JPH07242976A - Aluminum alloy for elongation, excellent in heat resistance, and its production - Google Patents

Aluminum alloy for elongation, excellent in heat resistance, and its production

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Publication number
JPH07242976A
JPH07242976A JP3112594A JP3112594A JPH07242976A JP H07242976 A JPH07242976 A JP H07242976A JP 3112594 A JP3112594 A JP 3112594A JP 3112594 A JP3112594 A JP 3112594A JP H07242976 A JPH07242976 A JP H07242976A
Authority
JP
Japan
Prior art keywords
alloy
aluminum alloy
heat resistance
elongation
strength
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.)
Withdrawn
Application number
JP3112594A
Other languages
Japanese (ja)
Inventor
Makoto Saga
誠 佐賀
Masao Kikuchi
正夫 菊池
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Nippon Steel Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Priority to JP3112594A priority Critical patent/JPH07242976A/en
Publication of JPH07242976A publication Critical patent/JPH07242976A/en
Withdrawn legal-status Critical Current

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Abstract

PURPOSE:To maintain solid solution strengthening property and precipitation strengthening property and to provide superior heat resistance by specifying respective contents of Cu, Mg, Si, Fe, Ni, and Ti in an Al alloy and also specifying mutual quantitative relationship between Fe and CONSTITUTION:This Al alloy for elongation has a composition consisting of, by weight, 1.5-4.0% Cu, 1.0-2.0% Mg, 0.1-0.7% Si, 0.1-0.7% Fe, 0.5-1.5% Ni, 0.04-0.2% Ti, and the balance Al with inevitable impurities and satisfying the relation in 0.4Fe+0.6Ni<=1.0. If necessary, one or more kinds among 0.1-0.7% Mn, 0.05-0.5% V, and 0.1-0.3% Zr are further incorporated. This Al alloy is cast and worked by conventional methods and subjected to solution heat treatment and then to aging treatment at 180-220 deg.C for 10-30hr. By this method, the Al alloy material for elongation, having >=154N/mm<2> proof stress even at a temp. as high as about 250 deg.C, can be obtained.

Description

【発明の詳細な説明】Detailed Description of the Invention

【0001】[0001]

【産業上の利用分野】本発明は、自動車、鉄道車両、船
舶等輸送分野において、エンジン部品、コンプレッサー
等の機械部品用材料として200℃以上の高温雰囲気の
下でも使用される耐熱性に優れた展伸用アルミニウム合
金およびその製造方法に関するものである。
INDUSTRIAL APPLICABILITY The present invention is excellent in heat resistance and can be used as a material for mechanical parts such as engine parts and compressors in a transportation field such as automobiles, railway vehicles and ships even under a high temperature atmosphere of 200 ° C. or higher. The present invention relates to an wrought aluminum alloy and a method for manufacturing the same.

【0002】[0002]

【従来の技術】耐熱性に優れた展伸用アルミニウム合金
としては、A・A規格で規定されているように2218
合金、2219合金、2618合金が良く知られてい
る。しかしながらこれらの合金は、150℃以上の使用
温度における強度の点で必ずしも十分な特性を有してい
るものではなかった。そこで特開平1〜290741号
公報に開示されているようなAl−Cu−Mg系の耐熱
性に優れたアルミニウム合金が提示されている。
2. Description of the Related Art As an aluminum alloy for wrought having excellent heat resistance, 2218 is specified as specified in the A / A standard.
Alloys, 2219 alloys and 2618 alloys are well known. However, these alloys do not always have sufficient properties in terms of strength at operating temperatures of 150 ° C. or higher. Therefore, an Al—Cu—Mg-based aluminum alloy excellent in heat resistance as disclosed in JP-A No. 1-290741 is proposed.

【0003】[0003]

【発明が解決しようとする課題】上記の提案された耐熱
性アルミニウム合金は、確かに150℃程度までは優れ
た高温強度特性を有している。しかしながら使用温度が
200℃以上とますます上昇する状況においてはこの合
金でもまだ不十分と言わざるを得ない。本発明は、従来
よりもさらに高い200℃以上の使用温度においても高
温強度に優れた展伸用アルミニウム合金およびその製造
方法を提供することを目的としたものである。
The heat-resistant aluminum alloy proposed above certainly has excellent high-temperature strength characteristics up to about 150 ° C. However, it must be said that this alloy is still insufficient in the situation where the operating temperature rises above 200 ° C. An object of the present invention is to provide a wrought aluminum alloy excellent in high temperature strength even at a use temperature of 200 ° C. or higher, which is higher than before, and a method for producing the same.

