JP2762127B2 - Method for producing structural member made of amorphous Al alloy and amorphous Al alloy powder - Google Patents
Method for producing structural member made of amorphous Al alloy and amorphous Al alloy powderInfo
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- JP2762127B2 JP2762127B2 JP1237867A JP23786789A JP2762127B2 JP 2762127 B2 JP2762127 B2 JP 2762127B2 JP 1237867 A JP1237867 A JP 1237867A JP 23786789 A JP23786789 A JP 23786789A JP 2762127 B2 JP2762127 B2 JP 2762127B2
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- atomic
- alloy powder
- alloy
- structural member
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- 239000000843 powder Substances 0.000 title claims description 52
- 229910000838 Al alloy Inorganic materials 0.000 title claims description 41
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- 238000010521 absorption reaction Methods 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 3
- 239000000956 alloy Substances 0.000 claims description 3
- 239000000126 substance Substances 0.000 claims description 3
- 239000000203 mixture Substances 0.000 claims description 2
- 238000000034 method Methods 0.000 description 9
- 238000010586 diagram Methods 0.000 description 6
- 238000002425 crystallisation Methods 0.000 description 5
- 230000008025 crystallization Effects 0.000 description 5
- 238000001816 cooling Methods 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000004455 differential thermal analysis Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 229910000808 amorphous metal alloy Inorganic materials 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000005280 amorphization Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 125000001475 halogen functional group Chemical group 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000002250 progressing effect Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Description
【発明の詳細な説明】 A.発明の目的 （１）産業上の利用分野 本発明は非晶質Al合金製構造部材の製造方法および非
晶質Al合金粉末に関する。DETAILED DESCRIPTION OF THE INVENTION A. Object of the Invention (1) Field of Industrial Application The present invention relates to a method for producing an amorphous Al alloy structural member and an amorphous Al alloy powder.
（２）従来の技術 従来、この種構造部材の製造方法として、例えばAl85
Ni5Y10（数値の単位は原子％、以下同じ）で表わされる
非晶質Al合金粉末を用い、この粉末より圧粉体を成形
し、次いでその圧粉体に熱間塑性加工を施す、といった
方法が知られている。(2) Conventional technology Conventionally, as a method of manufacturing such a structural member, for example, Al 85
Using an amorphous Al alloy powder represented by Ni 5 Y 10 (the unit of numerical value is atomic%, the same applies hereinafter), a green compact is formed from this powder, and then the green compact is subjected to hot plastic working. Such a method is known.
（３）発明が解決しようとする課題 しかしながら前記粉末よりなる圧粉体は可塑化範囲が
比較的狭いため、熱間塑性加工過程において結晶化が進
行し、その結果、加工性の悪化を招き、また構造部材に
おける非晶質成分の体積分率の低下に伴いその部材の強
度も比較的低い、といった問題がある。(3) Problems to be Solved by the Invention However, since the green compact made of the powder has a relatively narrow plasticizing range, crystallization proceeds in the hot plastic working process, and as a result, the workability is deteriorated, Further, there is a problem that the strength of the structural member is relatively low as the volume fraction of the amorphous component in the structural member decreases.
本発明は前記問題を解決し得る前記製造方法およびそ
の方法に用いられる非晶質Al合金粉末を提供することを
目的とする。An object of the present invention is to provide the manufacturing method capable of solving the above-mentioned problem and an amorphous Al alloy powder used in the manufacturing method.
B.発明の構成 （１）課題を解決するための手段 本発明に係る非晶質Al合金製構造部材の製造方法は、
化学式：AlaNibYcCodで表わされ、 81原子％≦ａ≦85原子％、 ２原子％≦ｂ≦７原子％、 ７原子％≦ｃ≦10原子％、 １原子％≦ｄ≦４原子％、 ５原子％≦ｂ＋ｄ≦９原子％、 の組成を有し、且つ非晶質成分の体積分率VfがVf≧50％
である非晶質Al合金粉末より圧粉体を成形し、次いでそ
の圧粉体に熱間塑性加工を施し、その熱間塑性加工にお
いて、加工温度を240℃以上、400℃以下に設定して前記
非晶質Al合金粉末に吸熱変化を生じさせることを特徴と
する。B. Configuration of the Invention (1) Means for Solving the Problems The method for producing a structural member made of an amorphous Al alloy according to the present invention comprises:
Formula: Al a Ni b is represented by Y c Co d, 81 atomic% ≦ a ≦ 85 atomic%, 2 atomic% ≦ b ≦ 7 at%, 7 at% ≦ c ≦ 10 atomic%, 1 atomic% ≦ d ≦ 4 atomic%, 5 atomic% ≦ b + d ≦ 9 atomic%, and the volume fraction Vf of the amorphous component is Vf ≧ 50%
A green compact is formed from the amorphous Al alloy powder that is, and then subjected to hot plastic working on the green compact, and in the hot plastic working, the working temperature is set to 240 ° C or higher and 400 ° C or lower. An endothermic change is caused in the amorphous Al alloy powder.
