WO1992007676A1 - Poudre a base d'un alliage aluminium/silicium hypereutectique et production de cette poudre - Google Patents

Poudre a base d'un alliage aluminium/silicium hypereutectique et production de cette poudre Download PDF

Info

Publication number
WO1992007676A1
WO1992007676A1 PCT/JP1991/001488 JP9101488W WO9207676A1 WO 1992007676 A1 WO1992007676 A1 WO 1992007676A1 JP 9101488 W JP9101488 W JP 9101488W WO 9207676 A1 WO9207676 A1 WO 9207676A1
Authority
WO
WIPO (PCT)
Prior art keywords
silicon
alloy powder
aluminum
weight
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.)
Ceased
Application number
PCT/JP1991/001488
Other languages
English (en)
Japanese (ja)
Inventor
Yoshinobu Takeda
Tetsuya Hayashi
Toshihiko Kaji
Yusuke Odani
Kiyoaki Akechi
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
Sumitomo Electric Industries Ltd
Original Assignee
Toyo Aluminum KK
Sumitomo Electric Industries 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 Toyo Aluminum KK, Sumitomo Electric Industries Ltd filed Critical Toyo Aluminum KK
Priority to DE69120299T priority Critical patent/DE69120299T2/de
Priority to US07/863,285 priority patent/US5366691A/en
Priority to EP91918937A priority patent/EP0592665B1/fr
Publication of WO1992007676A1 publication Critical patent/WO1992007676A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • 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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent

