WO2024159682A1 - 高强韧压铸铝硅合金及其制备方法和应用 - Google Patents

高强韧压铸铝硅合金及其制备方法和应用 Download PDF

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Publication number
WO2024159682A1
WO2024159682A1 PCT/CN2023/098373 CN2023098373W WO2024159682A1 WO 2024159682 A1 WO2024159682 A1 WO 2024159682A1 CN 2023098373 W CN2023098373 W CN 2023098373W WO 2024159682 A1 WO2024159682 A1 WO 2024159682A1
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Prior art keywords
strength
silicon alloy
die
cast aluminum
aluminum
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English (en)
French (fr)
Inventor
熊守美
臧永奕
刘文宁
葛素静
刘亦贤
刘永昌
万翱翔
田战峰
苑高利
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Hebei Xinlizhong Nonferrous Metals Group Co Ltd
Tsinghua University
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Hebei Xinlizhong Nonferrous Metals Group Co Ltd
Tsinghua University
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
    • 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
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master 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
    • C22C21/04—Modified aluminium-silicon alloys

Definitions

  • the present invention belongs to the technical field of metal alloy preparation, development and application, and specifically relates to a high-strength and toughness die-cast aluminum silicon alloy and a preparation method and application thereof.
  • Aluminum-silicon alloy has the advantages of low density, good fluidity, high specific strength and specific stiffness, and is widely used in automobile parts.
  • the traditional method of manufacturing automobile bodies is to first heat treat individual automobile parts to improve the comprehensive mechanical properties, and then weld or rivet several parts together.
  • the implementation of Tesla's integrated die-casting technology has greatly reduced the weight of the car and eliminated the welding or riveting process, which has improved efficiency while reducing manufacturing production costs.
  • thermal deformation and blistering will occur during heat treatment. Therefore, it is urgent to develop a die-cast aluminum-silicon alloy material that can maintain high strength and toughness in a non-heat-treated state.
  • the present disclosure aims to solve at least one of the technical problems in the related art to a certain extent.
  • the purpose of the present disclosure is to provide a high-strength and toughness die-cast aluminum-silicon alloy and a preparation method and application thereof.
  • the high-strength and toughness die-cast aluminum-silicon alloy has high yield strength, tensile strength and elongation, and exhibits excellent toughness.
  • the present disclosure provides a high-strength and toughness die-cast aluminum-silicon alloy.
  • the high-strength and toughness die-cast aluminum-silicon alloy includes: 8.0wt% to 10.0wt% silicon, 0.35wt% to 0.75wt% manganese, 0.05wt% to 0.15wt% chromium, 0.01wt% to 0.6wt% magnesium, 0.1wt% to 3.0wt% zinc, 0.01wt% to 0.1wt% vanadium, 0.01wt% to 0.1wt% molybdenum, 0.05wt% to 0.3wt% zirconium, 0.05wt% to 0.3wt% titanium, 0.02wt% to 0.07wt% strontium, no more than 0.2wt% iron, no more than 0.15wt% unavoidable inclusions, and the balance of aluminum.
  • the above-mentioned content range of each element is used to prepare Aluminum-silicon alloy is prepared, wherein iron is an inevitable impurity element, but is also a necessary element to ensure demolding, and iron in the die-cast aluminum-silicon alloy is easily combined with aluminum and silicon to form a relatively coarse primary iron-rich compound in the pressure chamber, which is a hard and brittle phase, easily splits the matrix, and reduces the mechanical properties.
  • the inventors found that adding molybdenum can refine the primary iron-rich phase, reduce its size, reduce its number, and transform its shape into a spherical shape.
  • molybdenum, manganese, chromium, and vanadium coordinate and optimize the primary iron-rich phase, thereby refining and spheroidizing the primary iron-rich phase, thereby improving the mechanical properties of the silicon-aluminum alloy; on the other hand, increasing the amount of zinc added can reduce the nucleation temperature of the primary ⁇ -Al phase, play a role in refining the primary ⁇ -Al grains, and achieve fine grain strengthening.
