EP0137180B1 - Hitzebeständige Aluminiumlegierung - Google Patents

Hitzebeständige Aluminiumlegierung Download PDF

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Publication number
EP0137180B1
EP0137180B1 EP19840109194 EP84109194A EP0137180B1 EP 0137180 B1 EP0137180 B1 EP 0137180B1 EP 19840109194 EP19840109194 EP 19840109194 EP 84109194 A EP84109194 A EP 84109194A EP 0137180 B1 EP0137180 B1 EP 0137180B1
Authority
EP
European Patent Office
Prior art keywords
powder particles
weight
heat
parent metal
aluminium alloy
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.)
Expired
Application number
EP19840109194
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English (en)
French (fr)
Other versions
EP0137180A1 (de
Inventor
Masahiko Shioda
Syunsuke Suzuki
Akira Matsuyama
Yoshishiro Maki
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.)
Nissan Motor Co Ltd
Original Assignee
Nissan Motor Co Ltd
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 Nissan Motor Co Ltd filed Critical Nissan Motor Co Ltd
Publication of EP0137180A1 publication Critical patent/EP0137180A1/de
Application granted granted Critical
Publication of EP0137180B1 publication Critical patent/EP0137180B1/de
Expired legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium

Definitions

  • This invention relates, in general, to a heat-resisting aluminum alloy which is high in mechanical strength not only at ordinary temperatures but also at high temperatures, and more particularly to the heat-resisting aluminum alloy suitable for the material of automotive engine component parts subjected to ordinary to high temperatures.
  • so-called high strength aluminum alloy such as one whose designation number is 7075 has a good strength characteristics at normal temperatures but is sharply lowered in strength in a temperature range from normal temperatures to 200°C.
  • high strength aluminum alloy is not suitable for the material of the component parts of automotive engines.
  • the designation numbers of aluminium alloys mentioned hereinabove and hereinafter are adopted by the Aluminium Association in the United States of America.
  • heat-resisting aluminium alloys such as one whose designation number is 2218, it is excellent in strength at high temperatures but is lower in strength at normal temperatures. As a result, such a heat-resisting aluminium alloy is also not suitable for the material of automotive engine component parts.
  • Heat-resistant aluminium alloys comprising 2.2 to 6% manganese are disclosed in FR-A-1 370 542. These conventional heat-resistant aluminium alloys are based on the finding that aluminium-manganese alloys comprising 4% manganese up to 4% iron and up to 0.02% titanium can be processed by casting and have high mechanical strengths at temperatures of around 650°C.
  • a typical alloy of this type having excellent mechanical properties at temperatures of higherthan 650°C consists of 3 to 9% manganese, 2.5 to 12% iron, 0.001 to 2.5% titanium, the balance being aluminium and impurities such as copper, zinc and magnesium.
  • the above object is achieved by heat-resisting aluminium alloy consisting of more than 6 to 8% by weight manganese, from 0.5 to 2% by weight iron, from 0.03 to .05% by weight zirconium, from 2 to 5% by weight copper, the balance being aluminium and incidental impurities.
  • the aluminum alloy becomes high both in strength at ordinary and high temperatures and becomes suitable for the material of an article produced by using so-called atomization process in which molten metal of the parent metal is sprayed to obtain powder particles which will be finally compression-formed into a desired article.
  • the upper limit of the added amount or content of manganese (Mn) and iron (Fe) is kept lower thereby to suppress crystallization of bulky phase and segregation of Mn compound, while increasing the added amount of content of copper (Cu) which is an additive element for improving mechanical strength throughout a wide temperature range from ordinary temperatures to about 250°C without affecting Mn compound.
  • Cu copper
  • Mn more than 6 to 8% by weight (excluding a content of 6.0%).
  • Mn is an element effective for improving heat resistance and wear resistance of aluminium alloy.
  • the content of Mn is 6% or less, sufficient heat resistance cannot be obtained, while if it exceeds 8%, there occurs crystallization of the bulky phase and segregation of Mn compound at the cooling rate obtained by the atomization process. As a result, the content of Mn has been limited within the range from more than 6 to 8% by weight.
  • Fe 0.5 to 2% by weight.
  • Fe is an element effective for improving high temperature stability of supersaturated solid solution (obtained by quenching) of AI-Mn alloy and fine Al-Mn intermetallic compound.
  • the content of Fe is less than 0.5%, such an effect cannot be obtained, while if it exceeds 2%, brittle phase of AI-Mn-Fe and Al-Fe is crystallized in the atomization process.
  • the content of Fe has been limited within the range from 0.5 to 2% by weight.
  • Zr 0.03 to 0.5% by weight.
