EP0592665B1 - 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

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EP0592665B1
EP0592665B1 EP91918937A EP91918937A EP0592665B1 EP 0592665 B1 EP0592665 B1 EP 0592665B1 EP 91918937 A EP91918937 A EP 91918937A EP 91918937 A EP91918937 A EP 91918937A EP 0592665 B1 EP0592665 B1 EP 0592665B1
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Prior art keywords
silicon
alloy powder
aluminum
percent
weight
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EP0592665A1 (fr
EP0592665A4 (fr
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Yoshinobu Itami Works Of Sumitomo Elect. Takeda
Tetsuya Itami Works Of Sumitomo Electr. Hayashi
Toshihiko Itami Works Of Sumitomo Electri. Kaji
Yusuke Itami Works Of Sumitomo Electric Odani
Kiyoaki Itami Works Of Sumitomo Electric Akechi
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Toyo Aluminum KK
Sumitomo Electric Industries Ltd
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Toyo Aluminum KK
Sumitomo Electric Industries Ltd
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    • 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

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  • the present invention relates to hyper-eutectic aluminum-silicon alloy powder and a method of preparing the same, and more particularly, it relates to hyper-eutectic aluminum-silicon alloy powder which stably contains fine silicon primary crystals and a method of preparing the same.
  • Al-Si alloys a cast material is classified as AC or ADC under the Japanese Industrial Standards, and employed in plenty as an aluminum alloy casting such as an engine block.
  • An Al-Si alloy prepared as an wrought material is classified in the 4,000 series, and worked from a cast billet into various parts by extrusion, forging or the like.
  • a hyper-eutectic Al-Si alloy is prepared by a casting method.
  • a hyper-eutectic Al-Si alloy casting obtained by the casting method which has excellent properties such as a low thermal expansion coefficient, a high Young's modulus and high wear resistance, is expected for employment in various fields.
  • a hyper-eutectic Al-Si alloy casting contains coarse primary crystals of silicon, however, its mechanical properties and machinability in machine work are deteriorated.
  • a refiner particularly phosphorus (P)
  • P phosphorus
  • a refiner may be added in order to refine primary crystals of silicon contained in a hyper-eutectic Al-Si alloy casting. Even if such a refiner is added when a hyper-eutectic Al-Si alloy is cast, however, refinement of silicon primary crystals is restricted. Particularly when the Al-Si alloy contains silicon in excess of 20 percent by weight, coarse primary crystals of silicon still remain even if the refiner is added, and hence the alloy is still deteriorated in mechanical properties and machinability in machine work.
  • Powder metallurgical alloys such as Al-17Si-X, Al-20Si-X and Al-25Si-X, having properties further superior to those of cast alloys, have been put into practice as alloys prepared by a powder metallurgical method using such powder materials.
  • a cooling rate in preparation of powder may be increased in order to refine primary crystals of silicon.
  • a cooling rate is generally decided by a method of and an apparatus for atomizing, and no other industrial method of increasing such a cooling rate has been implemented due to problems in economic property and productivity.
  • the particle sizes of silicon primary crystals contained in the overall powder are extremely dispersed so far as the as-obtained powder has particle size distribution of a constant width, since the cooling rate depends on the particle size of the powder.
  • powder of about 400 ⁇ m in particle size has generally unavoidably contained coarse silicon primary crystals of about 20 ⁇ m in particle size.
  • an object of the present invention is to provide a composition of hyper-eutectic Al-Si alloy powder containing fine and homogeneous primary crystals of silicon and being capable of suppressing primary crystallization of coarse primary crystals of silicon in particular by atomizing, and a method of preparing the same.