Definitions

  • the present invention relates to a hypereutectic aluminum-silicon-based alloy powder and a method for producing the same, and in particular, to a hypereutectic aluminum-silicon-based alloy powder having a stable fine silicon primary crystal. And its manufacturing method.
  • A11-Si-based alloys steel materials are classified as AC or ADC according to the JIS standard, and are used in large quantities as aluminum alloys such as engine blocks.
  • A1-Si-based alloys as wrought materials are classified into the 4000 series, and are added to various parts by extrusion, forging, etc. from forged billets.
  • hypereutectic Al-Si alloys are produced by a sintering method.
  • Hypereutectic A 1 -Si-based alloys obtained by sintering have excellent properties such as low coefficient of thermal expansion, high rigidity, high wear resistance, and are suitable for use in various fields. It is expected.
  • hypereutectic A 1 -Si-based alloy The presence of large silicon primary crystals degrades their mechanical properties and machinability during machining.
  • a rapidly solidified powder manufacturing method such as an atomizing method can produce a powder from a molten metal at a large cooling rate that was impossible with the melt-casting method.
  • the primary crystal of silicon can be refined and contains silicon having a eutectic composition or more, and further, iron (Fe) and nickel (Ni) as the third alloy components.
  • transition metal elements X such as chromium (Cr) and manganese (Mn).
  • Al — 17 S i — X, A 1-20 S i-X, A Powder metallurgy alloys such as 1-25Si-X have been put to practical use.
  • the primary crystal of silicon can be refined by increasing the cooling rate when producing powder.
  • the cooling rate is largely determined by the atomizing method and equipment, and increasing the cooling rate by other industrial methods has not been realized due to economic and productivity problems.
  • the present invention has been made in view of the above-described conventional circumstances, and it has been found that the atomization method allows the silicon primary crystals to be fine and uniform, and particularly suppresses the crystallization of coarse silicon primary crystals. It is an object of the present invention to provide a possible hypereutectic A 1 —Si alloy powder composition and a method for producing the same.
  • an aluminum silicon-based material to which a primary crystal silicon refiner containing phosphorus is added is added. It is obtained by melting a molten alloy or an aluminum-silicon alloy ingot containing a phosphorus-containing primary crystal silicon refiner in advance. The molten alloy is prepared using air or an inert gas. It was found that by atomizing, an extremely fine hypereutectic aluminum-silicon alloy powder of primary silicon could be obtained.
  • silicon is contained in an amount of from 12% by weight to 50% by weight, and phosphorus is contained in an amount of 0.0005% by weight or more. Contains 0.1% by weight or less.
  • the particle diameter of the primary crystal silicon in the hypereutectic aluminum silicon-based alloy powder of the present invention is the same as that of the primary crystal silicon in the hypereutectic aluminum-silicon alloy obtained by the conventional fabrication method. Much smaller than the size, usually less than 10 m.
  • the aluminum-silicon alloy powder of the present invention has a silicon content of 12% by weight or more and 50% by weight or less, preferably 20% by weight or more and 30% by weight or less. If the silicon content is less than 12% by weight, primary silicon does not crystallize. On the other hand, if the silicon content exceeds 50% by weight, the amount of primary crystal silicon is too large even if the primary crystal of silicon is refined no matter how much, and it was made from the obtained powder. The machinability of the solidified body is poor, and its mechanical strength is also poor.
  • the phosphorus content in the aluminum silicon alloy powder of the present invention is from 0.0005% to 0.1% by weight, preferably from 0.0005% to 0.05% by weight. It is as follows. If the content of phosphorus is less than 0.0005% by weight, no refining effect is obtained and no improvement in mechanical strength is observed. On the other hand, even if the phosphorus content exceeds 0.1% by weight, the effect of miniaturization is not further improved. In particular, aluminum-silicon alloy powder having a phosphorus content of 0.02% by weight or more and 0.1% by weight or less has excellent machinability during machining.
  • a molten metal of a hypereutectic aluminum-silicon alloy containing phosphorus is prepared.
  • the molten metal is sprayed and rapidly solidified using air or an inert gas.
  • the melt of a hypereutectic aluminum silicon-based alloy containing phosphorus can be either a molten aluminum-silicon-based alloy to which a primary silicon-containing alloy refiner containing phosphorus is added, or a molten metal containing phosphorus.
  • the primary silicon refiner containing phosphorus may be any molten alloy obtained by melting an aluminum silicon-based alloy ingot containing a crystalline silicon refiner in advance.
  • primary crystal silicon refining agents used in conventional manufacturing methods such as Cu—8 wt% P, Cu
  • the primary crystal silicon refining agent is usually used in an amount of 0.0005% to 0.1% by weight, preferably 0.02% to 0.05% by weight. Is done. When the amount of the primary crystal silicon refiner is less than 0.005% by weight, the effect of the addition of the primary silicon refiner is not sufficient. Further, even if the primary crystal silicon refiner is added in an amount exceeding 0.1% by weight, no further improvement in the effect is observed.
  • the aluminum silicon alloy melt is subjected to an atomizing treatment according to a known method.
  • the alloy melt is subjected to the atomizing treatment while being kept at a temperature of 100 ° C. or higher and 130 ° C. or lower than the liquidus temperature of the aluminum-silicon alloy. It is preferable. Even when the primary silicon refiner is added to the aluminum-silicon alloy, it is preferable to keep the alloy at the above temperature.
  • the liquidus temperature means the temperature at which the alloy of the composition is completely melted.
  • the liquidus temperature of an aluminum-silicon alloy containing 25% by weight of silicon is about 780 ° C.
  • the molten alloy is maintained at a temperature lower than the liquidus temperature of the aluminum silicon-based alloy at (liquidus temperature + 100), the dissolution of the phosphorus will be insufficient and the amount of added phosphorus will be insufficient. In contrast, the amount of phosphorus contained in the alloy is reduced, and it is difficult to obtain an alloy powder containing the correct amount of phosphorus. Also, if the molten alloy is kept at a temperature exceeding 1300 ° C, the crucible and the furnace material will be seriously damaged, and depending on the contained alloy element, it will partially evaporate and have the desired composition. An alloy may not be obtained.
  • the aluminum-silicon alloy to which the method of the present invention is applied is not particularly limited, and elements other than aluminum and silicon, for example, magnesium, manganese, iron, nickel, zinc General aluminum silicon-based alloys containing the same may also be included.
  • the production method of the present invention is particularly useful for aluminum-silicon alloys having a high silicon content (20 to 40% by weight).
  • a hypereutectic aluminum silicon alloy powder in which extremely fine primary crystals are uniformly dispersed can be obtained. Further, when manufactured under the above preferable conditions, a hypereutectic aluminum-silicon alloy powder having a desired composition can be obtained.
  • the solidified body produced from the hypereutectic aluminum-silicon alloy powder of the present invention has extremely excellent machinability and mechanical properties.
  • a molten metal of a hypereutectic aluminum-silicon alloy containing phosphorus is prepared. It is.
  • the hypereutectic aluminum silicon-based alloy powder is produced by spraying and rapidly solidifying the molten metal using air. Only alloy powder with a particle size of 400 m or less is selected.
  • the inoculation method used in the melt-casting method is applied, and first, phosphorus is inoculated into a molten hypereutectic aluminum-double-silicon alloy for atomization.
  • nuclei for solidification can be prepared in advance, and uneven nucleation due to supercooling can be suppressed.
