JPH01242749A - Heat-resistant aluminum alloy - Google Patents
Heat-resistant aluminum alloyInfo
- Publication number
- JPH01242749A JPH01242749A JP7095288A JP7095288A JPH01242749A JP H01242749 A JPH01242749 A JP H01242749A JP 7095288 A JP7095288 A JP 7095288A JP 7095288 A JP7095288 A JP 7095288A JP H01242749 A JPH01242749 A JP H01242749A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- heat
- strength
- weight
- powder
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000838 Al alloy Inorganic materials 0.000 title abstract description 3
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 23
- 239000000956 alloy Substances 0.000 claims abstract description 23
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 4
- 239000000843 powder Substances 0.000 abstract description 8
- 238000000034 method Methods 0.000 abstract description 6
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 229910052726 zirconium Inorganic materials 0.000 abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 abstract description 2
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 238000000465 moulding Methods 0.000 abstract description 2
- 229910000735 Pm alloy Inorganic materials 0.000 description 18
- 239000000654 additive Substances 0.000 description 5
- 230000000996 additive effect Effects 0.000 description 5
- 239000011159 matrix material Substances 0.000 description 5
- 239000002245 particle Substances 0.000 description 5
- 229910001020 Au alloy Inorganic materials 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000003353 gold alloy Substances 0.000 description 4
- 238000000889 atomisation Methods 0.000 description 3
- 238000005242 forging Methods 0.000 description 3
- 238000007712 rapid solidification Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910019752 Mg2Si Inorganic materials 0.000 description 1
- 238000013475 authorization Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000001427 coherent effect Effects 0.000 description 1
- 238000009694 cold isostatic pressing Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000009661 fatigue test Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000010299 mechanically pulverizing process Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000007873 sieving Methods 0.000 description 1
- 238000007783 splat quenching Methods 0.000 description 1
- 230000002269 spontaneous effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
産業上の利用分野
本発明は、粉末冶金用低密度アルミニウム合金に関し、
より詳しくは、常温から２００°Ｃに至る温度範囲にお
いて、（憂れた機械的特性（引張り強度、疲労強度、延
性、靭性など）を発揮する低密度耐熱性アルミニウム粉
末合金に関する。DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application The present invention relates to a low density aluminum alloy for powder metallurgy.
More specifically, it relates to a low-density heat-resistant aluminum powder alloy that exhibits poor mechanical properties (tensile strength, fatigue strength, ductility, toughness, etc.) in a temperature range from room temperature to 200°C.
従来技術とその問題点
近年、アトマイズ法、スプラット クエンチング法、リ
ボン キャスト法などの急冷凝固法の急速な発展により
、高強度耐熱性アルミニウム粉末（ＡΩ−ＰＭ）合金の
耐用温度は、３００〜３５０℃程度にまで改善されてい
る。この耐熱性改善のためには、ＡＲに対する溶解性お
よび分散性の低い合金元素が大量に使用されている。Ｆ
ｅ、Ｃｒ５Ｚｒ、Ｔｉ、ＶＳＭｏ、ｗ、Ｍｎ、Ｎｉなど
を代表例とするこれらの合金元素は、溶湯からの急速凝
固により、ＡΩマトリックス中に過飽和に溶解し、引続
く熱的および機械的処理によって、Ａ［マトリックス中
に所望の状態で析出する。かくして得られたＡｆｌ−Ｐ
Ｍ合金中では、微細な均一に分散した粒子（通常０．１
〜０．５μｍ程度）が形成されており、これが転位障害
となって、Ａｌ１−ＰＭ合金の微細構造を安定化させ、
Ａ！２＝ＰＭ合金の特性を改善する。Ａρ−８Ｆｅ−２
Ｍｏ、Ａｆｆ−８Ｆｅ−４Ｃｒなどの合金が、３５０℃
までの温度域で優れた熱安定性と強度を備えていること
は、よく知られている。しかしながら、高強度耐熱性へ
Ω−ＰＭ合金の多くは、硬く且つ脆い金属間化合物相を
大量に含むので、成形性および延性に劣っている。これ
らの欠点のために、公知の高強度耐熱性ＡＲ−ＰＭ合金
は、高度の成形性と延性とが最も必要とされる中間温度
域（１５０〜２５０°Ｃ）での使用が不可能であった。Prior art and its problems In recent years, with the rapid development of rapid solidification methods such as atomization, splat quenching, and ribbon casting, the service temperature of high-strength, heat-resistant aluminum powder (AΩ-PM) alloy has increased from 300 to 350. It has been improved to about ℃. In order to improve this heat resistance, alloying elements with low solubility and dispersibility in AR are used in large quantities. F
These alloying elements, of which typical examples include e, Cr5Zr, Ti, VSMo, w, Mn, and Ni, dissolve into the AΩ matrix in a supersaturated state by rapid solidification from the molten metal, and are dissolved in the AΩ matrix by subsequent thermal and mechanical treatments. , A [precipitates in the matrix in the desired state. The thus obtained Afl-P
In M alloys, fine, uniformly dispersed particles (usually 0.1
~0.5 μm) are formed, which act as dislocation obstacles and stabilize the microstructure of the Al1-PM alloy.