  • Zr is an element effective for making fine crystal particles in addition for improving high temperature stability of supersaturated solid solution of Al-Mn alloy and fine Al-Mn intermetallic compound.
  • the content of Zr is less than 0.03%, such an effect cannot be obtained, while if it exceeds 0.5%, there occurs enlargement of AI-Zr phase. As a result, the content of Zr has been limited within the range from 0.03 to 0.5% by weight.
  • Cu 2 to 5% by weight.
  • Cu is an element which is effective for improving mechanical strength at ordinary temperatures and by which the heat-resisting aluminum alloy according to the present invention is most characterized.
  • the present invention is intended to improve the mechanical strength in a wide temperature range from ordinary temperatures to 250°C without affecting Mn compound, by increasing the content of Cu in order to compensate a decrease of Mn, Fe content which decrease is made for the purpose of suppressing coarsening and segregation of Mn compound in powder form produced by the atomization process.
  • the content of Cu is less than 2%, the effect of strength improvement cannot be expected, while if it exceeds 5%, corrosion resistance of the aluminum alloy is degraded, accompanied by deteriorating the high temperature stability of the supersaturated solid solution of AI-Mn alloy and very fine Al-Mn intermetallic compound. As a result, the content of Cu has been limited within the range from 2 to 5% by weight.
  • Si silicon
  • Mg magnesium
  • Mg is an element which improves mechanical strength at ordinary temperatures by age hardening upon binding of Mg with Si.
  • Si tends to take the form a-AI(Fe, Mn)Si phase and therefore strength improvement due to the precipitation of M 92 Si phase is degraded as compared with that due Cu addition.
  • the aluminum alloys of Sample Nos fto 5 and of Sample Nos. 8 to 12 were prepared as follows: A binary alloy ingot containing A1 and an individual component other than Al, and an AI ingot were weighed and molten to be mixed with each other thereby to produce a parent metal having a chemical composition shown in table 1. Thereafter, the patent metal was molten in a melting furnace of an atomizing device, and the thus prepared molten metal was sprayed upon being superheated 150°C over the melting point of the parent metal, thereby obtaining atomized powder.
  • the atomized powder having a particle size not larger than 120 mesh was used for preparing a specimen subjected to tests discussed below.
  • the atomized powder was formed into a cylindrical shape under the compression of 3.5 KN/cm 2 to obtain a billet.
  • the billet was then subjected to an extrusion process at a temperature lower than 400°C and at an extrusion ratio (the ratio between the cross-sectional areas of the billet and an extruded product) of 12:1.
  • the extruded product was cut out into a predetermined shape to obtain the specimen for the tests.
  • the Sample Nos. 6 and 7 correspond to aluminum alloys whose designation numbers are 2218 and 7075, respectively. These were prepared as follows: The molten metal of the parent metal corresponding to each Sample No. was formed into an ingot for rolling which ingot thereafter underwent hot rolling. Subsequently, a product corresponding to Sample No. 6 was subjected to solid solution treatment at 510°C for 4 hours and to artificial aging treatment at 175°C for 4 hours, whereas a product corresponding to Sample No. 7 was subjected to solid solution treatment at 460°C for 4 hours and to artificial aging treatment at 120°C for 24 hours. Thereafter, each product were cut out into the predetermined shape to obtain each specimen for the tests.
  • the Sample Nos 8 and 9 aluminum alloys (Comparative Examples) whose Mn and Fe contents are less than those of the aluminum alloy of the present invention are slightly lower in strength at 200°C as compared with the aluminum alloy of the present invention.
  • the Sample Nos. 10, 11 and 12 aluminum alloys (Comparative Examples) whose Mn and Fe contents are more than those of the aluminum alloy of the present invention are degraded in strength as compared with the aluminum alloy of the present invention because coarsening and segregation of Mn compound unavoidably occurs at the cooling rate obtained by the atomization process.
  • the Sample Nos. 8 to 12 aluminum alloys have been confirmed to be inferior as compared with the aluminum alloy according to the present invention.
  • the aluminum alloy according to the present invention is a light alloy material which is excellent in mechanical strength both at ordinary temperatures and at high temperatures as compared with conventional aluminum alloys, so that it is widely applicable, for example, engine component parts which are required not only to be heat-resistant but also to be high in ordinary temperature strength, while achieving weight reduction of the component parts and an assembled product.
  • an article made of the aluminum alloy of the present invention can be produced with powder particles prepared by the atomization process, thus offering an advantage of omitting quench solidification such as troublesome splat cooling process.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Powder Metallurgy (AREA)