  • the inoculated phosphorus must be uniformly dispersed in the molten metal as solid particles at the spray temperature. At the same time, if undissolved components other than phosphorus are present in the molten metal, coarse crystals can easily be formed.
  • the inoculated molten metal can be once cooled and solidified, then melted again and returned to the original inoculated molten metal state.
  • the air atomization method is used as a method for producing powder by rapid solidification because it is more economical than other methods and because the surface of the powder is stabilized by moderate oxidation, handling is easy. This is because there are advantages such as
  • the rapid solidification condition is that the higher the cooling rate, the finer the structure becomes.
  • a large number of crystallization nuclei of silicon primary crystals are previously contained in the molten metal.
  • the presence makes it possible to control the maximum crystal grain size of the primary silicon in a fine and narrow range with respect to the grain size of the obtained powder without strongly depending on the cooling rate which is difficult to directly control.
  • fine and relatively uniform primary crystals of silicon can be obtained even at a lower cooling rate (the particle size of the obtained powder is relatively large) as compared with the conventional atomizing method.
  • the maximum crystal grain size of the primary crystal silicon can be controlled to be equal to or less than 100 // m.
  • the maximum crystal grain size of primary silicon can be controlled to be 7 m or less. More preferably, if the grain size of the obtained alloy powder is selected to be 100 m or less, the maximum crystal grain size of primary silicon can be controlled to 5 m or less. If the particle size of the obtained alloy powder is selected to be 50 / zm or less, the maximum crystal grain size of primary silicon can be controlled to 3 zm or less.
  • the concentration of the inoculated phosphorus is preferably in the range of 0.05% by weight or more and 0.02% by weight or less.
  • the primary crystal silicon of the hypereutectic aluminum-silicon alloy powder produced by the atomization method is refined and uniformized,
  • the dependence of the primary crystal silicon particle size on the alloy powder particle size can be significantly reduced as compared with the conventional case.
  • a crystalline aluminum-silicon alloy powder it is possible to produce a solidified powder having improved mechanical properties at a high yield without restriction on the powder particle size.
  • FIG. 2 is a photograph of a crystal structure by an optical microscope showing a structure of primary crystal silicon in the alloy powder obtained in Comparative Example 1 (magnification: X400).
  • FIG. 3 is a photograph of the crystal structure by an optical microscope showing the structure of primary silicon in the forged alloy (magnification: X400).
  • FIG. 4 is an optical micrograph showing the metallographic structure of the hypereutectic aluminum 25-% by weight silicon alloy powder obtained in Example 3 and inoculated with phosphorus (magnification: X 40%). 0).
  • FIG. 5 is an optical micrograph (magnification: X400) showing the metal structure of the hypereutectic aluminum-125% by weight silicon alloy powder obtained in Example 3 but not inoculated with phosphorus.
  • FIG. 6 shows the relationship between the maximum grain size of silicon primary crystals in the hypereutectic aluminum alloy 25% by weight silicon alloy powder and the tensile strength at room temperature of the solidified body obtained from the powder in Example 3. It is a graph which shows a relationship.
  • Example 1 A molten aluminum alloy having the composition shown in Table 1 was maintained at a temperature of 950 ° C, and Cu-8% by weight P was melted so as to obtain the phosphorus content shown in Table 1. Was added. After maintaining the molten metal at a temperature of 950 ° C. for 1 hour, the molten metal was pulverized by an air atomizing method (see alloy powders N 0.1 to N 0.4 in Table 1).
  • Alloy powder N 0.5 was prepared under the same conditions as alloy powder No. 1. However, in this case, Cu—8% by weight of P was not added to the molten aluminum alloy.
  • the size of the primary crystal silicon in the powder is optically determined. It was measured by observing the structure with a microscope. The results are shown in Table 1. A micrograph of the alloy powder N 0.5 by an optical microscope is shown in FIG.
  • Aluminum alloy having the same composition as alloy powder No. 1. was maintained at a temperature of 950 ° C., and Cu—8 wt% P was added so that the phosphorus content shown in Table 1 was obtained. After holding at a temperature of 950 ° C. for 1 hour, the molten metal was poured into a mold having a diameter of 30 mm and a height of 80 mm to prepare an alloy material (No. 6).
  • the size of the primary crystal silicon in the alloy powder obtained by the method of the present invention was determined by the size of the lithium obtained in Comparative Example 1. It is clear that the particles are finer and more uniformly dispersed than the size of the primary silicon in the alloy powder of the same composition, which does not contain copper.
  • Comparative Example 1 A (structure N 0, 6) 1.01 From the results shown in Table 2, it is clear that the machinability of the compact produced from the alloy powder of the present invention is extremely excellent.
  • Alloy powders No. 16 to No. 18 were prepared under the same conditions as alloy powders No. ll to No. 15. However, in this case, Aluminum alloy ingots that do not contain phosphorus were used.
  • the alloy powders N 0.11 to N 0.18 obtained in Example 2 and Comparative Example were converted to 100 mesh (particle size of less than 147 / zm). After classification, cold preforming was performed at a pressure of 3 ton Z cm 2 to a size of 30 mm in diameter ⁇ 80 mm in height. Thereafter, these compacts were hot extruded into a flat plate having a width of 2 mm and a thickness of 4 mm at an extrusion temperature of 450 ° C. and an extrusion ratio of 10. After the flat plate extruded material thus obtained was subjected to T6 treatment, the transverse rupture strength was measured at a gauge distance of 30 mm based on JISZ223. The results are shown in Table 4. Table 4
  • the die strength of the alloy powder containing phosphorus of the present invention is about 10% higher than that of the alloy powder containing no phosphorus.
  • the alloy powder of the invention of No. 13 having a phosphorus content exceeding 0.02% by weight The force to lower the transverse rupture strength slightly compared to No. 16 of the alloy powder. It can be used sufficiently.
  • the following hypereutectic aluminum-silicon alloys were prepared from metal.
  • A-20 20 24 bullion + 20 wt% S i
  • the obtained alloy powder was continuously collected, classified by air, and further classified by sieving.
  • the particle size of the silicon co down primary crystals of these alloy powders as a result of determining by quantitative image analysis microscope, the maximum particle diameter D e of the powder particle size D p and S i primary crystal; the relationship first Table 5 shown in Table 5
  • the hypereutectic aluminum mini-silicon alloy powder obtained for the A-25 alloy was classified based on the maximum grain size of the silicon primary crystal.
  • the tensile strength at room temperature of the solidified product of each powder produced under the same conditions as above was measured. The results of these measurements are shown in FIG. From the above results, according to the production method of the present invention, the size of the silicon primary crystal in the powder can be controlled to be small and extremely narrow, so that the coarse silicon crystal is used as a starting point. The resulting fracture is significantly reduced and the mechanical strength of the solidified powder is improved. In addition, even when cutting the obtained solidified body, effects such as stabilization and control of chipping and wear of the cutting tool can be obtained.
  • the compact produced from the hypereutectic aluminum-silicon alloy powder according to the present invention has extremely excellent machinability and mechanical strength. Therefore, it is useful as a part for various mechanical structures.
  • the primary crystal silicon of the hypereutectic aluminum-silicon alloy powder can be made finer and uniform. The dependence of the primary silicon particle size on the powder particle size can be significantly reduced as compared with the conventional case. As a result, it is possible to produce a solidified powder having improved mechanical properties as compared with the conventional one at a high yield.

