JPH07216487A - Aluminum alloy, excellent in wear resistance and heat resistance, and its production - Google Patents
Aluminum alloy, excellent in wear resistance and heat resistance, and its productionInfo
- Publication number
- JPH07216487A JPH07216487A JP6012590A JP1259094A JPH07216487A JP H07216487 A JPH07216487 A JP H07216487A JP 6012590 A JP6012590 A JP 6012590A JP 1259094 A JP1259094 A JP 1259094A JP H07216487 A JPH07216487 A JP H07216487A
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- JP
- Japan
- Prior art keywords
- aluminum alloy
- alloy
- heat resistance
- wear resistance
- resistance
- 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.)
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Abstract
Description
【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、エンジン部品等の機械部品用材
料として１５０℃以上の高温雰囲気の下でかつ高圧摺動
状態において使用される耐摩耗性、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。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention is used in a transportation field such as an automobile, a railroad vehicle, and a ship, as a material for mechanical parts such as engine parts under a high temperature atmosphere of 150 ° C. or higher and under a high pressure sliding condition. The present invention relates to an wrought aluminum alloy having excellent wear resistance and heat resistance, and a method for producing the same.
【０００２】[0002]
【従来の技術】耐摩耗性に優れた展伸用アルミニウム合
金としては、４０３２合金が良く知られているが、耐熱
性に劣るという問題がある。一方、耐熱性に優れた展伸
用アルミニウム合金としては、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高温
強度の点で必ずしも十分な特性を備えておらず、また耐
摩耗性に劣るという問題があった。耐熱性の改善に関し
ては特開平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が、耐摩耗性については考慮され
ていない。2. Description of the Related Art As an wrought aluminum alloy having excellent wear resistance, 4032 alloy is well known, but it has a problem of poor heat resistance. On the other hand, as the wrought aluminum alloy having excellent heat resistance, 2218 alloy and 2219 are used.
Alloy 2618 alloy is well known. However, these alloys do not necessarily have sufficient characteristics in terms of high temperature strength at a use temperature of 150 ° C. or higher, and have a problem of poor wear resistance. Regarding the improvement of heat resistance, an Al—Cu—Mg-based aluminum alloy excellent in heat resistance as disclosed in JP-A-1-290741 is proposed, but no consideration is given to wear resistance. .
【０００３】[0003]
【発明が解決しようとする課題】本発明は、１５０℃以
上の高温雰囲気の下でかつ高圧摺動状態において使用さ
れる耐摩耗性ならびに耐熱性に優れたアルミニウム合金
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。DISCLOSURE OF THE INVENTION The present invention provides an aluminum alloy having excellent wear resistance and heat resistance, which is used under a high temperature atmosphere of 150 ° C. or higher and under a high pressure sliding condition, and a method for producing the same. It is intended for.
【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種々実験検討を重ねた結果、耐摩耗
性に優れるＡｌ−Ｓｉ系合金をベースに、Ｃｕ系析出物
による析出強化能を高めるために、特にＣｕ量を増大さ
せ、かつ複数の遷移金属元素を共存させることによっ
て、耐摩耗性ならびに耐熱性を兼ね備えるアルミニウム
合金を得るに至った。本発明の第１は、 Ｓｉ：１０．０ 〜 １４．０％ Ｃｕ： ３．０ 〜 ６．０％ Ｍｇ： ０．１ 〜 １．０％ Ｆｅ： ０．６ 〜 １．８％ Ｎｉ： ０．８ 〜 ３．０％ Ｍｎ： ０．１ 〜 ０．７％ Ｔｉ： ０．１ 〜 ０．７％ Ｚｒ： ０．０５ 〜 ０．３％ Ｖ ： ０．０５ 〜 ０．５％ を含有し、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。本発明の第２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１６０〜２００℃で１０〜３０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 inventors of the present invention have conducted various experiments to solve the above-mentioned problems, and as a result, based on an Al--Si alloy excellent in wear resistance, a Cu-based precipitate is used. In order to improve the precipitation strengthening ability, an aluminum alloy having both wear resistance and heat resistance has been obtained by increasing the amount of Cu and coexisting with a plurality of transition metal elements. The first of the present invention is: Si: 10.0 to 14.0% Cu: 3.0 to 6.0% Mg: 0.1 to 1.0% Fe: 0.6 to 1.8% Ni: 0 0.8-3.0% Mn: 0.1-0.7% Ti: 0.1-0.7% Zr: 0.05-0.3% V: 0.05-0.5% is contained. The balance consists of Al and unavoidable impurities. A second aspect of the present invention is to manufacture an aluminum alloy having the above-mentioned composition by casting and processing by a conventional method, subjecting it to solution treatment, and then subjecting it to aging treatment at 160 to 200 ° C. for 10 to 30 hours. Characterize.
