EP0539172B1 - Alliage d'aluminium - Google Patents

Alliage d'aluminium Download PDF

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Publication number
EP0539172B1
EP0539172B1 EP92309591A EP92309591A EP0539172B1 EP 0539172 B1 EP0539172 B1 EP 0539172B1 EP 92309591 A EP92309591 A EP 92309591A EP 92309591 A EP92309591 A EP 92309591A EP 0539172 B1 EP0539172 B1 EP 0539172B1
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EP
European Patent Office
Prior art keywords
aluminum alloy
tensile strength
wear resistance
matrix
dispersed
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 - Lifetime
Application number
EP92309591A
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German (de)
English (en)
Other versions
EP0539172A1 (fr
Inventor
Kunihiko c/o Toyota Jidosha K.K. Imahashi
Hirohisa c/o Toyota Jidosha K.K. Miura
Yasuhiro c/o Toyota Jidosha K.K. Yamada
Hirohumi c/o Toyota Jidosha K.K. Michioka
Jun c/o Toyo Aluminium K.K. Kusui
Akiei c/o Toyo Aluminium K.K. Tanaka
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.)
Toyo Aluminum KK
Toyota Motor Corp
Original Assignee
Toyo Aluminum KK
Toyota Motor Corp
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Publication date
Priority claimed from JP4280543A external-priority patent/JPH05311302A/ja
Application filed by Toyo Aluminum KK, Toyota Motor Corp filed Critical Toyo Aluminum KK
Publication of EP0539172A1 publication Critical patent/EP0539172A1/fr
Application granted granted Critical
Publication of EP0539172B1 publication Critical patent/EP0539172B1/fr
Anticipated expiration legal-status Critical
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ

Definitions

  • the present invention relates to an aluminum alloy which shows low friction characteristics. It is suitable for use as engine components of automobiles and is excellent in both tensile strength and wear resistance.
  • An aluminum alloy has light weight and excellent processability. So it has been conventionally used as structural materials of air planes and automobiles. Recently, an engine of automobiles comes to require high power and low fuel consumption. In accordance with this requirement, the aluminum alloy is being applied for rocker arms, shift forks and engine components such as piston or cylinder head. So, the aluminum alloy is improved in its wear resistance and tensile strength.
  • Al-based composite materials having excellent wear resistance and excellent stiffness include, for example, a high tensile aluminum alloy material. It is produced by powder metallurgy in which particles, whiskers and fibers of SiC or Al 2 O 3 are added into Al-Cu-Mg alloy (2000 series) or Al-Mg-Si alloy (6000 series).
  • a high tensile aluminum alloy powder having excellent tensile strength, excellent wear resistance and low thermal expansion is developed (See Japanese Patent Publication No. 56401/1990).
  • the method for producing the high tensile aluminum alloy powder is that 7.7 to 15% of Ni is added to an Al-Si alloy, then Cu and Mg are added. Concerning the obtained high tensile aluminum alloy powder, the size of primary Si is less than 15 ⁇ m.
  • a skirt portion requires excellent wear resistance, excellent heat conductivity, low thermal expansion and excellent tensile strength.
  • Cylinder liner requires excellent wear resistance, excellent antiseize and low friction coefficient.
  • the above alloy such as 2000 series alloy or 6000 series alloy is used as matrix, and particles, whiskers and fibers of SiC or Al 2 O 3 are added into the matrix, thereby obtaining Al-based Metal Matrix Composites (hereinafter described as MMC). It shows poor tensile strength because the matrix itself shows poor tensile strength.
  • the temperature of a sliding portion rises. So, agglutination abrasion or abrasive friction generates, and friction coefficient becomes high and abrasion loss becomes large. Therefore, to use the Al-based MMC as the sliding member is restricted not only at high temperature but also room temperature.
  • the above high tensile aluminum alloy in which Ni is added into an Al-Si alloy shows excellent tensile strength because stable Al-Ni intermetallic compounds are formed.
  • the high tensile aluminum alloy When the high tensile aluminum alloy is used as a sliding member, it shows poor wear resistance since hard particles such as ceramics are not included. Concerning sliding characteristics, Al is adhered to the mating member because of agglutination.
  • the high tensile aluminum alloy cannot be improved in its friction coefficient, seize load and abrasion loss. Therefore, the high tensile aluminum alloy is used as the sliding member only for the restricted area under the restricted condition.
  • an object of the present invention to provide an aluminum alloy which shows excellent tensile strength and excellent sliding characteristics (i.e. excellent wear resistance and excellent antiseize in spite of low friction).
  • Inventors examined a base composition for the purpose of obtaining tensile strength and wear resistance of the matrix. As the result, we happened to think that wear resistance is obtained by precipitating primary Si crystal within the-range of hyper-eutectic of an Al-Si alloy. Similarly, we also happened to think that tensile strength is obtained by adding Ni and Cu.
  • An aluminum alloy according to the present invention is excellent in its tensile strength and wear resistance.
  • the invention provides an aluminum alloy in accordance with claim 1.
  • the amount of Si is in the range of 10 to 25%.
  • Si is dispersed as primary crystal and eutectic, so tensile strength and wear resistance improve.
  • the amount of Si is less than 10%, the Al-Si alloy is hypo-eutectic, and it has ⁇ phase + eutectic structure. In this case, tensile strength and wear resistance are not expected.
  • the amount of Si is more than 25%, Si particle as primary crystal becomes large even if powder metallurgy is used. In this case, the mating member is attacked, and machinability in producing becomes remarkably bad. Furthermore, elongation of the material is very small, and the crack is produced in processing. So, the aluminum alloy in this case is not suitable for practical use.
  • the amount of Ni is in the range of 5 to 20%.
  • Intermetallic compounds such as Al 3 Ni are formed in the aluminum alloy by using Ni. These intermetallic compounds are stable even at high temperature, and they are useful for tensile strength and wear resistance.
  • the amount of Ni is less than 5%, the intermetallic compounds of Al-Ni is not formed. So, tensile strength and wear resistance cannot be obtained.
  • the amount of Ni is more than 20%, tensile strength and wear resistance are excellent. On the other hand, machinability deteriorates, so the aluminum alloy in this case is not suitable for practical use.
  • the amount of Cu is in the range of 1 to 5%.
  • Cu is useful for improving tensile strength of the aluminum alloy. When the amount of Cu is less than 1%, tensile strength is weak. When the amount of Cu is more than 5%, coarse CuAl 2 particle is produced, so strength is weak.