Landscapes

  • 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)

Abstract

On produit une poudre à base d'un alliage aluminium/silicium hypereutectique, dans laquelle un cristal primaire de silicium possède un tout petit grain dont le diamètre est inférieur ou égal à 10 νm, grâce au processus de l'atomisation, lequel consiste à préparer un bain de fusion d'un alliage aluminium/silicium hypereutectique contenant du phosphore et à vaporiser le bain de fusion à l'aide d'air ou d'un gaz inactif pour produire un refroidissement rapide permettant la solidification. La poudre d'alliage ainsi obtenue contient 12 à 50 % en poids de silicium et 0,0005 à 0,1 % en poids de phosphore. Cette poudre peut constituer une poudre solidifiée ayant des propriétés mécaniques améliorées avec un rendement élevé sans aucune restriction de granulométrie.
PCT/JP1991/001488 1990-10-31 1991-10-31 Poudre a base d'un alliage aluminium/silicium hypereutectique et production de cette poudre Ceased WO1992007676A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
DE69120299T DE69120299T2 (de) 1990-10-31 1991-10-31 Übereutektisches aluminium-silikon-pulver und dessen herstellung
US07/863,285 US5366691A (en) 1990-10-31 1991-10-31 Hyper-eutectic aluminum-silicon alloy powder and method of preparing the same
EP91918937A EP0592665B1 (fr) 1990-10-31 1991-10-31 Poudre a base d'un alliage aluminium/silicium hypereutectique et production de cette poudre