A! 2=Improve the properties of PM alloy. Aρ-8Fe-2
Alloys such as Mo, Aff-8Fe-4Cr, etc.
It is well known that it has excellent thermal stability and strength in the temperature range up to However, many of the high-strength, heat-resistant Ω-PM alloys contain a large amount of hard and brittle intermetallic compound phases, resulting in poor formability and ductility. These drawbacks make known high-strength, heat-resistant AR-PM alloys impossible to use in the intermediate temperature range (150-250°C), where high formability and ductility are most needed. Ta.
したがって、上記の如き高強度耐熱性Ａρ−Ｐ Ｍ合金
の使用分野は、未だ限られている。Therefore, the field of use of the above-mentioned high-strength, heat-resistant Aρ-PM alloy is still limited.
問題点を解決するための手段
本発明者は、上記の如き従来技術の問題点に鑑みて鋭意
研究を市ねた結果、Ｆｅ及び／又はＣｒとＺｒの含Ｇ量
を適度に抑え且つ特定量のＭｇを配合したＡ２合金が、
Ａ！Ｑ−ＰＭ合金として極めて優れた性能を発揮するこ
とを見出した。すなわち、本発明は、下記に示す組成を
有するＡＱ金合金提供するものである：
ｒ （ｉ ） Ｍｇ０． ５〜５重量％、（１ｉ） Ｓ
ｉ １重量％未満、
（１ｉｉ）Ｚ ｒ ０． ２〜３重量９６、（ｉｖ）Ｆ
ｅ及び／又はＣｒ０．５〜５重量２６、（ｖ）Ｃｕ０．
４重量％未満、および
（ｖｌ）残余が実質的にＡΩ
からなることを特徴とする耐熱性アルミニウム粉末合金
。」
以下、本発明Ａ［粉末合金の各添加成分について説明す
る。これらの各添加成分は、一般の合金における添加成
分と同様に、相互に関連しつつ合金全体の物性に影響す
るものであり、それぞれの限定理由を個別に論すること
は、必ずしも妥当であるとはいえないが、一応の限定理
由を示せば、以下の通りである。Means for Solving the Problems As a result of extensive research in view of the problems of the prior art as described above, the inventors of the present invention have found that the G content of Fe and/or Cr and Zr can be suppressed to an appropriate level and a specific amount can be obtained. A2 alloy containing Mg of
A! It has been found that this alloy exhibits extremely excellent performance as a Q-PM alloy. That is, the present invention provides an AQ gold alloy having the composition shown below: r (i) Mg0. 5-5% by weight, (1i)S
i less than 1% by weight, (1ii) Z r 0. 2-3 weight 96, (iv)F
e and/or Cr0.5-5 weight 26, (v) Cu0.
