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EP3170594B1 - Poudre d'alliage d'aluminium pour forgeage à chaud de composants coulissants, son procédé de production, produit forgé en alliage d'aluminium pour composant coulissant et son procédé de production - Google Patents

Poudre d'alliage d'aluminium pour forgeage à chaud de composants coulissants, son procédé de production, produit forgé en alliage d'aluminium pour composant coulissant et son procédé de production Download PDF

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Publication number
EP3170594B1
EP3170594B1 EP16194363.4A EP16194363A EP3170594B1 EP 3170594 B1 EP3170594 B1 EP 3170594B1 EP 16194363 A EP16194363 A EP 16194363A EP 3170594 B1 EP3170594 B1 EP 3170594B1
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Prior art keywords
aluminum alloy
sliding component
alloy
forged product
crystal grains
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German (de)
English (en)
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EP3170594A1 (fr
Inventor
Takumi Maruyama
Takafumi Fujii
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Resonac Holdings Corp
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Showa Denko KK
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • 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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
    • B22F2003/175—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging by hot forging, below sintering temperature
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • B22F2003/208—Warm or hot extruding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B22F2003/248—Thermal after-treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • the present invention relates to an aluminum alloy powder appropriate for an aluminum alloy forged product used as a component that slides at a high speed under a high temperature, such as an engine piston used in an internal combustion engine of a vehicle or the like, and particularly a forged product obtained by performing hot forging on a powder extruded material, and a method of producing the aluminum alloy powder. Furthermore, the present invention relates to an aluminum alloy forged product for a sliding component, which uses the aluminum alloy powder, and a method of producing the aluminum alloy forged product.
  • An engine piston of an internal combustion engine is a member which slides relative to a cylinder at a high speed under a high temperature, requires excellent wear resistance, requires strength, particularly excellent high-temperature strength, and also requires excellent seizure resistance.
  • an Al-Si-based alloy containing about 10 mass% or more of Si that is, an aluminum alloy having a eutectic composition to a hyper-eutectic composition with a high Si content, has a low coefficient of thermal expansion and excellent wear resistance and thus has been hitherto used as the material of a vehicle engine.
  • an atomization method an aluminum alloy powder having a fine and uniform structure due to rapid cooling solidification can be obtained, and the addition of a large amount of alloy elements is possible. That is, in the atomization method, molten aluminum alloy can be rapidly cooled to solidify at a high cooling rate of about 10 3 to 10 5 °C/s, and thus the diffusion of alloy constituent elements is suppressed during the solidification, thereby suppressing coarsening of crystal grains and precipitates. Furthermore, due to the suppression of the formation of equilibrium phases and metastable phases, the amount of solutionized alloy elements, particularly transition elements represented by Fe, Ni, and Mn can be increased.
  • Japanese Unexamined Patent Application, First Publication No. S63-266005 has proposed a method of producing, using an atomization method, a powder of an Al-Si-based aluminum alloy with a high Si content, which has a eutectic composition to a hyper-eutectic composition and contains a relatively large amount of transition elements such as Fe, Ni, and Mn added thereto, which are metals with high melting points, and using, as a material having wear resistance under high load for a vehicle engine or the like, a forged product, which is produced by performing compression molding, extrusion, and forging on the powder rapidly cooled and solidified according to the atomization method through a powder metallurgy method.
  • the present invention has been made taking the above-described circumstances into consideration as the background, and an object thereof is to provide an aluminum alloy powder for obtaining an aluminum alloy powder forged product having excellent wear resistance and high-temperature strength as a forged product for a sliding component used under high load, and an aluminum alloy forged product for a sliding member, which uses the aluminum alloy powder and has excellent wear resistance and high-temperature strength.