【０００５】[0005]
【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。 Ｓｉ：Ｓｉは、Ａｌ母相中にＳｉ相として晶出すること
によって耐摩耗性向上に寄与するとともに、ヤング率の
向上および熱膨張率の低下に効果がある。Ｓｉの含有量
は、重量％で１０．０〜１４．０％とした。Ｓｉ量が１
０．０％未満では、十分な耐摩耗性が得られず、また１
４．０％超に過剰に含有すると、粗大な初晶Ｓｉが形成
され、加工性を低下させてしまう。好ましい成分範囲
は、１１．０〜１３．０％である。Next, the reason for limiting the component composition range of the aluminum alloy in the present invention will be explained. Si: Si contributes to the improvement of wear resistance by crystallizing as a Si phase in the Al mother phase, and is effective in improving the Young's modulus and decreasing the thermal expansion coefficient. The Si content was 10.0 to 14.0% by weight. Si amount is 1
If it is less than 0.0%, sufficient wear resistance cannot be obtained, and 1
If it is contained in excess of 4.0%, coarse primary crystal Si is formed and the workability is deteriorated. A preferred component range is 11.0 to 13.0%.
【０００６】Ｃｕ，Ｍｇ：Ｃｕ，Ｍｇを共存させること
によって、Ａｌ2 Ｃｕ，Ａｌ2 ＣｕＭｇ等を析出させ、
その析出強化によって高温強度を向上させる。それぞれ
の元素の含有量は、重量％でＣｕ：３．０〜６．０％，
Ｍｇ：０．１〜１．０％とした。Ｃｕ量が３．０％未
満、Ｍｇ量が０．１％未満では１５０℃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
６．０％超に過剰に含有しても、強度向上効果は飽和す
る。またＭｇ量が１．０％超に過剰に含有されると加工
性が低下する傾向にある。好ましい成分範囲は、Ｃｕ：
３．５〜５．０％、Ｍｇ：０．３〜０．８％である。Cu, Mg: By coexisting Cu and Mg, Al 2 Cu, Al 2 CuMg, etc. are deposited,
The precipitation strengthening improves the high temperature strength. The content of each element is Cu: 3.0 to 6.0% by weight,
Mg: 0.1 to 1.0%. When the Cu content is less than 3.0% and the Mg content is less than 0.1%, the strength required at a high temperature of 150 ° C. or higher cannot be obtained. On the other hand, even if the Cu content exceeds 6.0% in excess, the strength improving effect is saturated. Further, if the Mg content exceeds 1.0% in an excessive amount, the workability tends to decrease. The preferred component range is Cu:
It is 3.5 to 5.0% and Mg: 0.3 to 0.8%.
【０００７】Ｆｅ，Ｎｉ：Ｆｅ，ＮｉはいずれもＡｌと
の間に金属間化合物を分散・形成し、合金の高温強度向
上に寄与する。ＦｅとＮｉの含有量としては、Ｆｅ：
０．６〜１．８％、Ｎｉ：０．５〜３．０％とした。こ
の金属間化合物粒子による分散強化は、Ｆｅ量が０．６
％未満、Ｎｉ量が０．５％未満ではその効果に乏しく、
一方Ｆｅ量が１．８％超、Ｎｉ量が３．０％超では、粗
大な金属間化合物を形成して、かえって強度を低下させ
てしまう。好ましい成分範囲は、Ｆｅ：１．０〜１．８
％、Ｎｉ：２．０〜３．０％である。Fe, Ni: Fe and Ni both disperse and form an intermetallic compound between Al and Al and contribute to the improvement of the high temperature strength of the alloy. The contents of Fe and Ni are Fe:
It was set to 0.6 to 1.8% and Ni: 0.5 to 3.0%. Dispersion strengthening by the particles of the intermetallic compound results in an Fe content of 0.6.
%, And the amount of Ni is less than 0.5%, the effect is poor,
On the other hand, if the Fe content exceeds 1.8% and the Ni content exceeds 3.0%, a coarse intermetallic compound is formed and the strength is rather reduced. A preferable component range is Fe: 1.0 to 1.8.
%, Ni: 2.0 to 3.0%.