  • EP-A-0 265 307 discloses a device with the features of the preamble of claim 1.
  • hyper-eutectic aluminum-silicon alloy powder containing extremely fine primary crystal silicon can be obtained by atomizing a molten metal of an aluminum-silicon alloy to which a primary crystal silicon refiner containing phosphorus is added, or an alloy molten metal obtained by melting an aluminum-silicon alloy ingot previously containing a primary crystal silicon refiner containing phosphorus, with air or an inert gas.
  • Hyper-eutectic aluminum-silicon alloy powder in accordance with a first aspect of the present invention is defined in claim 1. It contains at least 12 percent by weight and not more than 50 percent by weight of silicon, and at least 0.0005 percent by weight and not more than 0.1 percent by weight of phosphorus.
  • the particle size of primary crystal silicon contained in the inventive hyper-eutectic aluminum-silicon alloy powder is by far smaller than the size of primary crystal silicon contained in a conventional hyper-eutectic aluminum-silicon alloy obtained by a casting method, and is of at least 1 ⁇ m and not more than 10 ⁇ m.
  • the content of silicon in the inventive aluminum-silicon alloy powder is at least 12 percent by weight and not more than 50 percent by weight, preferably at least 20 percent by weight and not more than 30 percent by weight. If the content of silicon is less than 12 percent by weight, no primary crystal silicon is formed. If the content of silicon exceeds 50 percent by weight, on the other hand, the amount of primary crystal silicon is too much however primary crystals of silicon are refined, and hence consolidates prepared from the as-obtained powder are inferior in machinability while its mechanical strength is deteriorated.
  • the content of phosphorus in the inventive aluminum-silicon alloy powder is at least 0.0005 percent by weight and not more than 0.1 percent by weight, preferably at least 0.0005 percent by weight and not more than 0.05 percent by weight. If the content of phosphorus is less than 0.0005 percent by weight, no effect of refinement is attained and no improvement of mechanical strength is recognized. On the other hand, the effect of refinement is no more improved even if the content of phosphorus exceeds 0.1 percent by weight.
  • Aluminum-silicon alloy powder containing at least 0.02 percent by weight and not more than 0.1 percent by weight of phosphorus is particularly excellent in machinability in machine work.
  • More preferable and concrete aluminum-silicon alloy powder according to the present invention contains at least 12 percent by weight and not more than 50 percent by weight of silicon, at least 2.0 percent by weight and not more than 3.0 percent by weight of copper, at least 0.5 percent by weight and not more than 1.5 percent by weight of magnesium, at least 0.2 percent by weight and not more than 0.8 percent by weight of manganese and at least 0.0005 percent by weight and not more than 0.05 percent by weight of phosphorus, with a rest of aluminum and unavoidable impurities.
  • Aluminum-silicon alloy powder containing the respective elements of copper, magnesium and manganese has high mechanical strength.
  • a molten metal of a hyper-eutectic aluminum-silicon alloy containing phosphorus is prepared previously.
  • the molten metal is atomized with air or an inert gas, and quench-solidified.
  • the molten metal of a hyper-eutectic aluminum-silicon alloy containing phosphorus is prepared from a molten metal of an aluminum-silicon alloy to which a primary crystal silicon refiner containing phosphorus is added, or an alloy molten metal obtained by melting an aluminum-silicon alloy ingot previously containing a primary crystal silicon refiner containing phosphorus.
  • the primary crystal silicon refiner containing phosphorus is prepared from a primary crystal silicon refiner employed in a conventional casting method, such as Cu-8wt.%P, Cu-15wt.%P, PCl5 or mixed salt mainly composed of red phosphorus, or an Al-Cu-P refiner.