  • the present application comprehensively optimizes the die-cast aluminum silicon alloy structure through the overall adjustment of the content of each of the above elements, by achieving refinement and spheroidization of the primary iron-rich phase, refinement of the primary ⁇ -Al grains, and precipitation of the second phase strengthening, and prepares a die-cast aluminum silicon alloy with excellent performance, so that it has high strength and toughness in a non-heat-treated state, and can better meet the production and manufacturing needs of high-pressure casting thin-walled parts and integrated die-cast structural parts.
  • the yield strength of the silicon aluminum alloy rod specimen formed by each element with the above content ratio is 150MP ⁇ 180MPa
  • the tensile strength is 300MP ⁇ 350MPa
  • the elongation is 10% ⁇ 15%
  • the silicon aluminum alloy exhibits excellent strength and toughness.
  • the high-strength and toughness die-cast aluminum-silicon alloy according to the above embodiment of the present disclosure may also have the following technical features:
  • the high-strength and toughness die-cast aluminum-silicon alloy further includes no more than 0.01 wt % of calcium, thereby improving the strength and plasticity of the silicon-aluminum alloy.
  • the total mass of the vanadium and the molybdenum is 0.05 wt% to 0.15 wt%, preferably 0.1 wt%, thereby avoiding the precipitation of a coarse primary iron-rich phase.
  • the mass ratio of the zirconium to the titanium is (0.5-2):1, preferably 1:1.
  • the primary ⁇ -Al grains can be refined to achieve fine grain strengthening.
  • the present disclosure proposes a method for preparing the above-mentioned high-strength and toughness die-cast aluminum-silicon alloy. According to an embodiment of the present disclosure, the method comprises:
  • the high-strength and toughness die-cast aluminum-silicon alloy is obtained by mixing silicon, manganese, chromium, magnesium, zinc, vanadium, molybdenum, zirconium, titanium, strontium and aluminum within the above content range, smelting the mixture, casting and cutting the mixture, and then heating and melting the mixture and die-casting the mixture.
  • the addition of molybdenum can refine the primary iron-rich phase, and molybdenum, manganese, chromium and vanadium can coordinate with each other to refine and spheroidize the primary iron-rich phase.
  • the method of the present application can be used to prepare a die-cast aluminum-silicon alloy with high yield strength, tensile strength and elongation.
  • the method for preparing high-strength and toughness die-cast aluminum-silicon alloy according to the present disclosure may also have the following technical features:
  • step (2) the ingot is heated at a temperature of 730°C to 750°C.
  • the die-casting process parameters include: the casting temperature of the melt is 690°C to 710°C, the mold temperature is 140°C to 160°C, the vacuum degree inside the mold cavity is lower than 10kPa, the three-stage low-speed injection speed is 0.2-0.2-(0.2 to 0.4) m/s, the high-speed injection speed is 2.5m/s to 3.5m/s, the high-speed accumulator pressure value is 12.5MPa to 13.7MPa, and the boost accumulator pressure value is 12.5MPa to 13.7MPa.
  • the present disclosure proposes an aluminum-silicon alloy component.
  • the aluminum-silicon alloy component comprises the above-mentioned high-strength and toughness die-cast aluminum-silicon alloy or the high-strength and toughness die-cast aluminum-silicon alloy prepared by the above-mentioned method.
  • the aluminum-silicon alloy component has a long service life and excellent mechanical properties.
  • the present disclosure proposes the use of the high-strength and toughness die-cast aluminum-silicon alloy or the high-strength and toughness die-cast aluminum-silicon alloy prepared by the above method in the fields of automobile, high-speed train and large aircraft manufacturing. This is not only more conducive to achieving the needs of energy saving and environmental protection, and realizing the lightweight design of products such as automobiles, but also prolonging the service life of products such as automobiles.