  • the Al-Si alloy as matrix has hyper-eutectic structure because the amount of Si is 10 to 25%. Fine primary Si crystal is formed, so excellent wear resistance is provided. Since the Al-Si alloy also contains 5 to 20% of Ni, the intermetallic compounds such as Al 3 Ni or Al 3 Ni 2 are formed. Therefore, tensile strength and wear resistance improve. Furthermore, tensile strength improves because 1 to 5% of Cu is added.
  • Figure 7 shows X-ray diffraction result of Al-15Ni-15Si-3Cu, and Al 3 Ni and Al 3 Ni 2 are produced.
  • the amount of aluminium-nitride is in the range of 0.5 to 10%.
  • nitride is dispersed into the matrix, friction coefficient is lowered, and antiseize and wear resistance improve. Furthermore, Al isn't adhered to the mating member, and it can slide easily.
  • the amount of nitride is less than 0.5%, the above-described effect cannot be obtained.
  • the amount of nitride is more than 10%, flexural tensile strength and ductility deteriorate. So, desirable amount of nitride is 0.5 to 10%.
  • the amount of boride is in the range of 0.5 to 10%.
  • B 2 O 3 is produoed by oxidation of B because TiB 2 is thermodynamically unstable.
  • the melting point of B 2 O 3 is 450°C.
  • the part of B 2 O 3 changes to liquid, and finally becomes liquid lubrication. So, friction coefficient of the aluminum alloy is lowered, and antiseize and wear resistance improve.
  • the amount of boride is less than 0.5%, the above-described effect cannot be obtained.
  • the amount of boride is more than 10%, mechanical property such as flexural strength and ductility is remarkably lowered. So, desirable amount of boride is 0.5 to 10%.
  • the above boride includes, for example, TiB 2 , NiB, MgB 2 and ZrB 2 .
  • the dispersant is in a form of powders, whiskers and fibers.
  • the above dispersant is dispersed into the matrix by means of powder metallurgy. At first, the dispersant is mixed within the aluminum alloy powder. Then, the obtained mixed powder is sintered, forged, extruded and rolled. Finally, the mixed powder become solid and compacting is obtained.
  • particle diameter of the dispersant desirable particle diameter is in the range of 0.2 to 20 ⁇ m.
  • the particle diameter is less than 0.2 ⁇ m, the powder is agglomerated, and mechanical characteristics deteriorates.
  • the particle diameter is more than 20 ⁇ m, the particle is cracked or omitted at the time of sliding. Then, abrasive friction occurs, and the effect of wear resistance is weakened.
  • Figure 1 is a cross sectional view of a test piece and a mating member which are used for friction experiment.
  • Figure 2 is a cross sectional view for showing friction experiment.
  • Figure 3 is an EPMA photograph (magnification x 1000) for showing Al distribution on the surface of the mating member when LFW experiment is performed on the example of the present invention in which AlN is dispersed .
  • Figure 4 is an EPMA photograph (magnification x 1000) for showing Al distribution on the surface of the mating member when LFW experiment is performed on the comparative example in which AlN is not dispersed.
  • Figure 5 is a SEM photograph (magnification x 1000) after LFW experiment is performed on the example of the present invention in which AlN is dispersed.
  • Figure 6 is an EPMA photograph (magnification x 1000) for showing N distribution when LFW experiment is performed on the example of the present invention in which AlN is dispersed.
  • Figure 7 shows X-ray diffraction result of Al-15Ni-15Si-3Cu.
  • Figure 8 are optical micrographs (magnification x 100 and 400) for showing the metal structure of the comparative example 9.
  • Figure 9 are optical micrographs (magnification x 100 and 400) for showing the metal structure of the example 1 of the present invention.
  • Figure 10 are optical micrographs (magnification x 100 and 400) for showing the metal structure of the example 2 of the present invention.
  • Figure 11 is a SEM photograph (magnification x 5000) for showing the appearance of the dispersed AlN particle in the preferred embodiments.
  • an alloy containing Al, 15% of Si, 15% of Ni and 3% of Cu was melted and atomized, thereby obtaining an aluminum alloy powder.
  • the aluminum alloy powder was classified by 100 mesh sieve, and -100 mesh powder was obtained.
  • an alloy containing Al, 4.5 % of Cu, 1.6% of Mg and 0.5% of Mn was used, and -100 mesh powder was obtained.
  • an alloy containing Al, 1.0% of Mg, 0.6% of Si and 0.3% of Cu (being equivalent to AA 6061) was used, -100 mesh powder was obtained.
  • the above aluminum alloy powder was mixed with AlN, or boride such as TiB 2 , NiB or MgB 2 , in a grinding machine. Concerning nitride and boride, the adding amount and the average particle diameter were shown in Table 1.
  • the mixed powder was filled within a tube made of pure Al. Then a vacuum degassing was performed, and the tube was sealed. After that, the temperature of the tube was heated to 450°C, and the tube having the mixed powder therein was extruded at extrusion ratio of 10. Finally, the extruded material was mechanically processed. Concerning the extruded material, tensile strength, abrasion loss, friction coefficient and seize load were measured. The results were shown in Table 2.
  • the friction coefficient and seize load were measured by a testing machine as shown in Figure 1.
  • a ring-shaped member 1, JIS SUJ2 was pressed against a box-shaped test piece 2 under the condition that a load was increased by 250(N) and a sliding speed was 13m/min. Then, friction coefficient and seize load were measured under a drying condition.
  • the abrasion loss was measured by LFW testing machine as shown in Figure 2.