  • the primary crystal silicon refiner is generally used in an amount of at least 0.0005 percent by weight and not more than 0.1 percent by weight, preferably at least 0.002 percent by weight and not more than 0.05 percent by weight. If the amount of the primary crystal silicon refiner is less than 0.0005 percent by weight, no sufficient effect is attained by addition of the primary crystal silicon refiner. On the other hand, no further improvement of the effect is recognized even if the primary crystal silicon refiner is added in an amount exceeding 0.1 percent by weight.
  • the aluminum-silicon alloy molten metal is atomized according to a well-known method.
  • the alloy molten metal is preferably atomized in a state being at a temperature of at least a level exceeding the liquidus temperature of the aluminum-silicon alloy by 100°C and not more than 1300°C. Also when the primary crystal silicon refiner is added to the aluminum-silicon alloy, the alloy is preferably held at the aforementioned temperature.
  • liquidus temperature indicates a temperature at which the alloy of the composition is completely molten.
  • the liquidus temperature of an aluminum-silicon alloy containing 25 percent by weight of silicon is about 780°C.
  • the alloy molten metal is held at the temperature of at least a level exceeding the liquidus temperature of the aluminum-silicon alloy by 100°C and not more than 1300°C at least for 30 minutes, and thereafter atomized.
  • the holding time is shorter than 30 minutes, phosphorus is so insufficiently molten that the amount of phosphorus contained in the alloy is reduced as compared with the amount of the added phosphorus, and it is difficult to obtain alloy powder containing phosphorus in a correct amount.
  • this does not apply to employment of an Al-Cu-P inoculant (holding time may be reduced to be shorter than 30 minutes).
  • An aluminum-silicon alloy to which the inventive method is applied is not particularly restricted but can also include a general aluminum-silicon alloy containing elements other than aluminum and silicon, such as copper, magnesium, manganese, iron, nickel, zinc and the like.
  • the inventive preparation method is particularly useful for an aluminum-silicon alloy having a high content (at least 20 percent by weight and not more than 40 percent by weight) of silicon.
  • hyper-eutectic aluminum-silicon alloy powder in which extremely fine primary crystal silicon is homogeneously dispersed.
  • hyper-eutectic aluminum-silicon alloy powder having a desired composition.
  • Consolidates prepared from the inventive hyper-eutectic aluminum-silicon alloy powder have extremely superior machinability and mechanical properties.
  • a molten metal of a hyper-eutectic aluminum-silicon alloy containing phosphorus is prepared previously. This molten metal is atomized with air and quench-solidified, thereby preparing hyper-eutectic aluminum-silicon alloy powder. Only alloy powder of not more than 400 ⁇ m in particle size is selected.
  • an inoculation method which has been employed in a casting method is applied, to first inoculate a hyper-eutectic aluminum-silicon alloy molten metal for atomizing with phosphorus.
  • the inoculated molten metal is atomized by air atomizing, and quench-solidified.
  • the air atomizing is employed as the method of preparing powder by quench solidification, since this method is more economic as compared with other methods and the powder can be easily handled since its surface is stabilized by suitable oxidation.
  • the maximum crystal grain size of the primary crystal silicon can be controlled to be not more than 10 ⁇ m.
  • the maximum crystal grain size of the primary crystal silicon can be controlled to be not more than 7 ⁇ m when the particle size of the as-obtained alloy powder is selected to be not more than 200 ⁇ m. More preferably, the maximum crystal grain size of the primary crystal silicon can be controlled to be not more than 5 ⁇ m when the particle size of the as-obtained alloy powder is selected to be not more than 100 ⁇ m. Further, the maximum crystal grain size of the primary crystal silicon can be controlled to be not more than 3 ⁇ m when the particle size of the as-obtained alloy powder is selected to be not more than 50 ⁇ m.