A heat-resistant aluminum powder alloy, characterized in that less than 4% by weight, and the remainder (vl) consists essentially of AΩ. ” Hereinafter, each additive component of the present invention A [powder alloy] will be explained. Each of these additive components, like the additive components in general alloys, are interrelated and affect the physical properties of the alloy as a whole, and it is not necessarily appropriate to discuss the reasons for each limitation individually. No, but the reason for the limitation is as follows.
１、 Ｍｇ
０．５〜５％の範囲内のＭｇは、Ａ２合金に固溶体硬化
を与えるのみならず、加工硬化率を高め、合金密度を低
下させる。Ｍｇの量が、０，５重量％（以下単に％とす
る）未満の場合には、添加による効果が十分に発揮され
ず、一方５％を上回る場合には、Ａ２合金が応力腐蝕を
生じやすくなる。1. Mg Mg in the range of 0.5 to 5% not only imparts solid solution hardening to the A2 alloy, but also increases the work hardening rate and lowers the alloy density. If the amount of Mg is less than 0.5% by weight (hereinafter simply referred to as %), the effect of addition will not be sufficiently exhibited, while if it exceeds 5%, the A2 alloy will easily suffer from stress corrosion. Become.
さらに、Ｍｇが５％を上回る場合には、Ｍｇが他の添加
元素と反応して粗大な二次相粒子を形成し、疲労抵抗を
阻害することがある。Ｍｇが０．５〜５％の範囲内にあ
る本発明合金は、Ｍｇを含まない対応する組成のＡ℃金
合金比して、室温と２００℃との間でより高い強度を示
し、且つ熱間鍛造温度のような高温下での延性にも優れ
ている。Furthermore, if Mg exceeds 5%, Mg may react with other additive elements to form coarse secondary phase particles, which may impair fatigue resistance. The alloy of the present invention with Mg in the range of 0.5-5% exhibits higher strength between room temperature and 200°C than a corresponding A°C gold alloy without Mg, and has higher thermal resistance. It also has excellent ductility at high temperatures such as inter-forging temperatures.
Ｍｇの含＝ｆｆｆｆｆｉは、１〜３％とすることがより
好ましい。The Mg content = fffffi is more preferably 1 to 3%.
ＩＩ、５ｉ
Ｓｉの含量は、出来るだけ少ないことが好ましく、実用
上の観点からは、１％以下、より好ましくは０．５％以
下とする。Ｓｔの曾が１％を上回る場合には、Ａ！２Ｆ
ｅＳｉ、初晶Ｓｉ。The content of II,5i Si is preferably as small as possible, and from a practical standpoint, it is 1% or less, more preferably 0.5% or less. If the value of St exceeds 1%, then A! 2F
eSi, primary Si.
Ｍｇ２Ｓｉなどの種々の粒子が形成されて、１２合金の
延性及び疲労強度を低下させる。Various particles such as Mg2Si are formed and reduce the ductility and fatigue strength of the 12 alloy.
ｍ、Ｚｒ
Ａ！Ｑ中のＺｒは、分散性及び溶解性が低く、凝固時及
び過飽和Ａ℃粉末合金の３５０〜５００℃での熱処理時
にマトリックスにコヒーレントな微細な球状析出物分散
相（準安定ＺｒＡＬ３立法品）を形成する。これらの分
散相は、微小構造を安定化させ、熱的安定性を改善し、
強度を増大させる。m, Zr A! Zr in Q has low dispersibility and solubility, and forms a coherent fine spherical precipitate dispersed phase (metastable ZrAL3 cubic product) in the matrix during solidification and heat treatment at 350-500°C of supersaturated A°C powder alloy. Form. These dispersed phases stabilize the microstructure, improve thermal stability,
Increase strength.
Ｚｒの含有口は、０．２〜３％、より好ましくは０、．
５〜２．０％とする。Ｚｒの量が、０．２％未満の場合
には、添加による効果が十分に発揮されず、一方３％を
上回る場合には、Ａ２合金の溶融温度が急激に」二昇し
、製造が困難となる。The Zr content is 0.2 to 3%, more preferably 0.