  • the inventors examined various cases, repeatedly conducted reviews, and found that, as for the characteristics of a forged product obtained by performing compression molding, extrusion, and hot forging on an Al-Si-based alloy powder obtained by an atomization method, in a case where Mn from among Fe, Ni, and Mn, which are transition elements, is added, compared to a case where Fe and Ni are added, considerably excellent wear resistance and high-temperature strength can be obtained even in the same addition amount. That is, it was found that in a sliding component used under high load, such as a vehicle engine piston, a case where Mn is added as a transition element is considerably superior to a case where Fe and Ni are added.
  • Mn has a lower melting point than Fe and Ni, the melting point of the molten alloy for atomization does not need to be increased.
  • Mn has a lower specific gravity than Fe and Ni, Mn is advantageous to the use for a vehicle engine piston which requires lightweight properties.
  • the present invention provides the following [1] to [4]:
  • an aluminum alloy powder forged product for a sliding component used under high load such as a vehicle engine piston
  • a forged product having excellent wear resistance and high-temperature strength can be obtained.
  • the aluminum alloy powder for hot forging of a sliding component of the present invention may include, if necessary, in addition to the essential components, or in addition to the essential components and Cu and Mn, one or two or more of Ti, Zr, V, W, Cr, Co, Mo, Ta, Hf, Nb, each of which being in a proportion of 0.01% to 5.0%.
  • % for each component means mass%.
  • Si is a basically important element for the aluminum alloy powder of the present invention, causes the crystallization of a large amount of crystallized Si (primary crystal Si and eutectic Si) as Si in Al-Si-based eutectic to hyper-eutectic regions is contained.
  • Si contributes to an improvement in wear resistance due to finely crystallized Si and contributes to an improvement in strength.
  • the amount of Si is less than 10%, the amount of crystallized Si is small, which causes a reduction in wear resistance and strength.
  • the amount of Si is more than 19%, coarse primary crystal Si is crystallized, which causes a reduction in strength and embrittlement of the material. Therefore, forgeability is degraded.
  • the amount of Si is set to be in a range of 10.0% to 19.0%.
  • the amount of Si is particularly preferably in a range of 12% to 16%.
  • Mn is a transition metal and thus forms intermetallic compounds, thereby contributing to the improvement of wear resistance and high-temperature strength through dispersion strengthening.
  • Fe or Ni may be added in order to improve the strength of an Al-Si-based alloy with a high Si content.
  • Mn rather than Fe and Ni is considerably effective in improving wear resistance.
  • Mn is cheap, an increase in material costs is not incurred unlike a case where expensive Ni is added.
  • Mn is less likely to be incorporated during melting of an alloy or the like, and thus strict control of the amount of Mn in the alloy is easily performed.
  • Mn has a lower melting point than those of Fe and Ni, there is no need to set the melting temperature of the molten alloy for atomization to be high.
  • Mn has a lower specific gravity than those of Fe and Ni, adding Mn rather than Fe and Ni is advantageous, and is particularly advantageous to the use of a vehicle engine piston that requires lightweight properties. From the viewpoint, in the present invention, Fe and Ni are not actively added, and by adding Mn, the improvement in wear resistance and high-temperature strength is achieved.
  • the amount of Mn when the amount of Mn is less than 3.0%, dispersion strengthening due to intermetallic compound cannot be sufficiently achieved.
  • the amount of Mn when the amount of Mn is more than 10.0%, on the contrary, hardness and wear resistance decrease, and there is a tendency for the material in a formed body to become brittle.
  • the amount of Mn is set to be in a range of 3.0% to 10.0%.
  • the amount of Mn is particularly preferably in a range of 6.0% to 8.0% in the above range.
  • Cu is an element effective in imparting age hardenability to an alloy in cooperation with Mg. Therefore, when Cu is added along with Mg, Cu effectively acts to perform a solutionizing treatment to quenching and an age hardening treatment on a forced material as a heat treatment type alloy, and to improve room-temperature and high-temperature strength.
  • the amount of Cu is set to be in a range of 0.5% to 10%.
  • the amount of Cu is particularly preferably in a range of 2.0% to 5.0% in the above range.