  • the concentration of the inoculated phosphorus is preferably in a range of at least 0.005 percent by weight and not more than 0.02 percent by weight.
  • the third aspect of the present invention it is possible to refine and homogenize primary crystal silicon contained in hyper-eutectic aluminum-silicon alloy powder prepared by atomizing, as well as to remarkably reduce dependency of the particle size of the primary crystal silicon on the grain size of the alloy powder as compared with the prior art. Consequently, it is possible to prepare consolidates of powder which are more improved in mechanical properties as compared with the prior art, with no restriction of powder grain size in a high yield by employing the as-obtained hyper-eutectic aluminum-silicon alloy powder.
  • Molten metals of aluminum alloys having compositions shown in Table 1 were held at a temperature of 950°C, and Cu-8wt.%P was added to the molten metals to attain contents of phosphorus shown in Table 1. The molten metals were held at the temperature of 950°C for 1 hour, and then powdered by air atomizing (refer to alloy powder samples No. 1 to No. 4 in Table 1).
  • the as-obtained alloy powder samples were classified in -42 to -80 meshes (particle sizes of 175 to 350 ⁇ m), and thereafter sizes of primary crystal silicon particles contained in the powder samples were measured through structure observation with an optical microscope. The results are shown in Table 1.
  • Fig. 1 shows a structure photograph of the alloy powder No. 1 through an optical microscope.
  • Alloy powder No. 5 was prepared under the same conditions as the alloy powder No. 1. In this case, however, no Cu-8wt.%P was added to the molten metal of the aluminum alloy.
  • the as-obtained alloy powder was classified in -42 to -80 meshes (particle sizes of 175 to 350 ⁇ m), and thereafter sizes of primary crystal silicon particles contained in the powder were measured through structure observation with an optical microscope. The results are shown in Table 1.
  • Fig. 2 shows a structure photograph of the alloy powder No. 5 through an optical microscope.
  • a molten metal of an aluminum alloy having the same composition as the alloy powder No. 1 was held at a temperature of 950°C, and Cu-8wt.%P was added to attain the content of phosphorus shown in Table 1. This molten metal was held at the temperature of 950°C for 1 hour, and thereafter cast in a metal mold of 30 mm in diameter by 80 mm in height, to prepare an alloy casting (No. 6).
  • Fig. 3 shows a structure photograph of the alloy casting through an optical microscope.
  • the alloy powder samples No. 1 and No. 5 obtained in Example 1 and Comparative Example 1 were classified in -42 meshes (particle sizes of not more than 350 ⁇ m), and cold-preformed in sizes of 30 mm in diameter by 80 mm in height at a pressure of 3 ton/cm2. Thereafter these consolidated compacts were hot worked into round bars of 10 mm in diameter at an extrusion temperature of 450°C at an extrusion ratio of 10.
  • the alloy casting sample No. 6 obtained in Comparative Example 1A was also extruded into a round bar of 10 mm in diameter in a similar manner.
  • the as-obtained alloy powder samples were classified in -100 meshes (particle sizes of not more than 147 ⁇ m), and thereafter sizes of primary crystal silicon particles contained in the powder samples were measured through structure observation with an optical microscope. The results are shown in Table 3.
  • Alloy powder samples No. 16 to No. 18 were prepared under the same conditions as the alloy powder samples No. 11 to No. 15. In this case, however, aluminum alloy ingots containing no phosphorus were employed.