5 to 2.0%. If the amount of Zr is less than 0.2%, the effect of addition will not be fully exhibited, while if it exceeds 3%, the melting temperature of the A2 alloy will rise rapidly, making it difficult to manufacture. becomes.
ＴＶ、Ｆｅ及び／又はＣｒ
これら元素は、１２粉末合金の強度及び熱的安定性を改
善するための基本的成分である。Ｆｅ及び／又はＣｒは
、他の添加元素と結合して比較的粒径の小さい、均一に
分散した金属間化合物を形成する。これらの分散相は、
転位及び粒界移動を阻止し、その結果、熱的安定性を改
善する。Ｆｅ及び／又はＣｒの量が、０．５〜５％の範
囲内では、高い疲労強度及び延性並びに低密度を維持し
つつ、必要な強度と熱安定性が確保される。Ｃｒの量は
、１〜３％とすることがより好ましい。TV, Fe and/or Cr These elements are the basic components for improving the strength and thermal stability of the 12 powder alloy. Fe and/or Cr combine with other additive elements to form uniformly dispersed intermetallic compounds with relatively small particle sizes. These dispersed phases are
Prevents dislocations and grain boundary migration, thus improving thermal stability. When the amount of Fe and/or Cr is within the range of 0.5 to 5%, the necessary strength and thermal stability are ensured while maintaining high fatigue strength and ductility as well as low density. The amount of Cr is more preferably 1 to 3%.
Ｖ、Ｃｕ
Ｃｕの量は、０．４％未満とする。Ｃｕを添加する場合
には、ＡＲ金合金マトリックスに固溶して、常温におけ
る機械的強度を向上させるが、延性を著るしく低下させ
る。また、約２００℃以上の高温における強度を低下さ
せるため、本発明においては、Ｃｕの量はできるだけ低
いことが好ましい。V, Cu The amount of Cu is less than 0.4%. When Cu is added, it forms a solid solution in the AR gold alloy matrix and improves mechanical strength at room temperature, but significantly reduces ductility. Furthermore, in order to reduce the strength at high temperatures of about 200° C. or higher, in the present invention, the amount of Cu is preferably as low as possible.
本発明の、１−ＰＭ合金は、常法にしたがって、谷成分
を溶解し、エアアトマイズ法、単ロール法、双ロール法
、スプラット クエンチ法などの急冷凝固法により粉末
化し、あるいは機械的な粉砕法を組み合わせて粉末化し
、必要ならばふるい分けすることにより得られる。得ら
れた粉末は、やはり常法にしたがって、冷間予備成形し
、適切な温度で押出・鍛造加工により成形し、必要なら
ば、機械加工することによって所望の製品とされる。The 1-PM alloy of the present invention is produced by melting the valley components and pulverizing it by a rapid solidification method such as air atomization, single roll method, twin roll method, or splat quench method, or by mechanically pulverizing it. It is obtained by powdering by a combination of methods and, if necessary, by sieving. The obtained powder is then cold preformed, shaped by extrusion/forging at an appropriate temperature, and, if necessary, machined to form the desired product, again according to conventional methods.
発明の効果 本発明によれば、以下の様な効果が達成される。Effect of the invention According to the present invention, the following effects are achieved.
（イ）従来の耐熱ＡΩ−ＰＭ合金に比して、軽量のＡジ
ーＰＭ合金が得られる。(a) Compared to the conventional heat-resistant AΩ-PM alloy, a lightweight A-G PM alloy can be obtained.
（ロ）得られたＡρ−ＰＭ合金は、機械的性質、熱間成
形加工性及び耐疲労特性に優れている。(b) The obtained Aρ-PM alloy has excellent mechanical properties, hot formability, and fatigue resistance.
（ハ）得られたＡΩ−ＰＭ合金は、常温から２００℃ま
での温度域において、熱的安定性に優れている。(c) The obtained AΩ-PM alloy has excellent thermal stability in the temperature range from room temperature to 200°C.