  • Mg is an element effective in imparting age hardenability to an alloy in cooperation with Cu as described above. Therefore, when Mg is added along with Cu, Mg effectively acts to perform a solutionizing treatment to quenching and an age hardening treatment on a forced material as a heat treatment type alloy, and to improve room-temperature and high-temperature strength.
  • the amount of Mg is set to be in a range of 0.2% to 3.0%.
  • the amount of Mg is particularly preferably in a range of 1.0% to 2.0% in the above range.
  • These elements all have low diffusion rates in aluminum and thus have effects of improving heat resistance of an alloy and significantly improving high-temperature strength.
  • the amount of any of the elements is less than 0.1%, the above-described effect is insufficiently obtained.
  • the amount thereof is more than 0.5%, there is a tendency for the material to become brittle. It is preferable that in a case where two or more of these elements are contained, the total amount thereof is 8.0% or less.
  • the average size of Si crystal grains in powder particles needs to be 15 ⁇ m or less.
  • Si crystal grains in the powder particles are crystal grains of a Si simple substance and includes both primary crystal Si and eutectic Si. In the Si crystal grains, primary crystal Si is likely to coarsen.
  • the average size of Si crystal grains in the material (forged product) after compression molding, extrusion, and hot forging can be easily limited to as fine as 15 ⁇ m or less.
  • the improvement in wear resistance, and the improvement in strength and high-temperature strength can be achieved.
  • the average size of Si crystal grains in the powder particles is more than 15 ⁇ m, Si crystal grains in the forged product after compression molding, extrusion, and hot forging become coarse, and it becomes difficult to sufficiently improve wear resistance, strength, and high-temperature strength.
  • the particle size of the aluminum alloy powder particles is not particularly limited, and typically, is preferably about 30 to 70 ⁇ m on average. When the average particle size thereof is less than 30 ⁇ m, the yield significantly decreases. When the average particle size thereof is more than 70 ⁇ m, there is concern that coarse oxides and foreign matter may be incorporated.
  • fine alloy powder which is formed of an Al-Si-based alloy with a high Si content as described above, contains a relatively large amount of Fe as an alloy element, has an average Si crystal grain size of 15 ⁇ m or less, and an average powder particle size of about 30 to 70 ⁇ m can be reliably obtained by using an atomization method. That is, the atomization method is a method of spraying molten aluminum alloy through a nozzle along with gas, rapidly cooling fine molten alloy particles at a cooling rate of about 10 2 to 10 5 °C/s, thereby obtaining solidified powder.
  • the aluminum alloy forged product for a sliding component according to the present invention is produced by performing compression molding on the aluminum alloy powder for hot forging of a sliding component described above, performing extrusion on the resultant, and thereafter performing hot forging on the resultant. Therefore, the composition of the forged product is the same as that of the alloy powder described above. Moreover, if necessary, in addition to the essential components, one or two or more of Ti, Zr, V, W, Cr, Co, Mo, Ta, Hf, Nb may be included, each of which being in a proportion of 0.01% to 5.0%. Next, the reason for limiting the alloy elements is the same as that described above.
  • the average size of Si crystal grains in the aluminum alloy forged product for a sliding component needs to be 15 ⁇ m or less.
  • Si crystal grains are crystal grains of a Si simple substance and include both primary crystal Si and eutectic Si. In the Si crystal grains, primary crystal Si is likely to coarsen.
  • the average size thereof is more than 15 ⁇ m and becomes coarse, it becomes difficult to sufficiently improve wear resistance, strength, and high-temperature strength.
  • the average size of Si crystal grains rarely changes. Therefore, when a powder in which the average size of Si crystal grains in the particles is 15 ⁇ m is used as the alloy powder as described above, the average size of Si crystal grains in the forged product after compression molding, extrusion, and hot forging can be 15 ⁇ m or less.