【0004】[0004]

【課題を解決するための手段】本発明者等は、上述の課
題を解決するために耐熱性を阻害する要因について種々
実験検討を重ねた。その結果、特に2618合金の高温
における強度低下の主要因は、合金中に含有されるF
e,Niが高温で粗大なCu2 FeAl7 ,Cu 3 Ni
Al6 等の金属間化合物を形成し、Al母相中に固溶す
るCu濃度を低下させるためであることを究明した。そ
してFeとNiの単独含有量の規制とともに、FeとN
iの相互の量的な関係も規定することによって、高温で
のCuによる固溶強化能および析出強化能が維持され、
200℃以上の高温において従来よりも優れた耐熱性を
有した合金を得るに至った。本発明はこの知見に基づき
なされたものである。
Means for Solving the Problems The present inventors
Various factors that impede heat resistance to solve the problem
Experiments were repeated. As a result, especially the high temperatures of 2618 alloy
The main cause of the strength decrease in the alloy is F contained in the alloy.
e and Ni are high temperature and coarse Cu2FeAl7, Cu 3Ni
Al6Form an intermetallic compound such as, and form a solid solution in the Al matrix phase
It was clarified that this is to reduce the Cu concentration. So
The Fe and Ni contents are regulated together with the Fe and N contents.
By specifying the mutual quantitative relationship of i,
The solid solution strengthening ability and precipitation strengthening ability of Cu are maintained,
Superior heat resistance than before at high temperatures of 200 ° C or higher
It came to the obtained alloy. The present invention is based on this finding
It was made.

【0005】本発明の第1は、 Cu:1.5 〜4.0% Mg:1.0 〜2.0% Si:0.1 〜0.7% Fe:0.1 〜0.7% Ni:0.5 〜1.5% Ti:0.04〜0.2% を含有し、かつFeとNiが、 0.4Fe+0.6Ni≦1.0 の関係を有し、残部がAlおよび不可避不純物からなる
ことを特徴とする。
The first aspect of the present invention is: Cu: 1.5 to 4.0% Mg: 1.0 to 2.0% Si: 0.1 to 0.7% Fe: 0.1 to 0.7% Ni: 0.5 to 1.5% Ti: 0.04 to 0.2%, Fe and Ni have a relationship of 0.4Fe + 0.6Ni ≦ 1.0, and the balance is Al and unavoidable. It is characterized by comprising impurities.

【0006】本発明の第2は、第1の発明に対してさら
に、 Mn:0.1 〜0.7% V:0.05〜0.5% Zr:0.1 〜0.3% のうち1種以上を含有することを特徴とする。本発明の
第3は上記成分組成からなるアルミニウム合金を、常法
により鋳造、加工した後に溶体化処理を施し、次いで1
80〜220℃で20〜30時間の時効処理を施すこと
によって製造することを特徴とする。
The second aspect of the present invention further comprises: Mn: 0.1-0.7% V: 0.05-0.5% Zr: 0.1-0.3% It is characterized by containing at least one of them. The third aspect of the present invention is to cast an aluminum alloy having the above-mentioned composition by a conventional method, process it, and then subject it to solution treatment,
It is characterized by being manufactured by performing an aging treatment at 80 to 220 ° C. for 20 to 30 hours.

【0007】[0007]