【０００８】Ｍｎ，Ｔｉ，Ｚｒ，Ｖ：Ｍｎ，Ｔｉ，Ｚ
ｒ，Ｖ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。それぞれの元素の含有量は、Ｍ
ｎ：０．１〜０．７％、Ｔｉ：０．１〜０．７％、Ｚ
ｒ：０．０５〜０．３％、Ｖ：０．０５〜０．５％とし
た。Ｍｎ量が０．１％未満、Ｔｉ量が０．１％未満、Ｚ
ｒ量が０．０５％未満、Ｖ量が０．０５％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、Ｍｎ量が
０．７％超、Ｔｉ量が０．７％超、Ｚｒ量が０．３％
超、Ｖ量０．５％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、Ｍｎ：０．３〜０．７
％、Ｔｉ：０．４〜０．７％、Ｚｒ：０．１５〜０．３
％、Ｖ：０．２〜０．５％である。Mn, Ti, Zr, V: Mn, Ti, Z
r and V both form an intermetallic compound with Al and contribute to the refinement of crystal grains, and in particular Zr and V
Suppresses recovery and recrystallization from normal temperature to high temperature range to prevent the strength from decreasing. The content of each element is M
n: 0.1 to 0.7%, Ti: 0.1 to 0.7%, Z
r: 0.05-0.3%, V: 0.05-0.5%. Mn amount less than 0.1%, Ti amount less than 0.1%, Z
If the r content is less than 0.05% and the V content is less than 0.05%, the above effect cannot be sufficiently obtained. However, the Mn content exceeds 0.7%, the Ti content exceeds 0.7%, and the Zr content is 0.3%.
If the content of V is more than 0.5%, a coarse intermetallic compound is formed with Al, and the workability and mechanical properties are impaired. A preferable component range is Mn: 0.3 to 0.7.
%, Ti: 0.4 to 0.7%, Zr: 0.15 to 0.3
%, V: 0.2 to 0.5%.
【０００９】本発明のアルミニウム合金は、従来のＡｌ
−Ｓｉ系合金の製造方法に準じて製造できる。しかし、
耐熱性という点において、特にＣｕ，Ｍｇによる析出強
化、ＡｌとＦｅおよびＡｌとＮｉとの間での金属間化合
物形成による分散強化、さらにＭｎ，Ｔｉ，Ｚｒ，Ｖの
回復・再結晶抑制効果を有効に活用するためには、溶体
化処理を固相線温度−５℃〜固相線温度−２５℃の温度
範囲で施し、次いで１６０〜２００℃で１０〜３０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ために規定す
る。The aluminum alloy of the present invention is a conventional Al alloy.
It can be manufactured according to the method of manufacturing a Si-based alloy. But,
In terms of heat resistance, precipitation strengthening by Cu and Mg, dispersion strengthening by formation of intermetallic compounds between Al and Fe and Al and Ni, and Mn, Ti, Zr, and V recovery and recrystallization suppressing effects In order to effectively utilize it, it is preferable to perform solution treatment in a temperature range of solidus temperature −5 ° C. to solidus temperature −25 ° C., and then perform aging treatment at 160 to 200 ° C. for 10 to 30 hours. desirable. 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 defined because if the amount exceeds the upper limit, the formed intermetallic compound becomes coarse and it becomes difficult to obtain the strengthening effect.
【００１０】[0010]
実施例１ 本発明の成分組成範囲内にある２７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、５２０℃、４
時間の均質化焼鈍を施し、鍛造により直径１６ｍｍの丸
棒に加工した。次いで５４０℃の溶体化処理後、１８０
℃、２０時間の時効処理を行った。得られた丸棒より摩
耗試験および高温引張試験用の試験片を作製した。摩耗
試験は平板／回転円筒型試験法により、平板状試験片を
回転する円筒形状の相手材Ｓ５０Ｃに荷重２ｋｇの負荷
をかけて接触させて、摩擦距離を６００ｍとして行っ
た。なお摩擦速度は１および２ｍ／ｓとした。摩耗の評
価は摩耗体積を荷重および摩擦距離で除した値である比
摩耗量を用いて行った。また高温引張試験では、室温お
よび１５０℃における機械的性質（耐力）を調査した。
なお比較例として従来材の４０３２合金（比較例１）、
２２１９合金（比較例２）、２６１８合金（比較例３）
の試験片も準備した。Example 1 After casting 27 kinds of alloys (the chemical compositions of which are shown in Table 1) within the compositional range of the present invention, 520 ° C., 4
After homogenizing annealing for a period of time, it was forged into a round bar having a diameter of 16 mm. Then, after solution treatment at 540 ° C., 180
Aging treatment was performed at 20 ° C. for 20 hours. Test pieces for wear test and high temperature tensile test were prepared from the obtained round bar. The wear test was carried out by a flat plate / rotating cylinder type test method, in which a flat plate-shaped test piece was brought into contact with a rotating cylindrical mating member S50C under a load of 2 kg to make the friction distance 600 m. The friction speed was 1 and 2 m / s. The wear was evaluated using the specific wear amount, which is a value obtained by dividing the wear volume by the load and the friction distance. In the high temperature tensile test, the mechanical properties (proof stress) at room temperature and 150 ° C were investigated.