こゝで、加工温度とは、熱間塑性加工過程における圧
粉体（または構造部材）の温度を言う。したがって、圧
粉体を240℃以下の温度に加熱し、熱間塑性加工過程に
おいて圧粉体（または構造部材）の温度が上昇して前記
加工温度範囲に入る場合も本発明の概念に含まれる。Here, the working temperature refers to the temperature of the compact (or structural member) in the hot plastic working process. Therefore, the concept of the present invention includes a case where the green compact is heated to a temperature of 240 ° C. or less and the temperature of the green compact (or the structural member) increases in the hot plastic working process and falls within the working temperature range. .
本発明に係る非晶質Al合金粉末は、化学式：AlaNibYc
Codで表わされ、 81原子％≦ａ≦85原子％、 ２原子％≦ｂ≦７原子％、 ７原子％≦ｃ≦10原子％、 １原子％≦ｄ≦４原子％、 ５原子％≦ｂ＋ｄ≦９原子％、 の組成を有し、且つ非晶質成分の体積分率VfがVf≧50％
であり、可塑化温度Tgを超えた温度域において、組成が
Al85Ni5Y10（数値の単位は原子％）である基準非晶質Al
合金粉末の吸熱量ＱをＱ＝100としたとき、吸熱量Ｑが
Ｑ≧100であることを特徴とする。The amorphous Al alloy powder according to the present invention has a chemical formula: Al a Ni b Y c
Represented by Co d, 81 atomic% ≦ a ≦ 85 atomic%, 2 atomic% ≦ b ≦ 7 at%, 7 at% ≦ c ≦ 10 atomic%, 1 atomic% ≦ d ≦ 4 atomic%, 5 atomic% ≦ b + d ≦ 9 atomic%, and the volume fraction Vf of the amorphous component is Vf ≧ 50%
In the temperature range exceeding the plasticizing temperature Tg, the composition is
Reference amorphous Al which is Al 85 Ni 5 Y 10 (numerical unit is atomic%)
When the heat absorption Q of the alloy powder is Q = 100, the heat absorption Q is Q ≧ 100.
（２）作用 前記方法によれば、Coの添加により、前記加工温度範
囲において非晶質Al合金粉末に大きな吸熱変化を生じさ
せて圧粉体の可塑化範囲を広げることが可能であり、こ
れにより非晶質成分の体積分率が高く、高強度な構造部
材を得ることができる。(2) Operation According to the method, the addition of Co can cause a large endothermic change in the amorphous Al alloy powder in the processing temperature range, thereby expanding the plasticization range of the green compact. Accordingly, a structural member having a high volume fraction of the amorphous component and a high strength can be obtained.
たゞし、Al、Ni、ＹおよびCoの含有量が前記範囲より
外れると、非晶質Al合金粉末を得ることが困難になる。However, if the contents of Al, Ni, Y and Co are out of the above range, it becomes difficult to obtain an amorphous Al alloy powder.
熱間塑性加工において、その加工温度が240℃未満で
は、加工が困難となり、一方、400℃を上回ると、結晶
化が進行し、また析出物が粗大化する。In the hot plastic working, if the working temperature is lower than 240 ° C., the working becomes difficult. On the other hand, if the working temperature is higher than 400 ° C., crystallization proceeds and precipitates become coarse.
Coは前記作用に加えて、急冷速度が低くても非晶質化
を促進する、といった作用を有する。In addition to the above-mentioned effects, Co has the effect of promoting the amorphization even at a low quenching rate.
前記非晶質Al合金粉末は前記温度域において大きな吸
熱量を有し、したがって前記粉末を用いて前記方法を実
施することにより、前記のような特性を備えた構造部材
を得ることができる。The amorphous Al alloy powder has a large amount of heat absorption in the temperature range. Therefore, by performing the method using the powder, a structural member having the above-described characteristics can be obtained.
（３）実施例 表Ｉは、本発明に用いられる各種非晶質Al合金粉末A1
〜A7、比較例非晶質Al合金粉末B1〜B8および従来例非晶
質合金粉末Ｃの物性を示す。なお、比較例非晶質Al合金
粉末B2、B4、B5、B7の可塑化温度Tgは測定不能であっ
た。(3) Examples Table I shows various amorphous Al alloy powders A 1 used in the present invention.