  • the overall concept of the process for producing the aluminum alloy forged product for a sliding component includes, as illustrated in FIG. 1 , a powder production step P1 of producing an alloy powder through an atomization method by melting an aluminum alloy, a forged product production step P2 of obtaining a forged product by performing compression molding on the alloy powder obtained in the powder production step P1 into a predetermined shape (for example, a cylindrical shape), and performing extrusion and hot forging on the resultant, and a heat treatment step P3 of performing a solutionizing treatment to quenching on a final forged product and performing an aging treatment wherein the aging treatment includes a temperature in a range of 180°C to 280°C and a time of 1 hour to 4 hours.
  • molten aluminum alloy of which the composition is adjusted as described above is produced according to a typical melting method (S11).
  • the obtained molten aluminum alloy is atomized into powder by using an atomization method (S12).
  • the atomization method is a method of spraying small liquid droplets of the molten alloy into mist through a spraying nozzle using a gas flow such as nitrogen gas to rapidly cool and solidify the small liquid droplets, thereby obtaining fine alloy powder.
  • a gas flow such as nitrogen gas
  • the alloy powder obtained by using the atomization method is classified by a sieve if necessary (S13), and only alloy powder with a size of less than 150 ⁇ m is sent to the subsequent process.
  • the alloy powder sent to the subsequent process in this step has the composition as described above, and the average size of Si crystal grains in the alloy powder particles needs to be 15 ⁇ m or less.
  • the alloy powder obtained as described above is heated to, for example, about 250°C to 300°C (S21), is inserted into a mold preheated to, for example, about 230°C to 270°C, is compression-molded into a predetermined shape (S22), thereby obtaining a compact.
  • the pressure of the compression molding is not particularly limited but is typically a pressure of about 0.5 to 3.0 ton/cm 2 , and the compact preferably has a relative density of about 60% to 90%.
  • the shape of the compact is not particularly limited, but typically, a cylindrical shape or a disk shape is preferable in consideration of the extrusion process.
  • the compact is subjected to machining such as face milling if necessary, is then subjected to a degassing treatment (S23), and is heated (S24) to be subjected to an extrusion process (S25).
  • the heating temperature (preheating temperature) before the extrusion is, for example, preferably about 300°C to 450°C.
  • the compact is loaded into an extrusion container, and receives a pressurization force from an extrusion ram, and is extruded, for example, into a round bar shape from an extrusion die. It is preferable that the extrusion container is also heated to about 300°C to 400°C in advance.
  • the round bar-shaped extruded body is cut into a predetermined depth if necessary (S26) and is thereafter heated to a temperature appropriate for hot forging (S27), thereby being subjected to hot forging (S28).
  • a temperature appropriate for hot forging S27
  • S28 hot forging
  • closed-die forging or half-closed-die forging is preferable so as to cause the finish forced material (forged product) to have a shape close to a product shape (for example, an engine piston shape).
  • a product shape for example, an engine piston shape
  • free forging may also be employed.
  • the temperature of the hot forging is preferably about 300°C to 450°C in a case of the alloy as an object of the present invention.
  • cold forging may be performed after the hot forging.
  • the finish forged material is subjected to a subsequent heat treatment step P3.
  • the solutionizing treatment is a treatment for forming supersaturated solid solutions of Cu, Mg, and the like, which contribute to age hardening.
  • the heating temperature of the solutionizing treatment is preferably 480°C to 500°C. When the heating temperature is lower than 480°C, supersaturated solid solutions cannot be sufficiently obtained, and age hardenability decreases. When the heating temperature is higher than 500°C, crystal grains or eutectic Si becomes coarse, and there are problems in that a reduction in strength is incurred or the growth of pores is promoted.
  • the heating time of the solutionizing treatment is preferably 2 hours to 4 hours. When the heating time is shorter than 2 hours, supersaturated solid solutions cannot be sufficiently obtained, and when the heating time is longer than 4 hours, coarsening of crystal grains or eutectic Si occurs.