  • the as-obtained alloy powder samples were classified in -100 meshes (particle sizes of not more than 147 ⁇ m), and sizes of primary crystal silicon particles contained in the powder samples were measured through micro-structure observation with an optical microscope. The results are shown in Table 3. Table 3 Alloy No.
  • the alloy powder samples No. 11 to No. 18 obtained in Example 2 and Comparative Example 2 were classified in - 100 meshes (particle sizes of not more than 147 ⁇ m), and thereafter cold-preformed into sizes of 30 mm in diameter by 80 mm in height at a pressure of 3 ton/cm2. Thereafter these consolidated compacts were hot worked into flat plates of 20 mm in width by 4 mm in thickness at an extrusion temperature of 450°C at an extrusion ratio of 10.
  • the flat plate extruded materials obtained in the above manner were T6 treated, and thereafter subjected to measurement of transverse rupture strength on the basis of JISZ2203 with a gauge length of 30 mm. The results are shown in Table 4. Table 4 Alloy Powder Transverse Rupture Strengths (kg/mm 2) Example No. 11 79.9 12 80.3 13 67.0 14 73.1 15 71.6 Comparative Example 16 72.2 17 66.9 18 65.0
  • hyper-eutectic aluminum-silicon alloys were prepared from ingots: A-17: 2024 ingot + 17wt.%Si A-20: 2024 ingot + 20wt.%Si A-25: 2024 ingot + 25wt.%Si B-25: 2024 ingot + 25wt.%Si + 5wt.%Fe C-25: 2024 ingot + 25wt.%Si + 5wt.%Fe + 2wt.%Ni D-25: Al + 25wt.%Si + 2.5wt.%Cu + 1wt.%Mg + 0.5wt.%Fe + 0.5wt.%Mn E-25: Al ingot of 99.9 % purity + 25wt.%Si Molten metals of the aforementioned respective alloys were inoculated with phosphorus at the rates shown in Table 5 or inoculated with no phosphorus, atomized under conditions of air pressures of 5 to 10 kg/mm2 by open air atomizing, and quench-solidified
  • Table 5 shows relations between powder grain sizes D p and the maximum particle sizes D si of Si primary crystals as the results of deciding particle sizes of silicon primary crystals contained in these alloy powder samples with a image analysis microscope.
  • Fig. 4 shows the metallographic structure of hyper-eutectic aluminum-silicon alloy powder obtained by inoculating the aforementioned A-25 alloy with phosphorus with an optical microphotograph of 400 magnifications.
  • Fig. 5 similarly shows the metallographic structure of hyper-eutectic aluminum-silicon alloy powder obtained by inoculating the aforementioned alloy A-25 with no phosphorus. Referring to Figs. 4 and 5, dark gray portions show silicon primary crystals, pale gray portions show matrix, and black portions show holes and filled resin parts.
  • the two types of powder samples obtained by inoculating the aforementioned A-25 alloys with phosphorus and with no phosphorus were cold-formed at pressure with no classification. These compacts were degassed and heated at a temperature of 450°C for 30 minutes. The compacts were preheated at the same temperature, thereafter forged/formed at a surface pressure of 6 ton/cm2, and subjected to T6 heat treatment.
  • the hyper-eutectic aluminum-silicon alloy powder samples obtained in relation to the aforementioned A-25 alloy were classified through the maximum particle sizes of silicon primary crystals D si .
  • the respective classified powder samples were subjected to measurement of tensile strength of solidified bodies of the respective powder samples prepared under the same conditions as the above at the room temperature. The results of the measurement are shown in Fig. 6.
  • a consolidate or hot worked product prepared from the inventive hyper-eutectic aluminum-silicon alloy powder has extremely superior machinability and mechanical strength. Thus, it is usefully applied to various parts for machine structural use.
  • the inventive method of preparing hyper-eutectic aluminum-silicon alloy powder further, it is possible to refine and homogenize primary crystal silicon contained in the hyper-eutectic aluminum-silicon alloy powder, thereby remarkably reducing dependency of the particle size of the primary crystal silicon on the powder grain size as compared with the prior art. As the result, it is possible to prepare consolidates of powder which is improved in mechanical properties as compared with the prior art with a high yield.