7 shows the physical properties of Comparative Example amorphous Al alloy powders B 1 to B 8 and Comparative Example amorphous alloy powder C. The plasticization temperature Tg of the comparative amorphous aluminum alloy powders B 2 , B 4 , B 5 , and B 7 could not be measured.
各非晶質合金粉末A1〜A7、B1〜B8、Ｃは、4000rpmの
回転速度で回転する直径250mmの銅製冷却ロール上に、
アルゴンガス圧で溶融合金を噴出させる、単ロール式急
冷凝固法を適用して製造されたものである。Each of the amorphous alloy powders A 1 to A 7 , B 1 to B 8 , and C were placed on a copper cooling roll having a diameter of 250 mm rotating at a rotation speed of 4000 rpm.
It is manufactured by applying a single-roll rapid solidification method in which a molten alloy is jetted at an argon gas pressure.
第１〜第５図は非晶質Al合金粉末の示差熱量分析図で
あり、第１図は粉末A1に、第２図は粉末A2に、第３図は
粉末B1に、第４図は粉末B2に、第５図は粉末Ｃにそれぞ
れ対応する。 First to FIG. 5 is a differential thermal analysis diagram of amorphous Al alloy powder, Figure 1 is a powder A 1, FIG. 2 to the powder A 2, FIG. 3 is the powder B 1, the fourth figure powder B 2, Fig. 5 correspond to the powder C.
非晶質Al合金粉末A1，A2の場合は、第1,第２図に示す
ように可塑化温度Tgを超えた温度域で大きな吸熱変化が
生じ、これは圧粉体の可塑化範囲が広いことを意味する
ので、これら粉末A1，A2よりなる圧粉体の熱間塑性加工
性が良好になる。In the case of the amorphous Al alloy powders A 1 and A 2 , as shown in FIGS. 1 and 2, a large endothermic change occurs in a temperature range exceeding the plasticization temperature Tg, which is due to the plasticization range of the green compact. This means that the green compact of these powders A 1 and A 2 has good hot plastic workability.
非晶質Al合金粉末B1,Cの場合は、第3,第５図から明ら
かなように可塑化温度Tgを超えた温度域における吸熱変
化が小さい。In the case of the amorphous Al alloy powders B 1 and C, the endothermic change in the temperature range exceeding the plasticizing temperature Tg is small, as is clear from FIGS.
非晶質Al合金粉末B2の場合は、第４図から明らかなよ
うに可塑化温度Tgが現われない。Amorphous case of Al alloy powder B 2, as is apparent plasticizing temperature Tg from Figure 4 it does not appear.
表Ｉにおける吸熱量Ｑは、次のような方法で求められ
たものである。即ち、各非晶質Al合金粉末について、第
２図に明示するように可塑化温度Tgを通る温度軸に平行
な直線l1と曲線部l2とで囲まれる斜線領域Ｒの面積を求
め、次いで従来例非晶質Al合金粉末Ｃを基準非晶質Al合
金粉末と定め、その面積を吸熱量Ｑ＝100として、それ
に対する比を求める。The amount of heat absorption Q in Table I was determined by the following method. That is, for each amorphous Al alloy powder, and measuring the area of the hatched region R surrounded by the straight line parallel to l 1 and a curved portion l 2 to the temperature axis through the plasticizing temperature Tg as clearly shown in Figure 2, Next, the conventional amorphous Al alloy powder C is determined as the reference amorphous Al alloy powder, and the area thereof is set as the heat absorption Q = 100, and the ratio thereof is determined.
表Ｉの吸熱量Ｑからも、本発明において用いられる非
晶質Al合金粉末A1〜A7、したがって圧粉体は広い可塑化
範囲を持つことが明らかである。From Table I endotherm Q of amorphous Al alloy powder A 1 to A 7 for use in the present invention, therefore green compact is clear that a wide plasticizing range.
非晶質Al合金粉末A1〜A6、B1〜B5、B8、Ｃを用いて密
度98％以上の構造部材を製造したところ、表IIの結果が
得られた。When structural members having a density of 98% or more were produced using the amorphous Al alloy powders A 1 to A 6 , B 1 to B 5 , B 8 , and C, the results shown in Table II were obtained.