  • a ring-shaped member 4, JIS SUJ2 was immersed into oil 3. Then, a box-shaped test piece 5 was pressed against the ring-shaped member 4 under the condition that the load was 150(N) and the sliding speed was 18m/min. After being pressed for 15 minutes, abrasion loss was measured.
  • the composition of the matrix was AA 2024, and SiC was dispersed in more amount than that was needed.
  • the comparative example 10 showed poor tensile strength, and the tensile strength at 200°C was 170MPa. Moreover, the comparative example 10 showed rather high friction coefficient, and the value of friction coefficient was 0.53. According to friction coefficient, the value of seize load was 1000(N). Furthermore, the value of abrasion loss was 45 ⁇ m.
  • the comparative example 10 showed poor tensile strength, poor antiseize, and poor wear resistance.
  • the composition of the matrix was AA 6061, and SiC was dispersed in more amount than that was needed.
  • the comparative example 11 showed poor tensile strength, and the tensile strength at 200°C was 210MPa. Moreover, the comparative example 11 showed rather high friction coefficient, and the value of friction coefficient was 0.58. According to friction coefficient, the value of seize load was 750(N). Furthermore, the value of abrasion loss was 48 ⁇ m.
  • the comparative example 11 showed poor tensile strength, poor antiseize, and poor wear resistance.
  • examples 1 to 3 and 14, 15 showed excellent tensile strength, excellent antiseize, and excellent wear resistance.
  • the examples 1 to 3 and 14, 15 showed excellent tensile strength, and the tensile strength at 200°C were in the range of 400 to 450 MPa.
  • the examples 1 to 3, 14 and 15 showed lower friction coefficient and excellent seize load, and the values of friction coefficient were in the range of 0.32 to 0.37, and the values of seize load were in the range of 1250 to 1750(N).
  • the examples 1 and 2 in which AlN was dispersed showed very excellent abrasion loss, and the values of abrasion loss were in the range of 2 to 3 ⁇ m.
  • the values of abrasion loss were in the range of 3 to 9 ⁇ m.
  • example 3, 14 and 15 also showed excellent abrasion loss, and the values of abrasion loss were in the range of 25 to 27 ⁇ m.
  • the examples 14 and 15 in which nitride and boride are dispersed showed more excellent wear resistance.
  • Figure 3 is an EPMA photograph (magnification x 1000) for showing Al distribution on the surface of the ring-shaped member when LFW experiment is performed on the example 1 of the present invention in which AlN is dispersed. According to Figure 3, Al is hardly adhered to the ring-shaped member. On the contrary, Figure 4 shows that Al is adhered to the ring-shaped member and agglutination abrasion is occured. Figure 4 is an EPMA photograph (magnification x 1000) for showing Al distribution on the surface of the ring-shaped member when LFW experiment is performed on the comparative example 9 in which AlN is not dispersed.
  • Figure 5 is a SEM photograph (magnification x 1000) after LFW experiment is performed on the example 1 of the present invention in which AlN is dispersed.
  • Figure 6 is an EPMA photograph (magnification x 1000) for showing N distribution after LFW experiment is performed on the example 1 of the present invention in which AlN is dispersed. As is obvious from Figures 5 and 6, it is confirmed that AlN particle is held in the matrix after LFW experiment is performed. It is also confirmed that no AlN particle is omitted.
  • Figure 8 (a) and (b) are optical micrographs (magnification x 100 and 400) for showing the metal structure of the comparative example 9.
  • Figure 9 (a) and (b) are optical micrographs (magnification x 100 and 400) for showing the metal structure of the example 1.
  • Figure 10 (a) and (b) are optical micrographs (magnification x 100 and 400) for showing the metal structure of the example 2.
  • Figure 11 is a SEM photograph (magnification x 5000) for showing the appearance of the dispersed AlN particle in the preferred embodiments.
  • the present invention completed an aluminum alloy which shows excellent tensile strength and excellent wear resistance.
  • the aluminum alloy consists essentially of 90 to 99.5% by weight of matrix and 0.5 to 10% by weight of a dispersant dispersed within the matrix.
  • the matrix comprises 10 to 25% by weight of Si, 5 to 20% by weight of Ni, 1 to 5% by weight of Cu and the rest of Al and impurity elements.
  • the dispersant is at least one selected from the group consisting of 0.5 to 10% of AlN and boride
  • the Al-Si alloy as matrix has hyper-eutectic structure because the amount of Si is 10 to 25%. Excellent wear resistance is provided by fine primary Si crystal. Since the Al-Si alloy also contains 5 to 20% of Ni, intermetallic compounds such as Al 3 Ni or Al 3 Ni 2 are formed. Therefore, tensile strength and wear resistance improve. Furthermore, tensile strength improves because 1 to 5% of Cu is added.
  • the obtained aluminum alloy member can be applied to engine parts, an intake valve, a piston, or the like. This achieves light weight of these elements.
  • the aluminum alloy shows high-heat conductivity and it is excellent in its tensile strength and wear resistance. Therefore, the aluminum alloy is suitable for the intake valve, and it is applied to the piston of high power engine. Furthermore, the aluminum alloy is also applied to cylinder liner since it is excellent in its wear resistance and antiseize. Moreover, when the aluminum alloy is applied to a valve retainer or a spring retainer, this achieves light weight of their elements.

