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WO2024142830A1 - Matériau de forgeage d'alliage d'aluminium, produit forgé en alliage d'aluminium et leur procédé de fabrication - Google Patents

Matériau de forgeage d'alliage d'aluminium, produit forgé en alliage d'aluminium et leur procédé de fabrication Download PDF

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WO2024142830A1
WO2024142830A1 PCT/JP2023/043832 JP2023043832W WO2024142830A1 WO 2024142830 A1 WO2024142830 A1 WO 2024142830A1 JP 2023043832 W JP2023043832 W JP 2023043832W WO 2024142830 A1 WO2024142830 A1 WO 2024142830A1
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aluminum alloy
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PCT/JP2023/043832
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Japanese (ja)
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卓也 荒山
佳文 木村
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株式会社レゾナック
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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
    • 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
    • C22C21/06—Alloys based on aluminium with magnesium 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
    • C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
    • 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

Definitions

  • the present invention relates to an aluminum alloy material for forging, an aluminum alloy forging, and a method for producing the same.
  • iron-based materials were used exclusively for automobile parts, particularly suspension parts.
  • aluminum or aluminum alloy materials primarily for the purpose of reducing weight.
  • Zr is effective in preventing recrystallization, it has the following problems.
  • Zr forms compounds with Al-Ti-B based alloys. These compounds accumulate at the bottom of the furnace in which the molten alloy is stored, contaminating the furnace. In addition, these compounds also crystallize out as coarse particles in the produced ingot, reducing its strength.
  • Aspect 1 of the present invention is a composition in which Cu is in the range of 0.25 mass% or more and 0.55 mass% or less, Mg is in the range of 0.60 mass% or more and 1.25 mass% or less, Si is in the range of 0.90 mass% or more and 1.4 mass% or less, Mn is in the range of 0.35 mass% or more and 0.60 mass% or less, Fe is in the range of 0.15 mass% or more and 0.30 mass% or less, Zn is in the range of 0.25 mass% or less, Cr is in the range of 0.050 mass% or more and 0.30 mass% or less, Ti is in the range of 0.01 mass% or more and 0.1 mass% or less, and B is in the range of 0.0010 mass% or less.
  • the aluminum alloy forging material is composed of an aluminum alloy having an alloy composition containing 0.030% by mass or more, 0.0010% by mass or more and 0.050% by mass or less of Zr, a ratio of the Fe content to the Mn content Fe/Mn of 0.3 to 1.2 by mass, and the balance being Al and unavoidable impurities, and has a post-cast electrical conductivity of 25% IACS to 35% IACS and a Rockwell hardness HRF of 62 to 82.
  • Aspect 3 of the present invention is a steel sheet having a Cu content in the range of 0.25 mass% or more and 0.55 mass% or less, a Mg content in the range of 0.60 mass% or more and 1.25 mass% or less, a Si content in the range of 0.90 mass% or more and 1.4 mass% or less, a Mn content in the range of 0.35 mass% or more and 0.60 mass% or less, a Fe content in the range of 0.15 mass% or more and 0.30 mass% or less, a Zn content in the range of 0.25 mass% or less, a Cr content in the range of 0.050 mass% or more and 0.30 mass% or less, a Ti content in the range of 0.01 mass% or more and 0.1 % or less by mass, B in the range of 0.0010% by mass or more and 0.030% by mass or less, Zr in the range of 0.0010% by mass or more and 0.050% by mass or less, a ratio of the Fe content to the Mn content (Fe/Mn) of less
  • FIG. 1 is a perspective view showing an example of an aluminum alloy forging according to an embodiment of the present invention.
  • FIG. FIG. 2 is a plan view showing another example of an aluminum alloy forged product according to an embodiment of the present invention.
  • FIG. 2 is a perspective view showing yet another example of an aluminum alloy forged product according to an embodiment of the present invention.
  • 1 is a cross-sectional view showing an example of the vicinity of a mold of a horizontal continuous casting apparatus for producing an aluminum alloy forging according to an embodiment of the present invention.