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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.

Claims (12)

  1. Poudre d'alliage d'aluminium-silicium hypereutectique comprenant au moins 12 % en poids et pas plus de 50 % en poids de silicium, caractérisée par au moins 0,0005 % en poids, et pas plus de 0,1 % en poids de phosphore, et une granulométrie cristalline de silicium de cristal primaire dans la poudre d'alliage d'au moins 1 µm et pas plus de 10 µm.
  2. Poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 1, contenant au moins 0,0005 % en poids et pas plus de 0,05 % en poids de phosphore.
  3. Poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 1, contenant au moins 0,02 % en poids et pas plus de 0,1 % en poids de phosphore.
  4. Poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 1, 2 ou 3, contenant au moins 2,0 % en poids et pas plus de 3,0 % en poids de cuivre, au moins 0,5 % en poids et pas plus de 1,5 % en poids de magnésium, au moins 0,2 % en poids et pas plus de 0,8 % en poids de manganèse et au moins 0,0005 % en poids et pas plus de 0,05 % en poids de phosphore, avec un reste d'aluminium et d'impuretés inévitables.
  5. Procédé pour la préparation de la poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 1, comprenant :
       une étape de préparation d'un métal en fusion d'alliage d'aluminium-silicium hypereutectique contenant du phosphore ; et
       une étape d'atomisation du métal en fusion avec de l'air ou un gaz inerte et la solidification rapide de celui-ci, dans lequel
       l'étape de préparation d'un métal en fusion d'un alliage d'aluminium-silicium comprend une étape d'addition d'un affineur de silicium cristallin primaire contenant du phosphore au métal en fusion de l'alliage d'aluminium-silicium.
  6. Procédé pour la préparation d'une poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 1, comprenant :
       une étape de préparation d'un métal en fusion d'un alliage d'aluminium-silicium hypereutectique contenant du phosphore ; et
       une étape d'atomisation du métal en fusion avec de l'air ou un gaz inerte et la solidification rapide de celui-ci, dans lequel
       l'étape de préparation d'un métal en fusion d'un métal d'aluminium-silicium comprend l'étape de fusion d'un corps solide d'un alliage d'aluminium-silicium contenant préalablement un affineur de silicium cristallin primaire contenant du phosphore.
  7. Procédé pour la préparation de la poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 5 ou 6, dans lequel l'étape d'atomisation du métal en fusion et la solidification-trempe de celui-ci comprend l'étape d'atomisation du métal en fusion dans un état maintenu à une température d'au moins un niveau dépassant la température liquide de l'alliage d'aluminium-silicium de 100°C et pas plus de 1300°C.
  8. Procédé pour la préparation d'une poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 7, dans lequel l'étape d'atomisation du métal en fusion et de la solidification-trempe de celui-ci comprend une étape d'atomisation du métal en fusion après avoir maintenu celui-ci à une température d'au moins un niveau dépassant la température liquide de l'alliage aluminium-silicium de 100°C et pas plus de 1300°C.
  9. Procédé pour la préparation de la poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 5 ou 6, comprenant de plus :
       une étape de sélection de la poudre d'alliage ne dépassant pas 400 µm de taille particulaire.
  10. Procédé pour la préparation de la poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 9, dans lequel l'étape de sélection de la poudre d'alliage comprend une étape de sélection de la poudre d'alliage ne dépassant pas 200 µm de taille particulaire.
  11. Procédé pour la préparation de la poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 9, dans lequel l'étape de sélection de la poudre d'alliage comprend une étape de sélection de la poudre d'alliage ne dépassant pas 100 µm de taille particulaire.
  12. Procédé pour la préparation de la poudre d'alliage d'aluminium-silicium hypereutectique selon la revendication 9, dans lequel l'étape de sélection de la poudre d'alliage comprend une étape de sélection de la poudre d'alliage ne dépassant pas 50 µm de taille particulaire.
EP91918937A 1990-10-31 1991-10-31 Poudre a base d'un alliage aluminium/silicium hypereutectique et production de cette poudre Expired - Lifetime EP0592665B1 (fr)

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Application Number Priority Date Filing Date Title
JP29509990 1990-10-31
JP295018/90 1990-10-31
JP29501890 1990-10-31
JP295099/90 1990-10-31
JP295019/90 1990-10-31
JP29501990 1990-10-31
PCT/JP1991/001488 WO1992007676A1 (fr) 1990-10-31 1991-10-31 Poudre a base d'un alliage aluminium/silicium hypereutectique et production de cette poudre

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EP0592665A4 EP0592665A4 (fr) 1993-11-19
EP0592665A1 EP0592665A1 (fr) 1994-04-20
EP0592665B1 true EP0592665B1 (fr) 1996-06-12

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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)
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

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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
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
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

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Publication number Publication date
DE69120299D1 (de) 1996-07-18
EP0592665A1 (fr) 1994-04-20
WO1992007676A1 (fr) 1992-05-14
DE69120299T2 (de) 1997-01-23
EP0592665A4 (fr) 1993-11-19

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