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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 Alloys Or Alloy Compounds (AREA)

Claims (6)

  1. Alliage d'aluminium constitué de 90 à 99,5 % en poids de matrice et de 0,5 à 10 % en poids d'un agent dispersant dispersé à l'intérieur de ladite matrice, ladite matrice comprenant 10 à 25 % en poids de Si, 5 à 20 % en poids de Ni, 1 à 5 % de Cu et le reste d'Al et d'impuretés, ledit agent dispersant comprenant au moins un composé choisi dans le groupe constitué d'AlN et de borure, en une quantité de 0,5 à 10 %.
  2. Alliage d'aluminium selon la revendication 1, dans lequel ledit borure est le TiB2, le NiB, le MgB2 ou le ZrB2.
  3. Alliage d'aluminium selon la revendication 1, dans lequel ledit agent dispersant se présente sous forme de poudres, de barbes ou de fibres.
  4. Alliage d'aluminium selon la revendication 1, dans lequel ledit agent dispersant se présente sous forme d'une poudre ayant un diamètre de particule de 0,2 à 20 µm.
  5. Alliage d'aluminium selon la revendication 1, dans lequel ledit agent dispersant est dispersé à l'intérieur de la matrice par la métallurgie des poudres.
  6. Alliage d'aluminium selon la revendication 1, dans lequel la résistance à la rupture par traction, à 200° C, est de 400 à 490 MPa.
EP92309591A 1991-10-22 1992-10-21 Alliage d'aluminium Expired - Lifetime EP0539172B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP303964/91 1991-10-22
JP30396491 1991-10-22
JP4280543A JPH05311302A (ja) 1991-10-22 1992-09-25 高温強度および耐摩耗性に優れた低摩擦アルミニウム合金
JP280543/92 1992-09-25

Publications (2)

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EP0539172A1 EP0539172A1 (fr) 1993-04-28
EP0539172B1 true EP0539172B1 (fr) 1997-05-02

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DE (1) DE69219431T2 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110004327A (zh) * 2018-10-10 2019-07-12 上海交通大学 含陶瓷颗粒的铝锌镁铜合金及其制备方法和应用

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05311302A (ja) * 1991-10-22 1993-11-22 Toyota Motor Corp 高温強度および耐摩耗性に優れた低摩擦アルミニウム合金
EP0561204B1 (fr) * 1992-03-04 1997-06-11 Toyota Jidosha Kabushiki Kaisha Poudre d'alliage d'aluminium résistant à la chaleur, alliage d'aluminium résistant à la chaleur et matériau composite à base d'alliage d'aluminium résistant à la chaleur et à l'usure
EP0566098B1 (fr) * 1992-04-16 1997-01-22 Toyota Jidosha Kabushiki Kaisha Poudre d'alliage d'aluminium résistant à la chaleur, alliage d'aluminium résistant à la chaleur et matériau composite à base d'alliage d'aluminium résistant à la chaleur et à l'usure
DE69307848T2 (de) * 1992-12-03 1997-08-21 Toyota Motor Co Ltd Hoch warmfeste und verschleissfeste Aluminiumlegierung
DE19723868A1 (de) * 1996-11-21 1998-12-10 Seilstorfer Gmbh & Co Metallur Verwendungen eines hochwarmfesten Aluminiumwerkstoffs
JPH1136030A (ja) * 1997-07-17 1999-02-09 Yamaha Motor Co Ltd ピストン用アルミニウム合金及びピストン製造方法
CN104060128B (zh) * 2014-06-30 2016-05-25 安徽相邦复合材料有限公司 原位ZrB2、ALN混杂颗粒增强铝基复合材料及其制备方法

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US3551143A (en) * 1963-10-10 1970-12-29 Showa Denko Kk Aluminum base alloys having improved high temperature properties and method for their production
ES8504963A1 (es) * 1982-12-30 1985-05-01 Alcan Int Ltd Un metodo de fabricar un material de ceramica y metal
DE3807541C1 (fr) * 1988-03-08 1989-07-27 Daimler-Benz Aktiengesellschaft, 7000 Stuttgart, De
DK490388D0 (da) * 1988-09-02 1988-09-02 Risoe Forskningscenter Materiale
CA1327153C (fr) * 1988-10-07 1994-02-22 Haruo Shiina Dispositif de retenue de ressort de soupape de moteur a combustion interne

Non-Patent Citations (1)

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Title
CHEMICAL ABSTRACTS, vol. 104 Columbus, Ohio, US; abstract no. 73412, KOMURO, KATSUHIRO ET AL. 'Cast aluminum alloy composites containing dispersed ceramic powder' & JP-A-60 159 137 (HITACHI, LTD.) 20 August 1985 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110004327A (zh) * 2018-10-10 2019-07-12 上海交通大学 含陶瓷颗粒的铝锌镁铜合金及其制备方法和应用

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EP0539172A1 (fr) 1993-04-28
DE69219431T2 (de) 1997-10-09
DE69219431D1 (de) 1997-06-05

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