（ニ）したがって、本発明Ａρ−ＰＭ合金は、高温での
成形、例えば鍛造により製造され、２００°Ｃ近傍の高
温で使用される機械部品（、例えば自動車用エンジンの
コンロッドなど）の材料として有用である。(d) Therefore, the Aρ-PM alloy of the present invention is useful as a material for mechanical parts (such as connecting rods for automobile engines) that are produced by forming at high temperatures, such as forging, and are used at high temperatures around 200°C. It is.
（ホ）また、本発明ＡΩ−ＰＭ合金は、その優れた性能
の故に、既存のＡ！２−ＰＭ合金が使用できなかった種
々の分野で使用可能であり、Ａｌ１−ＰＭ合金の利用分
野を大きく拡大するものである。(e) Furthermore, the AΩ-PM alloy of the present invention is superior to the existing AΩ-PM alloy due to its excellent performance. It can be used in various fields where 2-PM alloy could not be used, and greatly expands the field of application of Al1-PM alloy.
実施例
以下に実施例を示し、本発明の特徴とするところをより
一層明確にする。EXAMPLES Examples will be shown below to further clarify the features of the present invention.
実施例１
第１表に示す組成のＡＩ２−ＰＭ合金をそれぞれ調製し
た後、平均凝固速度Ｉ Ｘ １０３℃／秒でエアアトマ
イズ法により粉末化し、ふるい分けして１００メツシュ
通過粉体（１５０μｍ以下）を得た。第２表に各合金粉
体の粒度分布を示す。Example 1 After preparing AI2-PM alloys having the compositions shown in Table 1, they were pulverized by air atomization at an average solidification rate of I x 103°C/sec, and sieved to obtain powder (150 μm or less) that passed through 100 meshes. Obtained. Table 2 shows the particle size distribution of each alloy powder.
１−記で得られた各合金粉体をコールド アイソスタテ
ィック プレス（ＣＩ Ｐ）法により円筒型試料（直径
３０ｍｍｘ高さ８０ｍｍ、相対密度７０〜８０９６ ）
にに成形し、空気中４００°Ｃで３０分間子熱した後、
押出し比１０：１、ラム速度２．５ｍｍ／秒で直径１０
ｍｍのロッドに押出成形した。該ロッドを機械加工して
、平行部長さ４０ｍｍｘ直径４．４ｍｍの試験片を製造
し、引張り試験及び疲労試験に供した。これらの試験結
果をロッドの密度ともに第３表に示す。Each alloy powder obtained in 1- was made into a cylindrical sample (diameter 30 mm x height 80 mm, relative density 70-8096) by cold isostatic pressing (CIP) method.
After molding into cubes and incubating in air at 400°C for 30 minutes,
diameter 10 at an extrusion ratio of 10:1 and a ram speed of 2.5 mm/s.
It was extruded into a mm rod. The rod was machined to produce a test piece with a parallel length of 40 mm and a diameter of 4.4 mm, which was subjected to a tensile test and a fatigue test. The results of these tests are shown in Table 3 together with the density of the rods.
第１表乃至第３表に示す結果から、本発明のＡρ−ＰＭ
金合金、ＡＡ２６１８に匹敵する延性と密度を有してお
り、疲労強度の点では、ＡＡ２６１８を大きく上回って
いる。From the results shown in Tables 1 to 3, it can be seen that Aρ-PM of the present invention
It has ductility and density comparable to the gold alloy AA2618, and greatly exceeds AA2618 in terms of fatigue strength.
また、比較合金Ｇとの対比では、本発明Ａρ−ＰＭ合金
は、引張り強度及び疲労強度においては同等であるが、
延性に優れ、密度も小さい。In addition, in comparison with Comparative Alloy G, the Aρ-PM alloy of the present invention has the same tensile strength and fatigue strength, but
It has excellent ductility and low density.