【作用】次に本発明におけるアルミニウム合金の成分組
成範囲の限定理由について説明する。Cu,Mg,S
i:CuはAl母相中に固溶し、固溶強化によって機械
的強度を大幅に向上させる効果を持つ。またCu,M
g,Siは相互に共存することによって、Al2 Cu,
Al2 CuMg,Mg2 Si等の析出強化による機械的
強度向上に寄与する。そこで、それぞれの元素の含有量
は、重量%でCu:1.5〜4.0%、Mg:1.0〜
2.0%、Si:0.1〜0.7%とした。Cu量が
1.5%未満、Mg量が1.0%未満、Si量が0.1
%未満では、いずれにおいても200℃以上の高温にお
いて必要とされる強度が得られない。一方、Cu量が
4.0%超に含有すると、Cu系金属間化合物析出の駆
動力が過度に大きくなりCuの固溶強化能および析出強
化能が低下してしまう。またMg量が2.0%超、Si
量が0.7%超に過剰に含有しても、強度向上効果は飽
和する。好ましい成分範囲は、Cu:2.4〜3.8
%、Mg:1.4〜1.8%、Si:0.3〜0.6%
である。
Next, the reason for limiting the component composition range of the aluminum alloy in the present invention will be explained. Cu, Mg, S
i: Cu forms a solid solution in the Al matrix phase and has the effect of significantly improving the mechanical strength by solid solution strengthening. Also Cu, M
Since g and Si coexist with each other, Al 2 Cu,
It contributes to improvement of mechanical strength by precipitation strengthening of Al 2 CuMg, Mg 2 Si and the like. Therefore, the content of each element is, by weight%, Cu: 1.5 to 4.0%, Mg: 1.0 to
2.0%, Si: 0.1 to 0.7%. Cu amount less than 1.5%, Mg amount less than 1.0%, Si amount 0.1
If it is less than%, the strength required at a high temperature of 200 ° C. or higher cannot be obtained in any case. On the other hand, if the Cu content exceeds 4.0%, the driving force for precipitation of the Cu-based intermetallic compound becomes excessively large, and the solid solution strengthening ability and precipitation strengthening ability of Cu decrease. Also, the amount of Mg exceeds 2.0%, Si
Even if the amount exceeds 0.7%, the strength improving effect is saturated. A preferable component range is Cu: 2.4 to 3.8.
%, Mg: 1.4 to 1.8%, Si: 0.3 to 0.6%
Is.

【0008】Fe,Ni:FeやNiはAlとの間に金
属間化合物を分散・形成し、合金の高温強度を向上させ
るために、Feは0.1%以上、Niは0.5%を必要
とする。しかしながら両者はともに過剰に含有すると、
金属間化合物が粗大化してしまうだけでなく、高温でC
2 FeAl7 やCu3 NiAl6 を形成してAl母相
中の固溶Cu量を下げ、かえって強度を低下させてしま
うので、Feは0.7%以下、Niは1.5%以下とす
る。好ましい成分範囲としては、Fe:0.3〜0.6
5%、Ni:0.8〜1.3%である。本発明において
はFeとNiを上記のように単独に限定するのみなら
ず、FeとNiの相互の量的な関係をも規定する。その
量的関係は、0.4Fe+0.6Ni≦1.0とする。
FeとNiの量的関係がこの式を満たさないと、高温に
おける強度が十分に得られない。
Fe, Ni: Fe and Ni disperse and form an intermetallic compound between Al and Al, and in order to improve the high temperature strength of the alloy, Fe is 0.1% or more and Ni is 0.5%. I need. However, if both are excessively contained,
Not only does the intermetallic compound coarsen, but also C
Since u 2 FeAl 7 and Cu 3 NiAl 6 are formed to reduce the amount of solid-soluted Cu in the Al matrix phase and rather reduce the strength, Fe is 0.7% or less and Ni is 1.5% or less. To do. As a preferable component range, Fe: 0.3 to 0.6
5%, Ni: 0.8-1.3%. In the present invention, not only is Fe and Ni limited to the above, but also the quantitative relationship between Fe and Ni is specified. The quantitative relationship is 0.4Fe + 0.6Ni ≦ 1.0.
If the quantitative relationship between Fe and Ni does not satisfy this formula, sufficient strength at high temperatures cannot be obtained.

【0009】Ti:Tiは、Alとの間に金属間化合物
を形成し結晶粒微細化に寄与する。元素の含有量は、T
i:0.04〜0.2%とした。Ti量が0.04%未
満では上記の効果を十分に得ることはできない。しか
し、Ti量が0.2%超に含有されるとAlとの間に粗
大な金属間化合物を形成して加工性、機械的性質を損な
うことになる。好ましい成分範囲は、Ti:0.07〜
0.16%である。
Ti: Ti forms an intermetallic compound with Al and contributes to grain refinement. The content of element is T
i: 0.04 to 0.2%. If the Ti content is less than 0.04%, the above effect cannot be sufficiently obtained. However, if the Ti content exceeds 0.2%, a coarse intermetallic compound is formed with Al and the workability and mechanical properties are impaired. A preferable component range is Ti: 0.07 to
It is 0.16%.

