The monolayered part of the second layer de-
posit become thicker and narrower than that of the
monolayer surfaced material3).
3.2 Surfacing efficiency
Regardless of the coating material, the consumed part
of the coating rod is not entirely accumulated on the
substrate used for friction surfacing: part of the surfac-
ing material is discharged outside in addition to the burrs
generated by friction welding5). Although not illus-
trated, the coating rod after multilayer friction surfac-
ing showed a similar to that of the monolayer friction
surfaced material 2).
The relationship between the phase as related to
the shape of the deposit and the surfacing efficiency of
the second layer (weight ratio of the coating rod before
and after surfacing) is shown in Fig. 5. The surfacing
efficiency of the second layer of the 5052 alloy surfaced
material showed almost equal to that of the monolayer
friction surfaced material 2). While the surfacing efficiency
was slightly smaller at the phase of 0 and 5 regardless
of either AS or RS, it slightly improves as the phase
grows.
Regardless of the AS or RS phase, the surfacing
efficiency of second layer of the 2017 alloy surfaced
material increases with increased phase as well as in
case of the 5052 alloy surfaced material. And, regard-
less of the degree of phase, the surfacing efficiency of
the 2017 alloy surfaced material is higher than that of
the 5052 alloy surfaced material. This is due to the
difference in high temperature strength of the coating ma-
terial used. To be specific, because the high temperature
strength of the 5052 alloy is lower than the 2017 alloy,
the amount of 5052 alloy discharged as burrs is greater
than for the 2017 alloy. The 2017 alloy surfaced mate-
rial showed the highest surfacing efficiency at the AS15
phase, the value of which is about 53%, and is remark-
ably high compared with that of the 5052 alloy sur-
faced material, which is about 33%. This value is higher
than the monolayer friction surfaced material under the
same conditions3).
3.3 Observation of Macro- and Microstructures
Figure 6 shows the macrostructures of the multi-
layer friction surfaced material. For the multilayer fric-
tion surfaced material, both inside of the deposit and
interface between deposit and substrate showed simi-
lar to that of the monolayer surfacing2), 3), regardless of
the coating materials.
Concerning the multilayer friction surfaced mate-
rial, at the part where the first layer and second layer
overlap, the incomplete welded part of the substrate and
coating rod at the edge of the deposit observed on the
first layer had been joined by heating and compression
by surfacing of the second layer. No voids due to in-
sufficient surfacing were found at the interface between
the first and second layer. However, some incomplete
welded parts were observed at both ends of the second
layer, although very small, as in the case of the single
layer alone. The thickness of the deposit of second layer
tends to be slightly greater than the first layer. In addi-
tion, regardless of the degree of phase, the thickness of
the deposit of second layer of the 5052 alloy surfaced
material is greater than that of the 2017 alloy surfaced
material in case of the AS phase, but thinner in case of
the RS phase.
Effects of the phase on the microstructures, near
the weld interface between the deposit and substrateFig. 5 Effect of friction surfacing conditions on surfacing
efficiency.
Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys
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are shown in Fig. 7. Regardless of the coating mate-
rial, the structure of deposit shows a finer lamellar struc-
ture than the coating rod or substrate. Even with the
largest phase, similar structural patterns resulted, and
no major differences were observed in the deposit with
different surfacing conditions and coating rod. Regard-
less of the direction and size of the phase, the thickness
of deposit using 5052 alloy coating rod became thicker
than that of the 2017 alloy coating rod.
In surfacing by fusion welding, it has been reported
Fig. 6 Macrostructures of multilayer deposit.
Fig. 7 Effect of phase value and direction of coating rod on the microstructures of multilayer deposit.
that the coating material penetrates to inside the sub-
strate 9). The friction surfacing is a novel solid phase
surface modification technology; no penetration of the
coating rod into the substrate was observed. On the other
hand, the mechanically mixed layer has been observed
on the weld interface of the dissimilar friction welded
2017/5052 alloys joint10). However, in this experiments,
the mechanically mixed layer was not observed at the
weld interface between the substrate and coating rod.
Hiroshi TOKISUE, Kazuyoshi KATOH, Toshikatsu ASAHINA and Toshio USHIYAMA
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3.4 Hardness Distribution
The hardness distribution of the multilayer friction
surfaced material is shown in Fig. 8. For the 5052
alloy surfaced material, a softening zone was found on
the substrate, as seen in case of the monolayer friction
surfaced material 2). The width of the softening zone
was proportional to the total width of the coating rod
that passes the substrate, since the width was influenced
by the deposit of first layer and that of second layer. In
case of the phase of 0, the hardness of the softening
zone was reduced as the coating rod of second layer
passed the same position as the first layer.