（以上）
手続十市正書（自発）
昭和６３年４月２７日 １
特許庁長官 小 川 ノ、ト 夫 殿
１ 事件の表示
昭和６３年特許願第７０９５２号
２ 発明の名称
ｍ−＋−へ
事件との関係 特許出願人
東洋アルミニウム株式会社
４代理人
自 発
別紙添付の通り ゛・ ・−・・・′−
・′
補正の内容
明細書第１１頁第２表を下記の通りに訂正すジ。(Above) Procedural Ten City Authorization (Spontaneous) April 27, 1988 1 Director General of the Patent Office Tono Ogawa 1 Indication of the Case 1988 Patent Application No. 70952 2 Name of the Invention m-+- Relationship to the case: Patent applicant Toyo Aluminum Co., Ltd. (4 agents) As attached: ゛・ ・−・・・′−
・' Table 2 on page 11 of the detailed description of amendments shall be corrected as follows.
明細書第１２頁第４行「にに成形し」とあるつを「に成
形し」と訂正する。In the fourth line of page 12 of the specification, the phrase ``Ni-molashi'' is corrected to ``Ni-molashi''.
（以 上）(that's all)
Claims (1)
Ｃｕ０．４重量％未満、および （ｖｉ）残余が実質的にＡｌ からなることを特徴とする耐熱性アルミニウム粉末合金
。(1) (i) Mg0.5-5% by weight, (ii) Si less than 1% by weight, (iii) Zr0.2-3% by weight, (iv) Fe and/or Cr0.5-5% by weight, (v )
A heat-resistant aluminum powder alloy characterized in that it contains less than 0.4% by weight of Cu, and (vi) the remainder consists essentially of Al.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7095288A JP2711296B2 (en) | 1988-03-24 | 1988-03-24 | Heat resistant aluminum alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7095288A JP2711296B2 (en) | 1988-03-24 | 1988-03-24 | Heat resistant aluminum alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01242749A true JPH01242749A (en) | 1989-09-27 |
| JP2711296B2 JP2711296B2 (en) | 1998-02-10 |
Family
ID=13446352
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7095288A Expired - Lifetime JP2711296B2 (en) | 1988-03-24 | 1988-03-24 | Heat resistant aluminum alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2711296B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0234738A (en) * | 1988-07-25 | 1990-02-05 | Furukawa Alum Co Ltd | Heat-resistant aluminum alloy material and its manufacture |
| US7177384B2 (en) | 1999-09-09 | 2007-02-13 | Mitsubishi Heavy Industries, Ltd. | Aluminum composite material, manufacturing method therefor, and basket and cask using the same |
| JP2007092117A (en) * | 2005-09-28 | 2007-04-12 | Toyota Central Res & Dev Lab Inc | Aluminum alloy with high strength and low specific gravity |
| CN113330132A (en) * | 2019-01-24 | 2021-08-31 | 肯联铝业技术中心 | Method for manufacturing an aluminium alloy part comprising at least zirconium and magnesium |
| WO2023162540A1 (en) * | 2022-02-24 | 2023-08-31 | 株式会社神戸製鋼所 | Aluminum alloy material and method for producing same |
-
1988
- 1988-03-24 JP JP7095288A patent/JP2711296B2/en not_active Expired - Lifetime
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0234738A (en) * | 1988-07-25 | 1990-02-05 | Furukawa Alum Co Ltd | Heat-resistant aluminum alloy material and its manufacture |
| US7177384B2 (en) | 1999-09-09 | 2007-02-13 | Mitsubishi Heavy Industries, Ltd. | Aluminum composite material, manufacturing method therefor, and basket and cask using the same |
| JP2007092117A (en) * | 2005-09-28 | 2007-04-12 | Toyota Central Res & Dev Lab Inc | Aluminum alloy with high strength and low specific gravity |
| CN113330132A (en) * | 2019-01-24 | 2021-08-31 | 肯联铝业技术中心 | Method for manufacturing an aluminium alloy part comprising at least zirconium and magnesium |
| WO2023162540A1 (en) * | 2022-02-24 | 2023-08-31 | 株式会社神戸製鋼所 | Aluminum alloy material and method for producing same |
| JP2023123344A (en) * | 2022-02-24 | 2023-09-05 | 株式会社神戸製鋼所 | Aluminum alloy material and method for producing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2711296B2 (en) | 1998-02-10 |
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