  • 5 is an enlarged cross-sectional view of a main portion near a cooling water cavity of the horizontal continuous casting machine shown in FIG. 4.
  • FIG. 2 is an explanatory diagram illustrating a heat flux in a cooling wall portion of a horizontal continuous casting apparatus.
  • FIG. 2 is a plan view showing the position at which the central portion was sampled from the aluminum alloy forging obtained in this example for preparing a test piece for evaluating mechanical properties.
  • FIG. 2 is a plan view showing a test
  • an aluminum alloy forging material contains Cu in the range of 0.25 mass% or more and 0.55 mass% or less, Mg in the range of 0.60 mass% or more and 1.25 mass% or less, Si in the range of 0.90 mass% or more and 1.4 mass% or less, Mn in the range of 0.35 mass% or more and 0.60 mass% or less, Fe in the range of 0.15 mass% or more and 0.30 mass% or less, Zn in the range of 0.25 mass% or less, Cr in the range of 0.050 mass% or more and 0.30 mass% or less, Ti in the range of 0.01 mass% or more and 0.02 mass% or less, and Zn in the range of 0.03 mass% or more and 0.04 mass% or less.
  • An aluminum alloy forging material has Cu in the range of 0.25% by mass or more and 0.55% by mass or less, Mg in the range of 0.60% by mass or more and 1.25% by mass or less, Si in the range of 0.90% by mass or more and 1.4% by mass or less, Mn in the range of 0.35% by mass or more and 0.60% by mass or less, Fe in the range of 0.15% by mass or more and 0.30% by mass or less, Zn in the range of 0.25% by mass or less, Cr in the range of 0.050% by mass or more and 0.30% by mass or less, Ti in the range of 0.01% by mass or more and 0.1% by mass or less, and the range below, B in the range of 0.0010% by mass or more and 0.030% by mass or less, Zr in the range of 0.0010% by mass or more and 0.050% by mass or less, a ratio of the Fe content to the Mn content Fe/Mn being 0.3 to 1.2 in mass ratio, with the balance
  • the electrical conductivity of the aluminum alloy forging material of the above embodiment is 25% IACS or more and 35% IACS or less. This electrical conductivity is the electrical conductivity at room temperature, which is about 20°C ⁇ 15°C. If the electrical conductivity is less than 25% IACS, the material will be too hard and its workability will decrease, whereas if it exceeds 35% IACS, the material will be too soft, resulting in poor machinability (ability to break away chips), and the guaranteed strength of the final product may not be satisfied.
  • the Rockwell hardness HRF of the aluminum alloy forging material of the above embodiment is 62 or more and 82 or less.
  • the Rockwell hardness HRF is a value measured in accordance with JIS Z2245:2016 "Rockwell hardness test - Test method". This is because the workability is good if the Rockwell hardness HRF is within this range. That is, if the Rockwell hardness HRF is less than 62, the material is too soft, resulting in poor machinability (chip breakability) and inability to satisfy the guaranteed strength of the final product, while if it exceeds 82, the material is too hard, resulting in poor workability.
  • the aluminum alloy forged product of this embodiment has an impact value of 10 J/cm 2 or more at room temperature.
  • the size of precipitates containing Mn within 2.0 ⁇ m, including grain boundaries is 0.5 ⁇ m or less.
  • the aluminum alloy forgings of this embodiment correspond to 6000 series aluminum alloy forgings in that they contain Mg and Si.
  • Cu has the effect of finely dispersing Mg-Si compounds in the aluminum alloy and the effect of improving the tensile strength of the aluminum alloy by precipitating as Al-Cu-Mg-Si compounds including the Q phase.
  • the mechanical properties of the aluminum alloy forging 1a at room temperature can be improved.
  • Mg has the effect of improving the tensile strength of the aluminum alloy.
  • Mg contributes to strengthening the aluminum alloy by dissolving in the aluminum parent phase or precipitating as Mg-Si compounds (Mg 2 Si) such as the ⁇ ′′ phase, or Al-Cu-Mg-Si compounds (AlCuMgSi) such as the Q phase.