  • FIG1 is a scanning representation diagram of the primary iron-rich phase and the primary ⁇ -Al phase structure of the aluminum-silicon alloy of Example 1 of the present disclosure
  • FIG2 is a diagram showing thermodynamic calculation results of an aluminum-silicon alloy according to an embodiment of the present disclosure
  • FIG3 is a scanning representation diagram of the heterogeneous core AlSi(Ti,Zr) x of the aluminum-silicon alloy of Example 1 of the present disclosure
  • FIG4 is a scanning representation diagram of the aluminum-silicon alloy eutectic silicon modification result of Example 1 of the present disclosure
  • FIG5 is a test diagram of the mechanical properties of the aluminum-silicon alloy of Example 1 of the present disclosure.
  • FIG6 is a test diagram of the mechanical properties of the aluminum-silicon alloy of Example 2 of the present disclosure.
  • FIG. 7 is a test diagram of the mechanical properties of the aluminum-silicon alloy of Example 3 of the present disclosure.
  • the present disclosure provides a high-strength and toughness die-cast aluminum-silicon alloy.
  • the high-strength and toughness die-cast aluminum-silicon alloy includes: 8.0wt% to 10.0wt% silicon, 0.35wt% to 0.75wt% manganese, 0.05wt% to 0.15wt% chromium, 0.01wt% to 0.6wt% magnesium, 0.1wt% to 3.0wt% zinc, 0.01wt% to 0.1wt% vanadium, 0.01wt% to 0.1wt% molybdenum, 0.05wt% to 0.3wt% zirconium, 0.05wt% to 0.3wt% titanium, 0.02wt% to 0.07wt% strontium, no more than 0.2wt% iron, no more than 0.15wt% unavoidable inclusions, and the balance of aluminum.
  • the aluminum-silicon alloy is prepared by mixing the content of each element in the above range, wherein iron is an inevitable impurity element, but it is also a necessary element to ensure demolding, and iron in the die-cast aluminum-silicon alloy is easy to combine with aluminum and silicon to form a relatively coarse primary iron-rich compound in the pressure chamber, which is a hard and brittle phase, which is easy to split the matrix and reduce the mechanical properties.
  • the inventors have found that adding molybdenum can refine the primary iron-rich phase, reduce its size, reduce its number, and transform its shape into a spherical shape, while Molybdenum, manganese, chromium and vanadium coordinate and optimize the primary iron-rich phase, thereby refining and spheroidizing the primary iron-rich phase, thereby improving the mechanical properties of the silicon-aluminum alloy; on the other hand, increasing the amount of zinc added can reduce the nucleation temperature of the primary ⁇ -Al phase, play a role in refining the primary ⁇ -Al grains, and achieve fine grain strengthening.
  • this application comprehensively optimizes the die-cast aluminum-silicon alloy structure by achieving refinement and spheroidization of the primary iron-rich phase, refinement of the primary ⁇ -Al grains, and precipitation of the second phase strengthening through the overall adjustment of the content of the above-mentioned elements, and prepares a die-cast aluminum-silicon alloy with excellent performance, so that it has high strength and toughness in a non-heat-treated state, and can better meet the production and manufacturing needs of high-pressure casting thin-walled parts and integrated die-cast structural parts.
  • the yield strength of the rod-shaped sample of the silicon aluminum alloy formed by the above-mentioned content ratio of each element is 150MP ⁇ 180MPa
  • the tensile strength is 300MP ⁇ 350MPa
  • the elongation is 10% ⁇ 15%
  • the silicon aluminum alloy exhibits excellent strength and toughness.
  • the high-strength and toughness die-cast aluminum-silicon alloy also includes no more than 0.01wt% of calcium.
  • strontium and Ca form a composite metamorphism, which can make the eutectic silicon at a higher metamorphic level, and then the flaky eutectic silicon will be completely converted into fine and uniform fibrous eutectic silicon, which is beneficial to improve the strength and plasticity of the silicon-aluminum alloy.
  • an oxide film can be formed on the surface of the aluminum melt to prevent internal oxidation, reduce air inhalation, and protect the melt. Therefore, the high-strength and toughness die-cast aluminum-silicon alloy of the present application also includes no more than 0.01wt% of calcium, which can improve the strength and plasticity of the silicon-aluminum alloy and effectively protect the aluminum melt.
