Structures and Mechanical Properties of Multilayer ... · Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys －5－ be predicted from the facts

Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys

－1－

* 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

－2－

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 %)


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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


－4－

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


－5－

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.


－6－

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.


－7－

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.


－8－

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.


－9－

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.


－10－

(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.


－11－

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－12－

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。


－13－

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.

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Structures and Mechanical Properties of Multilayer ... · Structures and Mechanical Properties of Multilayer Friction Surfaced Aluminum Alloys －5－ be predicted from the facts