製造に当っては、非晶質Al合金粉末より直径60mm、長
さ50mmで、圧粉密度90％以上の圧粉体を得、次いでこの
圧粉体を内径60mm、肉厚10mmのアルミニウム罐に挿入
し、その後加工温度240〜400℃（粉末の結晶化温度Txに
より異なる）、押出し比13にて熱間押出し加工を行っ
た。In the production, a green compact having a diameter of 60 mm, a length of 50 mm and a green density of 90% or more was obtained from the amorphous Al alloy powder, and then this green compact was transferred to an aluminum can with an inner diameter of 60 mm and a thickness of 10 mm. Then, hot extrusion was performed at a processing temperature of 240 to 400 ° C. (depending on the crystallization temperature Tx of the powder) and an extrusion ratio of 13.
表IIから明らかなように、本発明によれば、非晶質成
分の体積分率（Vf）が高く、高強度な構造部材が得られ
る。 As is clear from Table II, according to the present invention, a structural member having a high volume fraction (Vf) of an amorphous component and a high strength can be obtained.
これは、Coの添加により圧粉体の可塑化範囲を広げ、
熱間押出し加工過程における結晶化を抑制し、また加工
性を良好にしたことに起因する。This increases the plasticization range of the green compact by adding Co,
This is because crystallization in the hot extrusion process is suppressed and processability is improved.
第6,第７図は、前記冷却ロールの回転速度を1000rpm
に設定して得られた非晶質Al合金粉末に関する示差熱量
分析図であり、第６図が非晶質Al合金粉末A2に、また第
７図が非晶質Al合金粉末Ｃにそれぞれ対応する。FIGS. 6 and 7 show that the rotation speed of the cooling roll is 1000 rpm.
A differential thermal analysis diagram relating to amorphous Al alloy powder obtained by setting the, in FIG. 6 is an amorphous Al alloy powder A 2, also respectively Figure 7 is an amorphous Al alloy powder C I do.
第6,第７図を比較すると明らかなように、第６図では
比較的大きな吸熱変化が生じ、これはCoを添加すると、
急冷速度が低くても非晶質形成能が高いことを示してい
る。As is apparent from a comparison of FIGS. 6 and 7, a relatively large endothermic change occurs in FIG. 6, which is caused by adding Co.
This shows that the amorphous forming ability is high even when the quenching rate is low.
第8,第９図は、前記冷却ロールの回転速度を500rpmに
設定して得られた非晶質Al合金粉末に関する示差熱量分
析図であり、第８図が非晶質Al合金粉末A2に、また第９
図が非晶質Al合金粉末Ｃにそれぞれ対応する。8, FIG. 9 is a differential thermal analysis diagram relating to amorphous Al alloy powder obtained by setting the 500rpm rotational speed of the cooling roll, FIG. 8 is an amorphous Al alloy powder A 2 And ninth
The figure corresponds to the amorphous Al alloy powder C, respectively.
第8,9図を比較すると、明らかなように、第８図で
は、前記同様にCoの添加により比較的大きな吸熱変化が
生じており、非晶質形成能の高いことが判る。Comparing FIGS. 8 and 9, it is apparent that in FIG. 8, a relatively large endothermic change is caused by the addition of Co as described above, indicating that the amorphous forming ability is high.
これは、第８図に示された非晶質Al合金粉末A2のＸ線
回折図である第10図において、急峻なピークの無い非晶
質特有のハローパターンが見られることからも明らかで
ある。This is because, in FIG. 10 is an X-ray diffraction pattern of amorphous Al alloy powder A 2 shown in FIG. 8, also evident from the fact that sharp peaks without amorphous peculiar halo pattern is observed is there.
第11図は第９図に示された非晶質合Al金粉末ＣのＸ線
回折図であって、各急峻なピークは結晶面を示し、第11
図より冷却速度の低下に伴い結晶化が進行していること
が判る。FIG. 11 is an X-ray diffraction diagram of the amorphous alloyed Al gold powder C shown in FIG. 9, in which each steep peak indicates a crystal plane.
From the figure, it can be seen that crystallization is progressing as the cooling rate decreases.
なお、本発明の熱間塑性加工には熱間鍛造加工も含ま
れる。The hot plastic working of the present invention includes hot forging.
C.発明の効果 本発明によれば、特定の非晶質Al合金粉末を用い、ま
た熱間塑性加工における加工温度を特定することによっ
て、非晶質成分の体積分率が高く、高強度な構造部材を
得ることが可能な製造方法を提供することができる。C. Effect of the Invention According to the present invention, by using a specific amorphous Al alloy powder, and by specifying the processing temperature in hot plastic working, the volume fraction of the amorphous component is high, high strength A manufacturing method capable of obtaining a structural member can be provided.
また本発明によれば、前記構造部材の原料粉末として
最適な非晶質Al合金粉末を提供することができる。Further, according to the present invention, it is possible to provide an amorphous Al alloy powder optimal as a raw material powder for the structural member.