  • quenching such as water quenching is performed to obtain a material in which supersaturated solid solutions of Cu, Mg, and the like are formed over the solid solubility limit at room temperature (supersaturated solid solutions).
  • the quenching temperature is preferably 0°C to 50°C. When the quenching temperature is lower than 0°C, there is concern that cracks may occur due to rapid thermal contraction, resulting in cracking. When the quenching temperature is higher than 50°C, supersaturated solid solutions are insufficiently obtained, and strength is insufficiently obtained.
  • an aging treatment is performed. Due to the aging treatment, intermetallic compounds of Cu, Mg, and the like are finely precipitated, and strength and wear resistance can be significantly improved.
  • the present invention is applied to the production of a sliding component represented by an engine piston, and the sliding component preferably requires good dimensional stability.
  • the sliding component preferably requires good dimensional stability.
  • the clearance from the inner circumferential surface of a cylinder is stably maintained.
  • the aging treatment preferably proceeds to a stabilization treatment in a so-called T7 treatment to achieve overaging which exceeds aging treatment conditions in a general T6 treatment (aging treatment conditions for obtaining maximum strength).
  • the conditions of the aging treatment include a temperature in a range of 180°C to 280°C and a time of 1 hour to 4 hours.
  • the aging treatment temperature is lower than 180°C, long-term aging is necessary, resulting in a reduction in production efficiency.
  • the aging treatment temperature is higher than 280°C, coarsening of crystal grains or eutectic Si occurs within a short period of time, and there is concern that strength may be decreased.
  • the aging time is shorter than 1 hour, overaging is not achieved such that stabilization becomes insufficient and sufficient dimensional stability is not obtained.
  • the aging time is longer than 4 hours, coarsening of crystal grains and eutectic Si occurs due to excessive overaging, and there is concern that strength may be decreased.
  • the forged product after the aging treatment described above is appropriately subjected to machining such as cutting, surface polishing, or the like, thereby completing a sliding component of a vehicle engine piston or the like.
  • Molten aluminum alloy with a high Si content and a composition shown as Nos. 1 to 12 of Table 1 was atomized with gas into powder, and the powder was classified by a sieve, thereby obtaining -100 mesh powder. It is assumed from the measurement results of the size of the Si crystal grains in a sample (forged product), the size of Si crystal grains in the particles of the powder was 15 ⁇ m or less.
  • the powder was preheated to a temperature of 280°C, was inserted into a mold heated and retained at the same temperature, and was subjected to compression molding at a pressure of 1.5 ton/cm 2 , thereby obtaining a disk-shaped compact having a diameter of 210 mm and a length of 250 mm.
  • the compact was subjected to face milling to a diameter of 203 mm to form a billet of the compact.
  • the compact billet was heated to 350°C, was inserted into an extrusion container having an inner diameter of 210 mm, which was heated and retained at 350°C, and was extruded at an extrusion ratio of 7.8 using a die having an inner diameter of 75 mm according to an indirect extrusion method.
  • FIG. 2 shows an extruded material 10 before forging and a forged product 20 after the forging.
  • a sample of 10 mm ⁇ 10mm was cut from the obtained sample (forged product) and was embedded in a resin. Thereafter, the resultant was subjected to rough polishing using emery paper and finish polishing using buff. The structure thereof was observed using an optical microscope, and the sizes of Si crystal grains were measured. As a result, it was confirmed that the size of Si crystal grains in any sample was 15 ⁇ m or less.
  • the obtained sample was heated to 490°C and retained for 3 hours as the solutionizing treatment and was thereafter subjected to quenching with water at 20°C. Thereafter, as the aging treatment (over-aging stabilization treatment), the resultant was heated at 220°C for 1 hour to obtain a T7 treatment product.
  • the obtained T7 treatment product was processed into a room-temperature tensile test piece having a gauge length of 25.4 mm and a parallel portion diameter of 2.85 mm, and a flanged high-temperature tensile test piece having a gauge length of 20 mm and a parallel portion diameter of 4 mm, and a tensile test was conducted at room temperature, 150°C, and 300°C.