【0010】Mn,V,Zr:上述した成分が本発明の
必須成分であるが、さらに高温強度の確保を容易にする
ためには必要に応じてMn,V,Zrを含有させるとよ
い。Mn,V,Zrは、いずれの元素もAlとの間に金
属間化合物を形成し結晶粒微細化に寄与するとともに、
特にZrとVは、常温から高温域にわたって回復・再結
晶を抑制して強度の低下を防止する。これらの作用効果
を得るためにそれぞれの元素の含有量は、Mn:0.1
〜0.7%、V:0.05〜0.5%、Zr:0.1〜
0.3%とした。Mn量が0.1%未満、V量が0.0
5%未満、Zr量が0.1%未満では上記の効果を十分
に得ることができない。しかし、Mn量が0.7%超、
V量が0.5%超、Zr量が0.3%超に含有されると
粗大な金属間化合物を形成して加工性、機械的性質を損
なうことになる。好ましい成分範囲は、Mn:0.4〜
0.6%、V:0.2〜0.4%、Zr:0.15〜
0.25%である。
Mn, V, Zr: Although the above-mentioned components are essential components of the present invention, Mn, V, Zr may be added if necessary in order to further secure high temperature strength. Any of Mn, V, and Zr forms an intermetallic compound with Al and contributes to grain refinement.
In particular, Zr and V suppress recovery and recrystallization from normal temperature to high temperature range and prevent a decrease in strength. In order to obtain these effects, the content of each element is Mn: 0.1
~ 0.7%, V: 0.05 to 0.5%, Zr: 0.1
It was set to 0.3%. Mn amount is less than 0.1%, V amount is 0.0
If the amount is less than 5% and the Zr amount is less than 0.1%, the above effect cannot be sufficiently obtained. However, the Mn content exceeds 0.7%,
If the V content exceeds 0.5% and the Zr content exceeds 0.3%, a coarse intermetallic compound is formed and workability and mechanical properties are impaired. A preferable component range is Mn: 0.4 to
0.6%, V: 0.2 to 0.4%, Zr: 0.15
It is 0.25%.

【0011】上述のように成分規定した本発明のアルミ
ニウム合金は、従来のAl−Cu−Mg系合金の製造方
法に準じて製造できる。しかし、Cuによる固溶強化、
Cu,Mg,Siによる析出強化、AlとFeおよびA
lとNiとの間での金属間化合物形成による分散強化を
有効に活用するためには、固相線温度以下5〜25℃の
温度範囲で溶体化処理を施し、次いで180〜220℃
で20〜30時間の時効処理を施すことが望ましい。時
効処理条件における各下限値は、これらを下回ると強化
に作用し得るだけの金属間化合物が形成されないことか
ら規定する。一方、各上限値は、これらを上回ると形成
された金属間化合物が粗大化し、強化作用が得にくくな
るとともに、Cuの固溶強化能が低下するために規定す
る。
The aluminum alloy of the present invention, whose components are defined as described above, can be manufactured according to the conventional manufacturing method of an Al-Cu-Mg alloy. However, solid solution strengthening by Cu,
Precipitation strengthening by Cu, Mg, Si, Al and Fe and A
In order to effectively utilize the dispersion strengthening due to the formation of the intermetallic compound between 1 and Ni, the solution treatment is performed in the temperature range of 5 to 25 ° C. below the solidus temperature, and then 180 to 220 ° C.
It is desirable to perform aging treatment for 20 to 30 hours. The respective lower limit values under the aging treatment conditions are defined because below the above range, an intermetallic compound capable of acting on strengthening is not formed. On the other hand, the respective upper limit values are specified because if the amount exceeds the upper limit, the formed intermetallic compound becomes coarse and it becomes difficult to obtain the strengthening action, and the solid solution strengthening ability of Cu decreases.