第１〜第９図は各種非晶質Al合金粉末に関する示差熱量
分析図、第10,第11図は二種の非晶質Al合金粉末のＸ線
回折図である。FIGS. 1 to 9 are differential calorimetric analysis diagrams of various amorphous Al alloy powders, and FIGS. 10 and 11 are X-ray diffraction diagrams of two types of amorphous Al alloy powders.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 堀村 弘幸 埼玉県和光市中央１丁目４番１号 株式 会社本田技術研究所内 (72)発明者 松本 規明 埼玉県和光市中央１丁目４番１号 株式 会社本田技術研究所内 (56)参考文献 特開 平３−94030（ＪＰ，Ａ) (58)調査した分野(Int.Cl.6，ＤＢ名) B22F 1/00 - 3/20 C22C 1/04,45/08──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Hiroyuki Horimura 1-4-1 Chuo, Wako-shi, Saitama Prefecture Inside Honda R & D Co., Ltd. (72) Inventor Noriaki Matsumoto 1-4-1 Chuo, Wako-shi, Saitama No. In Honda R & D Co., Ltd. (56) References JP-A-3-94030 (JP, A) (58) Field surveyed (Int. Cl. 6 , DB name) B22F 1/00-3/20 C22C 1 / 04,45 / 08
Claims (2)
である非晶質Al合金粉末より圧粉体を成形し、次いでそ
の圧粉体に熱間塑性加工を施し、その熱間塑性加工にお
いて、加工温度を240℃以上、400℃以下に設定して前記
非晶質Al合金粉末に吸熱変化を生じさせることを特徴と
する非晶質Al合金製構造部材の製造方法。1. A chemical formula represented by Al a Ni b Y c Co d , 81 atomic% ≦ a ≦ 85 atomic%, 2 atomic% ≦ b ≦ 7 at%, 7 at% ≦ c ≦ 10 atomic%, 1 atomic% ≦ d ≦ 4 atomic%, 5 atomic% ≦ b + d ≦ 9 atomic%, and the volume fraction Vf of the amorphous component is Vf ≧ 50%
A green compact is formed from the amorphous Al alloy powder that is, and then subjected to hot plastic working on the green compact, and in the hot plastic working, the working temperature is set to 240 ° C or higher and 400 ° C or lower. A method for producing a structural member made of an amorphous Al alloy, wherein an endothermic change is caused in the amorphous Al alloy powder.
であり、可塑化温度Tgを超えた温度域において、組成が
Al85Ni5Y10（数値の単位は原子％）である基準非晶質Al
合金粉末の吸熱量ＱをＱ＝100としたとき、吸熱量Ｑが
Ｑ≧100であることを特徴とする非晶質Al合金粉末。2. A chemical formula represented by Al a Ni b Y c Co d , 81 atomic% ≦ a ≦ 85 atomic%, 2 atomic% ≦ b ≦ 7 at%, 7 at% ≦ c ≦ 10 atomic%, 1 atomic% ≦ d ≦ 4 atomic%, 5 atomic% ≦ b + d ≦ 9 atomic%, and the volume fraction Vf of the amorphous component is Vf ≧ 50%
In the temperature range exceeding the plasticizing temperature Tg, the composition is
Reference amorphous Al which is Al 85 Ni 5 Y 10 (numerical unit is atomic%)
An amorphous Al alloy powder characterized in that the heat absorption Q is Q ≧ 100 when the heat absorption Q of the alloy powder is Q = 100.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1237867A JP2762127B2 (en) | 1989-09-13 | 1989-09-13 | Method for producing structural member made of amorphous Al alloy and amorphous Al alloy powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1237867A JP2762127B2 (en) | 1989-09-13 | 1989-09-13 | Method for producing structural member made of amorphous Al alloy and amorphous Al alloy powder |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03100130A JPH03100130A (en) | 1991-04-25 |
| JP2762127B2 true JP2762127B2 (en) | 1998-06-04 |
Family
ID=17021595
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1237867A Expired - Fee Related JP2762127B2 (en) | 1989-09-13 | 1989-09-13 | Method for producing structural member made of amorphous Al alloy and amorphous Al alloy powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2762127B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2639455B2 (en) * | 1990-03-09 | 1997-08-13 | 健 増本 | High strength amorphous alloy |
| JP2799642B2 (en) * | 1992-02-07 | 1998-09-21 | トヨタ自動車株式会社 | High strength aluminum alloy |
-
1989
- 1989-09-13 JP JP1237867A patent/JP2762127B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH03100130A (en) | 1991-04-25 |
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