  • No. 7 as the present invention example is compared to Nos. 9 to 12 in which the amount of Mn varies while the amount of Si is constant, Nos. 9 and 10 as the present invention examples had sufficient wear resistance and high-temperature strength.
  • No. 11 as the comparative example dispersion strengthening of Al-Mn-Si-based intermetallic compounds could not be sufficiently achieved, and the high-temperature strength thereof was not excellent.
  • No. 12 as the comparative example toughness was decreased due to an excessive amount of Mn and thus forgeability was decreased. Accordingly, cracking had occurred during quenching after the solutionizing treatment.
  • the forged product after being subjected to the heat treatments described above was cut to obtain an evaluation material (fixed piece) of 5 ⁇ 25 ⁇ 40 mm, and an Ogoshi wear test was conducted thereon.
  • SS400 was used as a mating material (rotating disk), and the rotating disk was pressed and rubbed against the fixed piece.
  • the wear amount and specific wear rate were calculated from a wear trace on the surface of the fixed piece.
  • the calculation results of the specific wear rate are shown in Table 2.
  • the wear amount was obtained using an approximation expression from the diameter and the thickness of the rotating disk and the width of the wear trace, and the specific wear rate was calculated from the obtained wear amount, the frictional distance, and the final load.
  • the wear amount is the amount of the evaluation material being worn
  • the specific wear rate is a value representing the amount of SS400 as the mating material being worn. As the specific wear rate decreases, better wear resistance is obtained.
  • Nos. 1, 2, and 5 as the comparative examples are compared to each other, it can be seen that No. 5 having a Si content of 20%, which was the maximum, had the lowest specific wear rate and good wear properties.
  • No. 5 is compared to No. 7 as the present invention example, it can be seen that while the specific wear rate was substantially the same, the material of the present invention had good wear properties.
  • Molten aluminum alloy with a high Si content and a composition shown as Nos. 13 to 17 of Table 1, that is, a non-heat-treatment type alloy composition was atomized into powder by using an atomization method, and the powder was classified by a sieve, thereby obtaining -100 mesh powder. It is assumed that even in the powder, the size of Si crystal grains in the particles of the powder was 15 ⁇ m or less.
  • Example 1 a compact billet obtained by performing compression molding and face milling as in Example 1 was subjected to hot extrusion, and the obtained extruded body was cut and subjected to hot free forging as in Example 1.
  • Example 2 In addition, in the case of Example 2, the heat treatments (the solutionizing treatment, quenching, and aging treatment) were not performed on the sample (forged product).
  • the materials of the present invention combine high-temperature strength, wear resistance, and forgeability and are appropriate for a sliding member used under high load, such as a vehicle engine piston.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)
  • Pistons, Piston Rings, And Cylinders (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Powder Metallurgy (AREA)

Claims (4)

  1. Poudre d'alliage d'aluminium pour le forgeage à chaud d'un composant coulissant, comprenant, en % en masse:
    Si: de 10,0 % à 19,0 %;
    Mn: de 3,0 % à 10,0 %;
    Cu: de 0,5 % à 10,0 %;
    Mg: de 0,2 % à 3,0 %;
    optionnellement un, deux ou plus de deux composants parmi Ti, Zr, V, W, Cr, Co, Mo, Ta, Hf et Nb, chacun dans une proportion de 0,01 % à 5 %; et
    le reste étant composé d'Al et d'impuretés inévitables,
    dans lequel une taille moyenne de grains de cristal de Si, qui est mesurée en observant la structure des grains de cristal de Si en utilisant un microscope optique, est de 15 µm, ou moins, et les impuretés inévitables composant le reste comprennent 1,0 %, ou moins, de Fe, et 1,0 %, ou moins, de Ni.