  • Mg 2 Si also has the effect of suppressing the formation of CuAl 2 phase in the aluminum alloy. By suppressing the formation of CuAl 2 phase, the corrosion resistance of the aluminum alloy forging 1a is improved. By keeping the Mg content within the above range, it is possible to improve the corrosion resistance as well as the mechanical properties at room temperature of the aluminum alloy forging 1a.
  • Si 0.90 mass% or more, 1.4 mass% or less
  • Si has the effect of improving the mechanical properties and corrosion resistance of the aluminum alloy forging 1a at room temperature.
  • coarse primary crystal Si grains may crystallize, which may reduce the tensile strength of the aluminum alloy.
  • Mn 0.35 mass% or more, 0.60 mass% or less
  • Mn has the effect of improving the tensile strength of the aluminum alloy by forming fine granular precipitates containing intermetallic compounds such as Al-Mn-Fe-Si and Al-Mn-Cr-Fe-Si in the aluminum alloy.
  • the Mn content is within the above range, the mechanical properties of the aluminum alloy forging 1a at room temperature can be improved.
  • FIG. 3 is a plan view of yet another example of an aluminum alloy forged product according to an embodiment of the present invention.
  • the aluminum alloy forging 1c shown in Fig. 3 has three connecting portions 4f, 4g, and 4h.
  • the connecting portions 4f and 4g are connected to each other by the long portion 2, and the connecting portions 4f and 4h are connected to each other by the long portion 2.
  • a through hole is provided in the connecting portion 4f.
  • This aluminum alloy forging 1b can be used as, for example, an A-type suspension arm.
  • Cu is in the range of 0.25 mass% or more and 0.55 mass% or less
  • Mg is in the range of 0.60 mass% or more and 1.25 mass% or less
  • Si is in the range of 0.90 mass% or more and 1.4 mass% or less
  • Mn is in the range of 0.35 mass% or more and 0.60 mass% or less
  • Fe is in the range of 0.15 mass% or more and 0.30 mass% or less
  • Zn is in the range of 0.25 mass% or less
  • Cr is in the range of 0.050 mass% or more and 0.30 mass% or less
  • Ti is 0.01 mass% and 0.1% by mass or less
  • B in the range of 0.0010% by mass or more and 0.030% by mass or less
  • Zr in the range of 0.0010% by mass or more and 0.050% by mass or less
  • a ratio of the Fe content to the Mn content Fe/Mn is 0.3 to 1.2 in mass ratio
  • the balance is Al and unavoidable impurities.
  • the molten metal receiving section 11 is composed of a molten metal inlet section 11a that receives the molten aluminum alloy M obtained in the above-mentioned molten metal forming process, a molten metal holding section 11b, and an outlet section 11c into the hollow section 21 of the mold 12.
  • the molten aluminum alloy M held in the molten metal holding portion 11b in the molten metal receiving portion 11 is poured into the hollow portion 21 of the mold 12 through the pouring passage 13a provided in the refractory plate body 13.
  • the molten aluminum alloy M supplied into the hollow portion 21 is then cooled and solidified by the cooling device 23 described below, and is drawn out from the other end side 12b of the mold 12 as an aluminum alloy rod B, which is a solidified ingot.
  • the elevation angle is less than 0°, when the aluminum alloy rod B is pulled out of the mold 12, it encounters resistance at the other end 12b, which is the mold outlet, and casting may become difficult.
  • the elevation angle exceeds 3°, the contact of the inner peripheral surface 21a with the molten aluminum alloy M may become insufficient, and the effect of removing heat from the molten aluminum alloy M and its solidified shell to the mold 12 may decrease, resulting in insufficient solidification.
  • a remelted skin may appear on the surface of the aluminum alloy rod B, or unsolidified molten aluminum alloy M may erupt from the end of the aluminum alloy rod B, which is not preferable, as this may lead to casting problems.