  • the total mass of vanadium and molybdenum is 0.05wt% to 0.15wt%, preferably 0.1wt%.
  • the content of vanadium and molybdenum is appropriately reduced, even if the total mass of vanadium and molybdenum is 0.05wt% to 0.15wt%, the precipitation temperature of the primary iron-rich phase can be basically maintained at 582 to 585°C, thereby avoiding the precipitation of a coarse primary iron-rich phase. Therefore, the total mass of vanadium and molybdenum in the present application is 0.05wt% to 0.15wt%, which can avoid the precipitation of a coarse primary iron-rich phase.
  • the mass ratio of zirconium to titanium is (0.5-2):1, preferably 1:1.
  • the present disclosure proposes a method for preparing the above-mentioned high-strength and toughness die-cast aluminum-silicon alloy. According to an embodiment of the present disclosure, the method comprises:
  • S100 Weigh silicon, manganese, chromium, magnesium, zinc, vanadium, molybdenum, zirconium, titanium, strontium and aluminum according to their mass fractions, mix them, smelt them, and then cast and cut them.
  • silicon, manganese, chromium, magnesium, zinc, vanadium, molybdenum, zirconium, titanium, strontium and aluminum are weighed and mixed according to mass fraction, and then smelted and treated, and the Fe content is controlled to be less than 0.2wt%, and the sum of the contents of other impurity elements is less than 0.15wt.%, and then cast and cut into a block ingot of about 3kg.
  • Al-Mn master alloy, Al-Cr master alloy, Al-V master alloy, Al-Mo master alloy, Al-Zr master alloy, Al-Ti master alloy, Al-Ca master alloy, Al-Sr master alloy, etc. can be selected as raw materials, as long as the content of the above elements is finally guaranteed to be within the content range of this application.
  • the block ingot obtained in S100 is placed in a die casting machine melting furnace for heating, and after the alloy is melted, argon gas is introduced into the interior, and the agitator is used to stir the alloy evenly, so as to remove the gas and inclusions in the melt, and finally the melt is left to stand for 15 minutes, and the oxidized inclusions on the surface are removed by slagging. Furthermore, the temperature of the ingot heating is 730°C to 750°C.
  • the melt obtained in S200 is cooled to 710-720°C and is ready for die casting.
  • the die casting process parameters include: the casting temperature of the melt is 690-710°C, the mold temperature is 140-160°C, the vacuum degree inside the mold cavity is lower than 10kPa, the three-stage low-speed injection speed is 0.2-0.2-(0.2-0.4) m/s, the high-speed injection speed is 2.5m/s-3.5m/s, the high-speed accumulator pressure value is 12.5MPa-13.7MPa, and the booster accumulator pressure value is 12.5MPa-13.7MPa.
  • the high-strength and toughness die-cast aluminum silicon is obtained by mixing silicon, manganese, chromium, magnesium, zinc, vanadium, molybdenum, zirconium, titanium, strontium and aluminum within the above content range, smelting the mixture, casting and cutting the mixture to obtain an ingot, and then heating and melting the ingot and performing die-casting to obtain the ingot.
  • Alloy wherein the addition of molybdenum can refine the primary iron-rich phase, and at the same time, molybdenum coordinates with manganese, chromium, and vanadium to refine and spheroidize the primary iron-rich phase, thereby improving the mechanical properties of the silicon-aluminum alloy;
  • increasing the amount of zinc added can reduce the nucleation temperature of the primary ⁇ -Al phase, play a role in refining the primary ⁇ -Al grains, and achieve fine grain strengthening, and zinc and magnesium can form MgZn2 phases, which again play a role in strengthening the aluminum matrix as a second phase.
  • the method of the present application can be used to prepare a die-cast aluminum-silicon alloy with high yield strength, tensile strength, and elongation. It should be noted that the characteristics and advantages described for the above-mentioned high-strength and toughness die-cast aluminum-silicon alloy are also applicable to this method, and will not be repeated here.
  • the present disclosure proposes an aluminum-silicon alloy component.