  2. Procédé de production de la poudre d'alliage d'aluminium pour le forgeage à chaud d'un composant coulissant selon la revendication 1, comprenant la production d'un alliage fondu présentant une composition selon la revendication 1, et le refroidissement rapide de l'alliage fondu afin de le solidifier et de le pulvériser en une poudre en utilisant un procédé de pulvérisation.
  3. Produit forgé en alliage d'aluminium pour un composant coulissant, qui est produit en exécutant un forgeage à chaud sur un matériau extrudé de la poudre d'alliage d'aluminium selon la revendication 1, comprenant, en % en masse:
    Si: de 10,0 % à 19,0 %;
    Mn: de 3,0 % à 10,0 %;
    Cu: de 0,5 % à 10,0 %; et
    Mg: de 0,2 % à 3,0 %;
    optionnellement un, deux ou plus de deux composants parmi Ti, Zr, V, W, Cr, Co, Mo, Ta, Hf et Nb, chacun dans une proportion de 0,01 % à 5,0 %; et
    le reste étant composé d'Al et d'impuretés inévitables,
    dans lequel une taille moyenne de grains de cristal de Si, qui est mesurée en observant la structure des grains de cristal de Si en utilisant un microscope optique, est de 15 µm, ou moins, et les impuretés inévitables composant le reste comprennent 1,0 %, ou moins, de Fe, et 1,0 %, ou moins, de Ni.
  4. Procédé de production du produit forgé en alliage d'aluminium pour un composant coulissant, le procédé comprenant:
    un procédé de moulage par compression pour exécuter un moulage par compression sur la poudre d'alliage d'aluminium pour le forgeage à chaud d'un composant coulissant selon la revendication 1, obtenant de ce fait un produit compact;
    un procédé d'extrusion pour exécuter une extrusion à chaud sur le produit compact obtenu, obtenant de ce fait un matériau extrudé; et
    un procédé de forgeage pour exécuter un forgeage à chaud sur le matériau extrudé, obtenant de ce fait un produit forgé qui présente une taille de grains de cristal de Si moyenne de 15 µm, ou moins,
    dans lequel la taille moyenne des grains de cristal de Si est mesurée en observant la structure des grains de cristal de Si en utilisant un microscope optique; et
    le procédé comprenant en outre l'exécution d'un traitement de mise en solution, d'une trempe et d'un traitement de vieillissement sur le produit forgé après le procédé de forgeage, dans lequel le traitement de vieillissement implique une température comprise dans une gamme de 180°C à 280°C et une durée de 1 heure à 4 heures.
EP16194363.4A 2015-10-21 2016-10-18 Poudre d'alliage d'aluminium pour forgeage à chaud de composants coulissants, son procédé de production, produit forgé en alliage d'aluminium pour composant coulissant et son procédé de production Not-in-force EP3170594B1 (fr)

Applications Claiming Priority (1)

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JP2015207274A JP2017078213A (ja) 2015-10-21 2015-10-21 摺動部品向け熱間鍛造用アルミニウム合金粉末、その製造方法、摺動部品用アルミニウム合金鍛造品、およびその製造方法

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JP6738212B2 (ja) * 2016-06-13 2020-08-12 昭和電工株式会社 アルミニウム合金鍛造品及びその製造方法
JP2019026859A (ja) * 2017-07-25 2019-02-21 昭和電工株式会社 高速動部品用アルミニウム合金鍛造品、およびその製造方法
JP7112275B2 (ja) * 2018-07-26 2022-08-03 三菱重工業株式会社 アルミニウム合金材料、アルミニウム合金材料の製造方法、キャスク用バスケット及びキャスク
CN111872404A (zh) * 2020-06-30 2020-11-03 同济大学 一种用于3d打印的铝铜合金粉末及其制备方法
CN112063899A (zh) * 2020-09-14 2020-12-11 肇庆新联昌金属实业有限公司 一种高塑性铝合金及其制备方法

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