  • the inner surface 21a of the mold 12 is cooled by the cooling water W contained in the cooling water cavity 24, which removes heat from the molten aluminum alloy M filling the hollow portion 21 of the mold 12 from the surface in contact with the inner surface 21a of the mold 12, forming a solidified shell on the surface of the molten aluminum alloy M.
  • the mold 12 is formed so that the thickness t of the cooling wall 27 of the mold 12, i.e., the distance between the inner bottom surface 24a of the cooling water cavity 24 and the inner peripheral surface 21a of the hollow portion 21 of the mold 12, is within a range of, for example, 0.5 mm to 3.0 mm, and preferably 0.5 mm to 2.5 mm.
  • the material for forming the mold 12 is selected so that the thermal conductivity of at least the cooling wall 27 of the mold 12 is within a range of 100 W/m ⁇ K to 400 W/m ⁇ K.
  • the aluminum alloy rod B is pulled out at a constant speed by a pull-out drive device (not shown) installed near the other end 12b of the mold 12, so that it is cast continuously to form a long aluminum alloy rod B.
  • the pulled aluminum alloy rod B is then cut to the desired length, for example, by a synchronous cut-off machine (not shown).
  • composition ratio of the cast aluminum alloy rod B can be confirmed, for example, by a method using a photoelectric emission spectrophotometric analyzer (example: Shimadzu PDA-5500, manufactured by Japan) as described in "JIS H 1305.”
  • the lubricating oil supply rate is preferably 0.05 mL/min to 5 mL/min (more preferably 0.1 mL/min to 1 mL/min). If the supply rate is too low, the molten aluminum alloy M of the aluminum alloy rod B may not solidify and may leak from the mold 12 due to insufficient lubrication. If the amount of supply is excessive, the excess may be mixed into the aluminum alloy bar B and cause internal defects.
  • the casting speed which is the speed at which the aluminum alloy rod B is pulled out of the mold 12, is preferably 200 mm/min or more and 1500 mm/min or less (more preferably 400 mm/min or more and 1000 mm/min or less). This is because, at a casting speed within this range, the network structure of the crystals formed by casting becomes uniform and fine, which increases the resistance of the aluminum matrix to deformation at high temperatures and improves the high-temperature mechanical strength.
  • the amount of cooling water sprayed from the shower opening 25a of the cooling water spray passage 25 is preferably 10 L/min or more and 50 L/min or less (more preferably 25 L/min or more and 40 L/min or less) per mold. If the amount of cooling water is less than this, the molten aluminum alloy M may not solidify and may leak from the mold 12. In addition, the surface of the cast aluminum alloy bar B may remelt, forming an uneven structure that may remain as an internal defect. On the other hand, if the amount of cooling water is more than this range, the mold 12 may lose too much heat, causing it to solidify midway.
  • the average temperature of the molten aluminum alloy M flowing from the molten metal receiving portion 11 into the mold 12 is, for example, preferably 650°C or higher and 750°C or lower (more preferably 680°C or higher and 720°C or lower). If the temperature of the molten aluminum alloy M is too low, there is a risk that coarse crystals will form in the mold 12 or in front of it and will be incorporated into the aluminum alloy bar B as internal defects. On the other hand, if the temperature of the molten aluminum alloy M is too high, a large amount of hydrogen gas will be easily incorporated into the molten aluminum alloy M, which will be incorporated into the aluminum alloy bar B as porosity and may cause internal cavities.
  • the cooling wall portion 27 of the mold 12 is configured so that the heat flux value per unit area is 10 ⁇ 10 5 W/m 2 or more, thereby making it possible to prevent seizure of the cast aluminum alloy bar B. In addition, it is preferable that the heat flux value per unit area is 50 ⁇ 10 5 W/m 2 or less.
  • the aluminum alloy rod B thus obtained is cooled and solidified under conditions where the heat flux value per unit area in the cooling wall 27 is 10 ⁇ 10 5 W/m 2 or more, thereby suppressing adhesion of reaction products, such as carbides, caused by contact between the lubricating oil gas and the molten aluminum alloy M. This makes it unnecessary to cut and remove carbides, etc., on the surface of the aluminum alloy rod B, and allows the aluminum alloy rod B to be produced with a high yield.