  • the aluminum-silicon alloy component includes the above-mentioned high-strength and toughness die-cast aluminum-silicon alloy or the high-strength and toughness die-cast aluminum-silicon alloy prepared by the above-mentioned method.
  • the aluminum-silicon alloy component has a long service life and excellent mechanical properties. It should be noted that the features and advantages described for the above-mentioned high-strength and toughness die-cast aluminum-silicon alloy and its preparation method are also applicable to the aluminum-silicon alloy component, and will not be repeated here.
  • the fourth aspect of the present disclosure proposes the use of the above-mentioned high-strength and toughness die-cast aluminum silicon alloy or the high-strength and toughness die-cast aluminum silicon alloy prepared by the above-mentioned method in the fields of automobile, high-speed train and large aircraft manufacturing.
  • it is not only more conducive to achieving the needs of energy conservation and environmental protection, and realizing the lightweight design of products such as automobiles, but also prolonging the service life of products such as automobiles.
  • the characteristics and advantages described for the above-mentioned high-strength and toughness die-cast aluminum silicon alloy and its preparation method are also applicable to the means of transportation, and will not be repeated here.
  • the alloy raw materials pure Al, crystalline Si, Al-Mn master alloy, Al-Cr master alloy, pure Mg, pure Zn, Al-V master alloy, Al-Mo master alloy, Al-Zr master alloy, Al-Ti master alloy, Al-Ca master alloy, and Al-Sr master alloy are weighed and smelted after being prepared.
  • the content of each element is controlled to meet the content requirements, and the content of Fe element is controlled to be less than 0.2wt%, and the sum of the contents of other impurity elements is controlled to be less than 0.15wt%, and the casting and cutting are carried out into block ingots of about 3kg.
  • the specific element content of the silicon aluminum alloy is: Si: 9.60wt%; Mn: 0.41wt%; Cr: 0.08wt%; Mg: 0.02wt%; Zn: 0.18wt%; V: 0.07wt%; Mo: 0.03wt%; Zr: 0.14wt%; Ti: 0.16wt%; Ca: 0.005wt%; Sr: 0.02wt%; Fe: 0.11wt%;
  • the die-casting process parameters adopted are casting temperature 710°C, mold temperature 150°C, three-level low-speed injection speed 0.2-0.2-0.2m/s, high-speed injection speed 3.0m/s, high-speed ACC13.7MPa, and boost ACC13.7MPa, ensuring that the vacuum degree inside the mold cavity is lower than 10kPa.
  • the size of the primary iron-rich phase in the conventional die-cast aluminum-silicon alloy is coarse block-shaped, with a size of about 10 ⁇ m. It can be seen from Figure 1 that after adding Mn, Cr, Mo and V elements in this application, the size and morphology of the primary iron-rich phase are well regulated, and its size is about 1 ⁇ m, and the morphology tends to be spherical.
  • the primary ⁇ -Al phase in the conventional die-cast aluminum-silicon alloy is coarse and has well-developed dendrites, with a size close to 50 ⁇ m, and the largest size can be higher than 100 ⁇ m. From Figure 1, it can be observed that the primary ⁇ -Al phase of Example 1 is small in size, has a low degree of dendrite formation, tends to be spherical, and has a size of about 20 ⁇ m.
  • the solidification path of the silicon aluminum alloy before and after adding 3wt% Zn was calculated with the help of Thermo-Calc software.
  • the precipitation point of the primary ⁇ -Al phase was reduced from 604°C to 596°C, a decrease of 8°C, which provided a greater undercooling degree for solidification nucleation and promoted the grain refinement of the primary ⁇ -Al phase.
  • Ti and Zr elements are added to the alloy to promote grain refinement.
  • the mass ratio of zirconium to titanium is controlled to be 7:8, which is beneficial to the precipitation of AlSi(Ti,Zr)x phase in the early stage of solidification.
  • This phase has a good lattice mismatch with the primary ⁇ -Al phase and can provide a nucleation core for the nucleation of the primary ⁇ -Al phase, which is beneficial to grain refinement.