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP2/295099 1990-10-31
JP29501990 1990-10-31
JP29501890 1990-10-31
JP2/295019 1990-10-31
JP29509990 1990-10-31
JP2/295018 1990-10-31

Publications (1)

Publication Number Publication Date
WO1992007676A1 true WO1992007676A1 (fr) 1992-05-14

Family

ID=27337951

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP1991/001488 Ceased WO1992007676A1 (fr) 1990-10-31 1991-10-31 Poudre a base d'un alliage aluminium/silicium hypereutectique et production de cette poudre

Country Status (3)

Country Link
EP (1) EP0592665B1 (fr)
DE (1) DE69120299T2 (fr)
WO (1) WO1992007676A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5405576A (en) * 1991-07-22 1995-04-11 Toyo Aluminum Kabushiki Kaisha Hypereutectic aluminum-silicon alloys produced by powder metallurgy techniques
CN114101689A (zh) * 2021-11-15 2022-03-01 河北新立中有色金属集团有限公司 气雾化制粉用高硅铝合金熔体流动性、纯净度控制方法
CN116970831A (zh) * 2023-09-13 2023-10-31 四川航天职业技术学院(四川航天高级技工学校) 一种高硅铝合金细化方法

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08333645A (ja) * 1995-06-06 1996-12-17 Toyota Motor Corp 耐凝着性に優れたＡｌ基複合材料及びその製造方法
GB9514777D0 (en) * 1995-07-19 1995-09-20 Osprey Metals Ltd Silicon alloys for electronic packaging
DE19532252C2 (de) * 1995-09-01 1999-12-02 Erbsloeh Ag Verfahren zur Herstellung von Laufbuchsen
DE19532253C2 (de) * 1995-09-01 1998-07-02 Peak Werkstoff Gmbh Verfahren zur Herstellung von dünnwandigen Rohren (II)
DE19532244C2 (de) * 1995-09-01 1998-07-02 Peak Werkstoff Gmbh Verfahren zur Herstellung von dünnwandigen Rohren (I)

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5937339B2 (ja) * 1977-04-15 1984-09-08 昭和電工株式会社 高ケイ素アルミニウム合金焼結体の製造方法
JPS63266004A (ja) * 1987-11-10 1988-11-02 Showa Denko Kk 耐熱耐摩耗性高力アルミニウム合金粉末
JPH01147038A (ja) * 1987-12-02 1989-06-08 Honda Motor Co Ltd 粉末冶金用耐熱Ａｌ合金
JPH02213401A (ja) * 1989-02-13 1990-08-24 Toyota Motor Corp 粉末冶金用アルミニウム合金粉末

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3953202A (en) * 1975-02-10 1976-04-27 Kawecki Berylco Industries, Inc. Phosphorus-bearing master composition for addition to hyper-eutectic silicon-aluminum casting alloys and process therefor
JPS55145134A (en) * 1979-04-27 1980-11-12 Aikoorosuborou Kk Grain refiner for hyper-eutectic aluminum-silicon alloy
EP0185540A3 (fr) * 1984-12-18 1987-05-27 Sumitomo Light Metal Industries Limited Procédé pour l'affinage du grain de silicium primaire dans les alliages hypereutectiques Al-Si
FR2604186A1 (fr) * 1986-09-22 1988-03-25 Peugeot Procede de fabrication de pieces en alliage d'aluminium hypersilicie obtenu a partir de poudres refroidies a tres grande vitesse de refroidissement
JPS63108945A (ja) * 1986-10-27 1988-05-13 Nippon Light Metal Co Ltd 初晶珪素微細化用フラツクス
JP2703840B2 (ja) * 1991-07-22 1998-01-26 東洋アルミニウム 株式会社 高強度の過共晶Ａ１―Ｓｉ系粉末冶金合金

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5937339B2 (ja) * 1977-04-15 1984-09-08 昭和電工株式会社 高ケイ素アルミニウム合金焼結体の製造方法
JPS63266004A (ja) * 1987-11-10 1988-11-02 Showa Denko Kk 耐熱耐摩耗性高力アルミニウム合金粉末
JPH01147038A (ja) * 1987-12-02 1989-06-08 Honda Motor Co Ltd 粉末冶金用耐熱Ａｌ合金
JPH02213401A (ja) * 1989-02-13 1990-08-24 Toyota Motor Corp 粉末冶金用アルミニウム合金粉末