  • Molds are generally made of metal components with good thermal conductivity, and have a hollow structure to allow the introduction of a coolant inside.
  • the mold used in this embodiment is appropriately selected from metals such as copper and aluminum, or graphite, from the viewpoint of heat transfer performance and durability at the contact point with the molten metal.
  • the header is generally made of a refractory material and is installed on the upper side of the mold. There are no particular restrictions on the material and size of the header, and it can be appropriately selected depending on the composition range of the alloy to be cast and the dimensions of the cast product.
  • the casting method described above makes it possible to obtain a uniform metal structure even in medium to large castings.
  • the forging process is a process in which the aluminum alloy casting after casting is cut to a predetermined size, the obtained forging material is heated to a predetermined temperature, and then pressure is applied by a press machine to mold it into a die.
  • the forging process is performed without performing the homogenization process that was conventionally performed after casting to remove segregation. Therefore, since it is necessary to perform the segregation removal performed by the homogenization process by heating the material during forging, it is necessary to perform the heating at a temperature of 500°C or higher and below the melting point. Then, the forging process is performed to obtain a forged product (for example, a suspension arm part of an automobile).
  • the material heating temperature during forging is less than 500°C, compounds such as AlFeSi and Mg 2 Si in the alloy structure remain in a segregated state, the deformation resistance increases, making it impossible to perform sufficient processing, and cracks occur. Furthermore, if the temperature exceeds the melting point, defects such as eutectic melting are likely to occur.
  • the forged product is subjected to solution treatment by holding it at a treatment temperature of 530°C or more and 560°C or less for 0.3 or more and 3 hours or less.
  • the heating rate from room temperature to the above-mentioned treatment temperature is preferably 5.0°C/min or more. If the treatment temperature is less than 530°C, the solute elements may not be dissolved in solid solution. On the other hand, if the treatment temperature exceeds 560°C, the solute elements may be dissolved in solid solution more, but eutectic melting and recrystallization may occur easily. In addition, if the heating rate is less than 5.0°C/min, Mg 2 Si may precipitate coarsely. On the other hand, if the treatment temperature is less than 530°C, the solution treatment may not proceed, making it difficult to achieve high strength by aging precipitation.
  • the quenching process is a process in which the forged product in the solid-solution state obtained in the solution treatment process is rapidly cooled to form a supersaturated solid solution.
  • the forged product is placed in a water tank that stores water (quenching water) and quenched by submerging the forged product.
  • the temperature of the water in the tank is preferably 20°C or higher and 60°C or lower.
  • the forged product is preferably placed in the water tank for 5 seconds or higher and 60 seconds or lower after solution treatment so that all surfaces of the forged product are in contact with water.
  • the submersion time of the forged product varies depending on the size of the casting, but is, for example, between more than 1 minute and 30 minutes.
  • the aging treatment process is a process in which the forged product is heated and held at a relatively low temperature to precipitate the elements that are supersaturated in solid solution, thereby imparting an appropriate hardness.
  • a method for producing an aluminum alloy forged product further includes, between the casting step and the forging step, a homogenization heat treatment step in which the aluminum alloy cast product is subjected to homogenization heat treatment by holding the aluminum alloy cast product at a temperature range of 370° C. or higher and 560° C. or lower for 2 hours or higher and 10 hours or lower.
  • the method for producing an aluminum alloy forged product of this embodiment differs from the method for producing an aluminum alloy forged product of the above-described embodiment in that it includes a homogenization heat treatment step.
  • Examples 1 to 8 and Comparative Examples 1 to 3 (Production of continuous cast products) First, an aluminum alloy having the alloy composition (the balance being aluminum) shown in the following Table 1 was prepared. A continuous cast product having a circular cross section and a diameter of 82 mm was produced from the prepared aluminum alloy.
  • ⁇ Conductivity (%IACS)> The conductivity was measured at room temperature. (Judgment criteria) "Good”: 25% IACS or more and 35% IACS or less. “X”: Less than 25% IACS or more than 35% IACS.