Claims (8)

1. Wärmebeständige Aluminiumlegierung, bestehend aus mehr als 6 bis 8 Gew.-% Mangan, aus 0,5 bis 2 Gew.-% Eisen, aus 0,03 bis 0,5 Gew.% Zirconium, aus 2 bis 5 Gew.-% Kupfer, wobei der Rest Aluminium und zufällige Verunreinigungen sind.
2. Verwendung der Aluminiumlegierung nach Anspruch 1 zur Herstellung eines Komponententeils eines Kraftfahrzeugmotors.
3. Verfahren zur Herstellung eines Gegenstands mit verbesserter Festigkeit bei Temperaturen im Bereich von üblicher Temperature bis 250°C, bei dem ein Ausgangsmetall mit einer Zusammensetzung gemäß Anspruch 1 hergestellt wird, das Ausgangsmetall zur Herstellung einer Schmelze des. Ausgangsmetalls geschmolzen wird, die Schmelze zur Herstellung von Zerstäubten Pulverteilchen gesprüht wrid und die Pulverteilchen zu einer vorbestimmten Form geformt werden.
4. Verfahren nach Anspruch 3, worin die Sprühstufe in einem Zustand durchgeführt wird, wo die Schmelze 150°C über dem Schmelzpunkt des Ausgangsmetalls superwarmt wird.
5. Verfahren nach Anspruch 4, das weiterhin eine Stufe einschließt, bei der Pulverteilchen mit Teilchengrößen von weniger als weniger 125 um (120 mesh) nach der Sprühstufe ausgewählt werden.
6. Verfahren nach Anspruch 5, worin die Formungsstufe durchgeführt wird, indem die Pulverteilchen unter Druck von etwa 343 N/mm2 (3,5 t/cm2) komprimiert werden.
7. Verfahren nach Anspruch 6, das weiterhin eine Stufe einschließt, bei der die gebildeten Pulverteilchen in eine vorbestimmte Form nach der Formungsstufe extrudiert werden.
8. Verfahren nach Anspruch 7, worin die Extrusionsstufe bei einer Temperatur von weniger als 400°C durchgeführt wird.
EP19840109194 1983-08-17 1984-08-02 Hitzebeständige Aluminiumlegierung Expired EP0137180B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP14916183A JPS6043453A (ja) 1983-08-17 1983-08-17 耐熱アルミニウム合金
JP149161/83 1983-08-17

Publications (2)

Publication Number Publication Date
EP0137180A1 EP0137180A1 (de) 1985-04-17
EP0137180B1 true EP0137180B1 (de) 1988-12-28

Family

ID=15469120

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19840109194 Expired EP0137180B1 (de) 1983-08-17 1984-08-02 Hitzebeständige Aluminiumlegierung

Country Status (3)

Country Link
EP (1) EP0137180B1 (de)
JP (1) JPS6043453A (de)
DE (1) DE3475798D1 (de)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE3533233A1 (de) * 1985-09-18 1987-03-19 Vaw Ver Aluminium Werke Ag Hochwarmfeste aluminiumlegierung und verfahren zu ihrer herstellung
JPH04187701A (ja) * 1990-11-20 1992-07-06 Honda Motor Co Ltd 粉末冶金用アルミニウム合金粉末、圧粉体および焼結体
JP3725279B2 (ja) 1997-02-20 2005-12-07 Ｙｋｋ株式会社 高強度、高延性アルミニウム合金
KR100415400B1 (ko) * 2001-04-26 2004-01-16 학교법인연세대학교 자발적 파괴에 의한 Ａｌ기 준결정상 합금분말의 제조방법

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB498227A (en) * 1937-06-04 1939-01-04 Hubert Sutton Improvements in or relating to aluminium alloys
US3462248A (en) * 1956-12-14 1969-08-19 Kaiser Aluminium Chem Corp Metallurgy
US2966731A (en) * 1958-03-27 1961-01-03 Aluminum Co Of America Aluminum base alloy powder product
US3265493A (en) * 1963-05-31 1966-08-09 Dow Chemical Co Aluminum base pellet alloys containing copper and magnesium and process for producing the same
BE637348A (de) * 1963-10-09

Also Published As

Publication number Publication date
EP0137180A1 (de) 1985-04-17
DE3475798D1 (en) 1989-02-02
JPS6157380B2 (de) 1986-12-06
JPS6043453A (ja) 1985-03-08

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