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP0592665A4 *

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5405576A (en) * 1991-07-22 1995-04-11 Toyo Aluminum Kabushiki Kaisha Hypereutectic aluminum-silicon alloys produced by powder metallurgy techniques
CN114101689A (zh) * 2021-11-15 2022-03-01 河北新立中有色金属集团有限公司 气雾化制粉用高硅铝合金熔体流动性、纯净度控制方法
CN114101689B (zh) * 2021-11-15 2023-11-03 河北新立中有色金属集团有限公司 气雾化制粉用高硅铝合金熔体流动性、纯净度控制方法
CN116970831A (zh) * 2023-09-13 2023-10-31 四川航天职业技术学院(四川航天高级技工学校) 一种高硅铝合金细化方法

Also Published As

Publication number Publication date
DE69120299D1 (de) 1996-07-18
DE69120299T2 (de) 1997-01-23
EP0592665A1 (fr) 1994-04-20
EP0592665A4 (fr) 1993-11-19
EP0592665B1 (fr) 1996-06-12

Similar Documents

Publication Publication Date Title
JP5326114B2 (ja) 高強度銅合金
US6471797B1 (en) Quasicrystalline phase-reinforced Mg-based metallic alloy with high warm and hot formability and method of making the same
EP0144898A2 (fr) Alliages d'aluminium et procédé pour leur fabrication
JP4500916B2 (ja) マグネシウム合金及びその製造方法
JPH02503331A (ja) 機械抵抗の高いマグネシウム合金及び該合金の急速凝固による製造方法
EP0821072B1 (fr) Alliage composite à base d'aluminium à haute résistance d'usure et pièces résistant à l'usure
Qin et al. Microstructure evolution of in situ Mg2Si/Al–Si–Cu composite in semisolid remelting processing
WO2010007484A1 (fr) Alliage d’aluminium, procédé de coulage d’alliage d’aluminium et procédé de production d’un produit d’alliage d’aluminium
CN114438374B (zh) 一种Al-V-Ti-B晶粒细化剂及其制备和应用方法
JP5691477B2 (ja) Ａｌ−Ｓｉ系合金及びその製造方法
JP2021507088A (ja) 添加剤技術用のアルミニウム合金
JP3173452B2 (ja) 耐摩耗性被覆部材及びその製造方法
JP2703840B2 (ja) 高強度の過共晶Ａ１―Ｓｉ系粉末冶金合金
EP0105595B1 (fr) Alliages à base d'aluminium
JP3283550B2 (ja) 初晶シリコンの最大結晶粒径が１０μｍ以下の過共晶アルミニウム−シリコン系合金粉末の製造方法
US5366691A (en) Hyper-eutectic aluminum-silicon alloy powder and method of preparing the same
WO1992007676A1 (fr) Poudre a base d'un alliage aluminium/silicium hypereutectique et production de cette poudre
CN111411270B (zh) 一种改变铝合金中硅铁相形貌的方法
JPH07316601A (ja) アルミニウム急冷凝固粉末およびアルミニウム合金成形材の製造方法
WO2003080881A1 (fr) Processus de production d'alliages al-fe-v-si
JPH10298684A (ja) 強度、耐摩耗性及び耐熱性に優れたアルミニウム基合金−硬質粒子複合材料
JPH062057A (ja) Ａｌ基複合材料
JP3485961B2 (ja) 高強度アルミニウム基合金
JP2023069367A (ja) 過共晶Ａｌ－Ｓｉ合金及び過共晶Ａｌ－Ｓｉ合金鋳物並びにその製造方法
Gomez Influence of nano-particles of alumina (Al2O3) and titanium di-boride (TiB2) on the microstructure and properties of the alloy Al-Cu 3-Fe1-Si9 for foundry applications to high pressure

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): US

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): AT BE CH DE DK ES FR GB GR IT LU NL SE

WWE Wipo information: entry into national phase

Ref document number: 1991918937

Country of ref document: EP

WWP Wipo information: published in national office

Ref document number: 1991918937

Country of ref document: EP

WWG Wipo information: grant in national office

Ref document number: 1991918937

Country of ref document: EP