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Abstract

L'invention propose un produit forgé en alliage d'aluminium contenant : 0,25 à 0,55 % en masse de Cu ; 0,60 à 1,25% en masse de Mg ; 0,95 à 1,4 % en masse de Si ; 0,35 à 0,60 % en masse de Mn ; 0,15 à 0,30 % en masse de Fe ; au plus 0,25 % en masse de Zn ; 0,050 à 0,30 % en masse de Cr ; 0,01 à 0,1 % en masse de Ti ; 0,0010 à 0,030 % en masse de B ; et 0,0010 à 0,050 % en masse de Zr, le rapport Fe/Mn étant inférieur à 1,4, le reste étant constitué d'Al et d'impuretés inévitables, la densité en nombre de précipités contenant du Mn à l'intérieur de 2,0 µm comprenant des joints de grains étant de 4/µm2 ou plus, et lorsque la fraction de joints de grains à angle élevé présentant une désoriorientation cristalline de 15° ou plus est de 27 % ou moins, la valeur d'impact à température ambiante est de 10 J/cm2 ou plus.
PCT/JP2023/043832 2022-12-27 2023-12-07 Matériau de forgeage d'alliage d'aluminium, produit forgé en alliage d'aluminium et leur procédé de fabrication WO2024142830A1 (fr)

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Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006274415A (ja) * 2005-03-30 2006-10-12 Kobe Steel Ltd 高強度構造部材用アルミニウム合金鍛造材
WO2007114078A1 (fr) * 2006-03-31 2007-10-11 Kabushiki Kaisha Kobe Seiko Sho Element forge d'alliage d'aluminium et son procede de production
WO2013114928A1 (fr) * 2012-02-02 2013-08-08 株式会社神戸製鋼所 Matériau d'alliage d'aluminium forgé et son procédé de fabrication
WO2015146654A1 (fr) * 2014-03-27 2015-10-01 株式会社神戸製鋼所 Matériau d'alliage d'aluminium forgé et son procédé de production
JP2021143374A (ja) * 2020-03-11 2021-09-24 昭和電工株式会社 アルミニウム合金鍛造品およびアルミニウム合金鍛造品の製造方法
JP2022093990A (ja) * 2020-12-14 2022-06-24 昭和電工株式会社 アルミニウム合金鍛造品およびアルミニウム合金鍛造品の製造方法
WO2023139960A1 (fr) * 2022-01-18 2023-07-27 株式会社レゾナック Produit forgé en alliage d'aluminium, et procédé de fabrication associé
JP2023161784A (ja) * 2022-04-26 2023-11-08 株式会社レゾナック アルミニウム合金鍛造品及びその製造方法

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006274415A (ja) * 2005-03-30 2006-10-12 Kobe Steel Ltd 高強度構造部材用アルミニウム合金鍛造材
WO2007114078A1 (fr) * 2006-03-31 2007-10-11 Kabushiki Kaisha Kobe Seiko Sho Element forge d'alliage d'aluminium et son procede de production
WO2013114928A1 (fr) * 2012-02-02 2013-08-08 株式会社神戸製鋼所 Matériau d'alliage d'aluminium forgé et son procédé de fabrication
WO2015146654A1 (fr) * 2014-03-27 2015-10-01 株式会社神戸製鋼所 Matériau d'alliage d'aluminium forgé et son procédé de production
JP2021143374A (ja) * 2020-03-11 2021-09-24 昭和電工株式会社 アルミニウム合金鍛造品およびアルミニウム合金鍛造品の製造方法
JP2022093990A (ja) * 2020-12-14 2022-06-24 昭和電工株式会社 アルミニウム合金鍛造品およびアルミニウム合金鍛造品の製造方法
WO2023139960A1 (fr) * 2022-01-18 2023-07-27 株式会社レゾナック Produit forgé en alliage d'aluminium, et procédé de fabrication associé
JP2023161784A (ja) * 2022-04-26 2023-11-08 株式会社レゾナック アルミニウム合金鍛造品及びその製造方法

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