Whereas the hardness of substrate of the 2017 alloy
surfaced material showed a similar distribution to that
of the 5052 alloy surfaced material, but the hardness of
softening zone of the 2017 alloy surfaced material at
the phase 0 tends to be slightly higher than the 5052
alloy surfaced material.
Concerning hardness distribution in a transverse
section of the 5052 alloy surfaced material, the hard-
ness of deposit was slightly higher than that of the phase
of 0. When some phase was applied, however, no clear
difference was observed hardness between the deposit
and substrate. Hardness distribution in the transverse
section of the 2017 alloy surfaced material showed simi-
lar patterns to those of the monolayer friction surfaced
material3) regardless of whether phase is applied or not.
In case of the coating rod with the phase of 0, the hard-
ness of the first layer and second layer were both greater
than that of the substrate and equal to the base metal of
coating material. For the coating rod with some phase,
Fig. 8 Hardness distributions of multilayer deposit.
Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys
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Fig. 9 Results of tensile test of multilayer deposits.
the hardness of the deposit of first layer as it approaches
the second layer, and the hardness of almost the entire
surface of the second layer turned out to be equal to
that of the base metal of the coating material. This is
probably due to the thermal influence on the first layer
by surfacing of the second layer. For the hardness at
the center between the rotational centers of coating rod
of the first and second layer, the influence of heat during
surfacing became smaller as the decrease in phase be-
came greater, suggesting that a reflection of hardness
changes according to the degree of phase.
3.5 Tensile test
Results of the tensile tests are shown in Fig. 9. For
the 5052 alloy surfaced material, there was a small dif-
ference in tensile strength depending on the direction
and degree of phase, and the tensile strength was equal
to that of the substrate. Although the elongation for the
RS phase of 10 and 15 was equal to that of the sub-
strate, the other phase conditions was slightly lower than
the substrate.
Although the tensile strength of the 2017 alloy sur-
faced material showed higher than that of the substrate,
the tensile strength is affected very little by the degree
of phase. The elongation decreases in comparison with
the substrate regardless of the degree of phase, and it
was almost equal to that of the monolayer friction sur-
faced material3). Elongation of the 2017 alloy surfaced
material with the phase of 0 showed the smallest value,
while elongation with some phase decreased with an
increase in phase, regardless of the direction of phase.
The tensile strength of the 2017 alloy surfaced mate-
rial, calculated assuming that the strength of the coat-
ing material simply follows the rule of mixture, was
319 MPa, but the maximum value of the 2017 alloy
surfaced material showed in this experiment was 95.2%
of that value. Regardless of the coating material, the
peeling of at the interface of substrate and deposit was
not recognized at the rupture part of the tensile tested
specimen.
4. Conclusion
The 5052 aluminum alloy plate was used the sub-
strate, and multilayer friction surfacing was carried out
on the substrate with both 5052 and 2017 aluminum
alloys for the coating rod. The surfaced materials were
studied to investigate the influence on the structures and
mechanical properties of surfaced material of phase
applied to the coating rod, the following results were
obtained.
(1) The circular pattern due to the rotation of coat-
ing rod was clearly observed on the surface of
deposit. The second layer deviated toward the
first layer, regardless of phase direction.
(2) Regardless of the coating material, the incom-
plete welded parts of the edge in the first layer
deposit were disappeared by the deposition of
second layer surfacing. The deposit showed fine
lamellar structure, which is finer than that of the
coating rod and substrate.
Hiroshi TOKISUE, Kazuyoshi KATOH, Toshikatsu ASAHINA and Toshio USHIYAMA
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(3) The surfacing efficiency of the second layer of
the 5052 alloy surfaced material, calculated from
the weight ratio before and after surfacing of the
coating rod, was equal to that of the 5052 mono-
layer surfaced material. The surfacing efficiency
of second layer of the 2017 alloy surfaced mate-
rial was remarkably higher than that of the 5052
alloy surfaced material, and still higher than that
of the 2017 alloy monolayer surfaced material.
(4) The hardness of the deposit of both 5052 and
2017 alloy surfaced materials were revealed to be
equal to those of the base metals. Softening zones
were observed as wide as the coating rod that
passed the part of the substrate under deposit.
(5) The tensile strength and elongation of the 5052
alloy surfaced material were almost equal to those
of the substrate. But the tensile strength of the
2017 alloy surfaced material showed higher value
whereas its elongation was lower than that of the
substrate.
(6) Regardless of the coating material, the influence
of phase was observed more clearly on the elon-
gation than the tensile strength.