As a comparative example, a conventional material 4032 alloy (Comparative Example 1),
2219 alloy (Comparative example 2), 2618 alloy (Comparative example 3)
I prepared the test piece.
【００１１】[0011]
【表１】 [Table 1]
【００１２】表２の調査結果から明かなように、本発明
の合金は、従来の耐摩耗性合金と同等以上の耐摩耗性を
備え、ならびに１５０℃において従来の耐熱合金を上回
る３３０Ｎ／ｍｍ2 以上の優れた高温強度特性を有して
いることがわかる。As is clear from the results of the investigation in Table 2, the alloy of the present invention has a wear resistance equal to or higher than that of the conventional wear-resistant alloy, and 330 N / mm 2 at 150 ° C., which is higher than that of the conventional heat-resistant alloy. It can be seen that it has the excellent high-temperature strength characteristics described above.
【００１３】[0013]
【表２】 [Table 2]
【００１４】実施例２ 表１に示される成分組成の合金を用い、５４０℃で溶体
化処理を施した後に、時効処理条件を変化させて耐熱性
に及ぼす影響を調査した。時効処理条件および耐熱性の
評価結果を表３に示す。同表より、本発明の製造条件範
囲内であれば、優れた耐熱性が得られることがわかる。Example 2 Using alloys having the component compositions shown in Table 1, after subjecting to solution treatment at 540 ° C., the effect on heat resistance was investigated by changing the aging treatment conditions. Table 3 shows the aging treatment conditions and the evaluation results of heat resistance. From the table, it can be seen that excellent heat resistance can be obtained within the manufacturing condition range of the present invention.
【００１５】[0015]
【表３】 [Table 3]
【００１６】[0016]
【発明の効果】本発明アルミニウム合金は、Ｓｉにより
耐摩耗性を付与するとともに、Ｃｕ，Ｍｇの析出強化元
素を含有し、さらにＦｅ，Ｎｉの高温強度向上に寄与す
る元素、並びに高温での回復・再結晶抑制効果を有する
Ｍｎ，Ｔｉ，Ｚｒ，Ｖを共存させることを特徴とするも
のであり、耐摩耗性に優れ、かつ１５０℃の高温におい
て長時間保持しても、３３０Ｎ／ｍｍ2 以上の耐力を発
揮する。したがって自動車用エンジン部品をはじめとす
る高温環境下でかつ高圧摺動状態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 not only imparts wear resistance by Si, contains Cu and Mg precipitation strengthening elements, and further contributes to improvement of high temperature strength of Fe and Ni, and recovery at high temperature. -Mn, Ti, Zr, and V, which have the effect of suppressing recrystallization, are made to coexist, and are excellent in wear resistance and 330 N / mm 2 or more even when kept at a high temperature of 150 ° C for a long time. Exert the proof of. Therefore, it can be a very suitable material for machine parts such as automobile engine parts used in a high-pressure environment and under high-pressure sliding condition.
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【手続補正書】[Procedure amendment]
【提出日】平成６年７月２１日[Submission date] July 21, 1994
【手続補正１】[Procedure Amendment 1]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００１１[Correction target item name] 0011
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００１１】[0011]
【表１】 [Table 1]
Claims (2)
耗性、耐熱性に優れたアルミニウム合金。1. By weight%, Si: 10.0 to 14.0% Cu: 3.0 to 6.0% Mg: 0.1 to 1.0% Fe: 0.6 to 1.8% Ni : 0.8 to 3.0% Mn: 0.1 to 0.7% Ti: 0.1 to 0.7% Zr: 0.05 to 0.3% V: 0.05 to 0.5% An aluminum alloy that contains Al, and the balance is Al and unavoidable impurities, and has excellent wear resistance and heat resistance.