【0012】[0012]

【実施例】本発明の成分組成範囲内にある20種類の合
金(表1にそれらの化学組成を示す)を鋳造した後、5
40℃で6時間の均質化焼鈍を施し、鍛造により直径1
6mmの丸棒に加工した。次いで540℃の溶体化処理
後、200℃で20時間の時効処理を行った。得られた
丸棒より試験片を作製して、室温、150℃,200
℃,250℃における機械的性質(耐力および伸び)を
調査した。また比較例として特にFeとNiの単独量の
規定値からの外れ(比較例1,2,3,4)、およびF
eとNiの相互の量的関係の規定値からの外れ(比較例
5,6,7)、さらに従来例として従来材の2218合
金(従来例1)、2219合金(従来例2)、2618
合金(従来例3)の試験片も準備した。表2の調査結果
から明かなように、本発明の合金は、従来材よりも優れ
た高温強度特性を有している。特にその優位性は高温に
なるほど顕著であり、本発明の合金は150℃において
は従来材と同等あるいはそれ以上の耐力を有するのに対
し、250℃では154N/mm2 以上と、従来材を大
幅に凌ぐ耐力を保持することができる。
EXAMPLE After casting 20 alloys (the chemical compositions of which are shown in Table 1) within the compositional range of the present invention, 5
After homogenizing annealing at 40 ℃ for 6 hours, diameter 1 by forging
It was processed into a 6 mm round bar. Then, after solution treatment at 540 ° C., aging treatment was performed at 200 ° C. for 20 hours. A test piece was prepared from the obtained round bar, and it was stored at room temperature, 150 ° C, 200 ° C.
The mechanical properties (proof stress and elongation) at 250C and 250C were investigated. Further, as comparative examples, in particular, deviations from the specified values of the individual amounts of Fe and Ni (Comparative Examples 1, 2, 3, 4), and F
The deviation of the quantitative relationship between e and Ni from the specified value (Comparative Examples 5, 6, 7), and as conventional examples, the conventional material 2218 alloy (Conventional example 1), 2219 alloy (Conventional example 2), 2618
A test piece of alloy (conventional example 3) was also prepared. As is clear from the results of the investigation in Table 2, the alloy of the present invention has superior high temperature strength properties to the conventional materials. In particular, the superiority becomes remarkable as the temperature rises, and the alloy of the present invention has a proof stress equal to or higher than that of the conventional material at 150 ° C., while it is 154 N / mm 2 or more at 250 ° C. It is possible to maintain the proof strength that surpasses.

【0013】[0013]

【表1】 [Table 1]

【0014】[0014]

【表2】 [Table 2]

【0015】[0015]

【発明の効果】本発明のアルミニウム合金は、高温強度
向上に寄与するFe,Niの作用効果を有効に発揮させ
るとともに、固溶強化、析出強化の両者に効果のあるC
u、析出強化元素のMg,Si、結晶粒微細化効果を有
するTiをそれぞれ含有させ、さらには必要に応じて高
温での回復・再結晶抑制効果を有するMn,Zr,Vを
共存させることによって高い高温強度を付与することを
特徴とする。このような構成とすることによって250
℃の高温においても、154N/mm2 以上の耐力を発
揮することが可能となる。したがって自動車用エンジン
部品をはじめとする高温環境下で使用される機械部品に
非常に適した材料となり得る。
INDUSTRIAL APPLICABILITY The aluminum alloy of the present invention effectively exhibits the effects of Fe and Ni which contribute to the improvement of high temperature strength, and the effect of C on both solid solution strengthening and precipitation strengthening.
By incorporating u, Mg and Si as precipitation strengthening elements, and Ti having a grain refining effect, and coexisting with Mn, Zr, and V having a high temperature recovery / recrystallization suppressing effect, if necessary. It is characterized by imparting high temperature strength. With such a configuration, 250
It is possible to exhibit a yield strength of 154 N / mm 2 or more even at a high temperature of ° C. Therefore, it can be a very suitable material for mechanical parts used in high temperature environments such as automobile engine parts.

Claims (3)