Acknowledgements
This research is supported by both the Grant-in-
Aid for Scientific Research (c) (grant no. 14550710)
and the Technology to Special Research Grants for the
Development of Characteristic Education from the
Ministry of education, Culture, Sport, Science. Authors
wish to express our sense of gratitude by making spe-
cial mention here.
Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys
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Hiroshi TOKISUE, Kazuyoshi KATOH, Toshikatsu ASAHINA and Toshio USHIYAMA
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多層肉盛したアルミニウム合金の組織と機械的性質
時末 光 , 加藤 数良 , 朝比奈 敏勝 , 牛山 俊男
概 要
5052アルミニウム合金板を基材に,5052および2017アルミニウム合金丸棒を肉盛金属に用いて多層摩擦肉盛を行い,得られた肉盛材の組織と機械的性質に及ぼす肉盛金属の位相の大きさ,およびその方向の影響を検討した。使用した肉盛金属に関係なく,肉盛層の第2層は位相の方向に関係なく第1層側に偏る傾向を示した。第1層の端部に観察される未接合部は第2層の肉盛によって消滅した。肉盛層の微視的組織は,肉盛金属の種類に関係なく肉盛金属および基材に比較して微細な組織を呈した。5052合金肉盛材の第2層の肉盛効率は,第1層のそれとほぼ同程度の値であった。2017合金肉盛材では,第2層の肉盛効率は第1層に比較して高い値を示した。また位相を15mmアドバンシングサイドに与えた場合に最大値53%を示し,この値は5052合金肉盛材に比較して著しく高い値であった。肉盛層の硬さは,5052合金肉盛材は基材と同程度の値であったが,2017合金肉盛材は基材に比較して高い値を示した。また,肉盛層近傍の基材部には,通過した全肉盛金属の幅に対応した軟化域が認められた。5052合金肉盛材の引張強さと伸びは基材と同程度の値であった。2017合金肉盛材の引張強さは基材より高い値を示したが,伸びは基材より低下した。肉盛金属の種類に関係なく,位相の影響は引張強さよりも伸びに顕著に認められた。
Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys
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Biographical Sketches of the Authors
Hiroshi Tokisue was born in Okayama, Japan on May 19, 1936. He received his B.
Eng. degree in Industrial Engineering and D. Eng. degree in Mechanical Engineering
from Nihon University, Japan in 1961 and 1982, respectively.
He has belonged to the Nihon University from 1961, in 1984 a Professor of the College
of Industrial Technology, Nihon University.
He is engaged in the study of the metal processing, namely machining, friction welding,
friction stir welding and friction surfacing.
Dr. Tokisue is a member of the Japan Institute of Light Metals, the Japan Society of
Mechanical Engineers, the Japan Welding Society, the Japan Institute of Metals, the
Japan Society for Composite Materials, the Japan Friction Welding Association and the
Japan Light Metal Welding & Construction.
Kazuyoshi Katoh was born in Nagoya, Japan on January 28, 1947. He received his
B. Eng. degree in Mechanical Engineering from Nihon University in 1969, M. Eng.
degree and D. Eng. degree in Mechanical Engineering from Nihon University in 1972
and 1990, respectively.
He has belonged to the Nihon University from 1972, in 1995 a Professor of College
of Industrial Technology, Nihon University. And he is engaged in the study of the metal
processing such as machining, friction welding, friction stir welding and friction spot
welding.
Dr. Katoh is a member of the Japan Institute of Light Metals, the Japan Welding Soci-
ety, the Japan Society of Mechanical Engineers, the Japan Society of Precision Engineer-
ing, the Japan Institute of Metals and the Japan Light Metal Welding & Construction.
Toshikatsu Asahina was born in Tokyo, Japan on March 8, 1943. He received his B.
Eng. degree and D. Eng. degree in Mechanical Engineering from Nihon University in
1965 and 1998, respectively.
He has belonged to the Nihon University from 1965, in 2002 a professor of the College
of Industrial Technology, Nihon University. And his present research is laser welding,
tungsten inert gas welding, plasma arc welding and resistance spot welding.
Dr. Asahina is a member of the Japan Society of Mechanical Engineers, the Japan
Institute of Light Metals, the Japan Welding Society, the Japan Light Metal Welding &
Construction and the American Welding Society.
Toshio Ushiyama was born in Nagano, Japan on August 11, 1979. He received his B.
Eng. degree in Mechanical Engineering from Nihon University in 2003.
He is a student of Master Course of Department of Mechanical Engineering, Graduate
School of Industrial Technology, Nihon University. And he is a member of the Japan
Institute of Light Metals, the Japan Society of Mechanical Engineers and the Japan Weld-
ing Society.