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１６０〜２００℃で１０〜３０時間の
時効処理を施すことを特徴とする耐摩耗性、耐熱性に優
れたアルミニウム合金の製造方法。2. By weight%, Si: 10.0 to 14.0% Cu: 3.0 to 6.0% Mg: 0.1 to 1.0% Fe: 0.6 to 1.8% Ni : 0.8 to 3.0% Mn: 0.1 to 0.7% Ti: 0.1 to 0.7% Zr: 0.05 to 0.3% V: 0.05 to 0.5% Abrasion resistance characterized in that an aluminum alloy containing Al and unavoidable impurities in the balance is cast and processed by a conventional method, solution treatment is applied, and then aging treatment is performed at 160 to 200 ° C. for 10 to 30 hours. Of aluminum alloy having excellent heat resistance and heat resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6012590A JPH07216487A (en) | 1994-02-04 | 1994-02-04 | Aluminum alloy, excellent in wear resistance and heat resistance, and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6012590A JPH07216487A (en) | 1994-02-04 | 1994-02-04 | Aluminum alloy, excellent in wear resistance and heat resistance, and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07216487A true JPH07216487A (en) | 1995-08-15 |
Family
ID=11809572
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6012590A Withdrawn JPH07216487A (en) | 1994-02-04 | 1994-02-04 | Aluminum alloy, excellent in wear resistance and heat resistance, and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07216487A (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6669792B2 (en) * | 1998-09-08 | 2003-12-30 | The United States Of America As Represented By The Administrator Of The National Aeronautics And Space Administration | Process for producing a cast article from a hypereutectic aluminum-silicon alloy |
| EP1975262A3 (en) * | 2007-03-30 | 2010-09-15 | Kabushiki Kaisha Toyota Chuo Kenkyusho | Aluminum alloys for casting, aluminum alloy castings and process for producing aluminum alloy castings |
| WO2013050355A1 (en) * | 2011-10-04 | 2013-04-11 | Federal-Mogul Nürnberg GmbH | Method for producing an engine component and engine component |
| WO2014076174A1 (en) * | 2012-11-14 | 2014-05-22 | Federal-Mogul Nürnberg GmbH | Method for producing an engine component, engine component, and use of an aluminium alloy |
| CN105506409A (en) * | 2015-12-28 | 2016-04-20 | 常熟市明瑞针纺织有限公司 | High-wear-resistant cam of warp knitting machine |
| CN107532244A (en) * | 2015-04-01 | 2018-01-02 | 菲特尔莫古纽伦堡有限公司 | Cast aluminium alloy, the method for manufacturing engine components, engine components and use cast aluminium alloy gold manufacture engine components |
| CN114318089A (en) * | 2022-01-05 | 2022-04-12 | 成都阳光铝制品有限公司 | Aluminum alloy for manufacturing automobile parts and preparation method thereof |
-
1994
- 1994-02-04 JP JP6012590A patent/JPH07216487A/en not_active Withdrawn
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6669792B2 (en) * | 1998-09-08 | 2003-12-30 | The United States Of America As Represented By The Administrator Of The National Aeronautics And Space Administration | Process for producing a cast article from a hypereutectic aluminum-silicon alloy |
| EP1975262A3 (en) * | 2007-03-30 | 2010-09-15 | Kabushiki Kaisha Toyota Chuo Kenkyusho | Aluminum alloys for casting, aluminum alloy castings and process for producing aluminum alloy castings |
| WO2013050355A1 (en) * | 2011-10-04 | 2013-04-11 | Federal-Mogul Nürnberg GmbH | Method for producing an engine component and engine component |
| WO2014076174A1 (en) * | 2012-11-14 | 2014-05-22 | Federal-Mogul Nürnberg GmbH | Method for producing an engine component, engine component, and use of an aluminium alloy |
| JP2016505382A (en) * | 2012-11-14 | 2016-02-25 | フェデラル−モーグル ニュルンベルグ ゲゼルシャフト ミット ベシュレンクテル ハフツング | Method for manufacturing engine components, use of engine components and aluminum alloys |
| US10022788B2 (en) | 2012-11-14 | 2018-07-17 | Federal-Mogul Nurnberg Gmbh | Method for producing an engine component, engine component, and use of an aluminium alloy |
| JP2018114556A (en) * | 2012-11-14 | 2018-07-26 | フェデラル−モーグル ニュルンベルグ ゲゼルシャフト ミット ベシュレンクテル ハフツング | Method for manufacturing engine component, engine component, and use of aluminium alloy |
| CN107532244A (en) * | 2015-04-01 | 2018-01-02 | 菲特尔莫古纽伦堡有限公司 | Cast aluminium alloy, the method for manufacturing engine components, engine components and use cast aluminium alloy gold manufacture engine components |
| CN105506409A (en) * | 2015-12-28 | 2016-04-20 | 常熟市明瑞针纺织有限公司 | High-wear-resistant cam of warp knitting machine |
| CN114318089A (en) * | 2022-01-05 | 2022-04-12 | 成都阳光铝制品有限公司 | Aluminum alloy for manufacturing automobile parts and preparation method thereof |
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