【特許請求の範囲】[Claims] 【請求項1】 重量%で、 Cu:1.5 〜4.0% Mg:1.0 〜2.0% Si:0.1 〜0.7% Fe:0.1 〜0.7% Ni:0.5 〜1.5% Ti:0.04〜0.2% を含有し、かつFeとNiが、 0.4Fe+0.6Ni≦1.0 の関係を有し、残部がAlおよび不可避不純物からなる
耐熱性に優れた展伸用アルミニウム合金。
1. By weight%, Cu: 1.5 to 4.0% Mg: 1.0 to 2.0% Si: 0.1 to 0.7% Fe: 0.1 to 0.7% Ni : 0.5 to 1.5% Ti: 0.04 to 0.2%, Fe and Ni have a relationship of 0.4Fe + 0.6Ni ≦ 1.0, and the balance is Al and unavoidable impurities. An wrought aluminum alloy with excellent heat resistance.
【請求項2】 請求項1記載の成分を含有するアルミニ
ウム合金に、さらに重量%で、 Mn:0.1 〜0.7% V:0.05〜0.5% Zr:0.1 〜0.3% のうち1種以上を含有する耐熱性に優れた展伸用アルミ
ニウム合金。
2. The aluminum alloy containing the component according to claim 1, further comprising, by weight%, Mn: 0.1 to 0.7% V: 0.05 to 0.5% Zr: 0.1 to 0. An wrought aluminum alloy with excellent heat resistance containing at least one of 3%.
【請求項3】 請求項1または2記載の成分を含有する
アルミニウム合金を、常法によって鋳造、加工した後に
溶体化処理を施し、次いで180〜220℃で10〜3
0時間の時効処理を施すことを特徴とする耐熱性に優れ
た展伸用アルミニウム合金の製造方法。
3. An aluminum alloy containing the component according to claim 1 or 2 is cast and processed by a conventional method and then solution heat treated, and then 10 to 3 at 180 to 220 ° C.
A method for producing an wrought aluminum alloy having excellent heat resistance, which comprises performing an aging treatment for 0 hours.
JP3112594A 1994-03-01 1994-03-01 Aluminum alloy for elongation, excellent in heat resistance, and its production Withdrawn JPH07242976A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP3112594A JPH07242976A (en) 1994-03-01 1994-03-01 Aluminum alloy for elongation, excellent in heat resistance, and its production

Applications Claiming Priority (1)

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JP3112594A JPH07242976A (en) 1994-03-01 1994-03-01 Aluminum alloy for elongation, excellent in heat resistance, and its production

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JP2005206927A (en) * 2004-01-26 2005-08-04 Furukawa Sky Kk Compressor impeller made of aluminum alloy casting for turbocharger having excellent heat resistant strength
EP2036993A1 (en) * 2006-06-29 2009-03-18 Hitachi Metals Precision, Ltd. Casting aluminum alloy, cast compressor impeller comprising the alloy, and process for producing the same
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US8292589B2 (en) 2006-06-29 2012-10-23 Hitachi Metals Precision, Ltd. Casting aluminum alloy, cast compressor impeller comprising the alloy, and process for producing the same
KR100840385B1 (en) * 2006-07-20 2008-06-23 성훈엔지니어링(주) Heat resisting aluminum alloy
JP2009024217A (en) * 2007-07-19 2009-02-05 Hitachi Metals Ltd Aluminum die-casting alloy, cast compressor impeller made of the alloy, and manufacturing method of impeller
CN103469037A (en) * 2013-08-28 2013-12-25 中南大学 Aluminum alloy with high heat stability and fatigue resistance and heat treatment technology
CN105283568A (en) * 2013-12-13 2016-01-27 力拓加铝国际有限公司 Aluminum casting alloy with improved high-temperature performance
WO2015085433A1 (en) * 2013-12-13 2015-06-18 Rio Tinto Alcan International Limited Aluminum casting alloy with improved high-temperature performance
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US20160319400A1 (en) * 2013-12-13 2016-11-03 Rio Tinto Alcan International Limited Aluminum Casting Alloy with Improved High-Temperature Performance
JP2017503086A (en) * 2013-12-13 2017-01-26 リオ ティント アルカン インターナショナル リミテッドRio Tinto Alcan International Limited Aluminum casting alloy with improved high temperature performance
DE112016003841T5 (en) 2015-08-25 2018-05-17 Uacj Corporation Extruded aluminum alloy material and manufacturing method therefor
JP2017214655A (en) * 2016-05-31 2017-12-07 三協立山株式会社 Method for producing 2000 series aluminum alloy, and aluminum alloy
CN109906282A (en) * 2017-02-17 2019-06-18 卓特沃克埃里森塔尔厄德曼有限两合公司 Aluminium alloy, wire rod and connecting element made of aluminium alloy
CN109906282B (en) * 2017-02-17 2021-11-16 卓特沃克埃里森塔尔厄德曼有限两合公司 Aluminum alloy, wire made of aluminum alloy, and connecting element
WO2019167469A1 (en) * 2018-03-01 2019-09-06 本田技研工業株式会社 Al-mg-si system aluminum alloy material
JPWO2019167469A1 (en) * 2018-03-01 2021-01-14 本田技研工業株式会社 Al-Mg-Si based aluminum alloy material

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