  • Sr and Ca form a composite metamorphism to ensure that the eutectic silicon is at a higher metamorphic level, thereby completely transforming the plate-like eutectic silicon into a fine fibrous eutectic silicon structure.
  • the eutectic silicon in Figure 4 has been completely fiberized and is small in size, reaching the micron level, which is beneficial to the strength and toughness of the alloy.
  • the tensile strength and yield strength of the die-cast aluminum silicon alloy are very high, the tensile strength can reach 320MPa, and the yield strength can reach 170MPa. At the same time, it can maintain an elongation of nearly 11%, indicating that the die-cast aluminum silicon alloy of the present application exhibits excellent comprehensive mechanical properties and can better meet the production and manufacturing needs of high-pressure casting thin-walled parts and integrated die-cast structural parts.
  • the specific element content of the silicon aluminum alloy is: Si: 8.58wt%; Mn: 0.46wt%; Cr: 0.12wt%; Mg: 0.43wt%; Zn: 0.37wt%; V: 0.08wt%; Mo: 0.01wt%; Zr: 0.14wt%; Ti: 0.13wt%; Ca: 0.001wt%; Sr: 0.06wt%; Fe: 0.08wt%;
  • the die-casting process parameters adopted are casting temperature 710°C, mold temperature 150°C, three-level low-speed injection speed 0.2-0.2-0.2m/s, high-speed injection speed 3.0m/s, high-speed ACC13.7MPa, and boost ACC13.7MPa, ensuring that the vacuum degree inside the mold cavity is lower than 10kPa.
  • the die-cast aluminum-silicon alloy rod sample prepared in Example 2 was subjected to microstructure analysis and mechanical property testing, and the relevant results are shown in Figure 6. As can be seen from Figure 6, the die-cast aluminum-silicon alloy prepared in Example 2 has a tensile strength of 318 MPa, a yield strength of 174 MPa, and an elongation of 10.17%.
  • the alloy raw materials pure Al, crystalline Si, Al-Mn master alloy, Al-Cr master alloy, pure Mg, pure Zn, Al-V master alloy, Al-Mo master alloy, Al-Zr master alloy, Al-Ti master alloy, Al-Ca master alloy, and Al-Sr master alloy are weighed and smelted after being prepared.
  • the content of each element is controlled to meet the content requirements, and the content of Fe element is controlled to be less than 0.2wt%, and the sum of the contents of other impurity elements is controlled to be less than 0.15wt%, and the casting and cutting are carried out into block ingots of about 3kg.
  • the specific element content of the silicon aluminum alloy is: Si: 8.67wt%; Mn: 0.40wt%; Cr: 0.05wt%; Mg: 0.43wt%; Zn: 0.47wt%; V: 0.06wt%; Mo: 0.02wt%; Zr: 0.23wt%; Ti: 0.17wt%; Ca: 0.004wt%; Sr: 0.04wt%; Fe: 0.09wt%;
  • the die-casting process parameters adopted are casting temperature 710°C, mold temperature 150°C, three-level low-speed injection speed 0.2-0.2-0.2m/s, high-speed injection speed 3.0m/s, high-speed ACC13.7MPa, and boost ACC13.7MPa, ensuring that the vacuum degree inside the mold cavity is lower than 10kPa.
  • the die-cast aluminum-silicon alloy rod sample prepared in Example 3 was subjected to microstructure analysis and mechanical property testing. The relevant results are as follows: As shown in Figure 7. As can be seen from Figure 7, the tensile strength of the die-cast aluminum-silicon alloy prepared in Example 3 is 315 MPa, the yield strength is 179 MPa, and the elongation is 10.23%.

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Abstract

一种高强韧压铸铝硅合金及其制备方法和应用，该高强韧压铸铝硅合金包括8.0wt％～10.0wt％的硅、0.35wt％～0.75wt％的锰、0.05wt％～0.15wt％的铬、0.01wt％～0.6wt％的镁、0.1wt％～3.0wt％的锌、0.01wt％～0.1wt％的钒、0.01wt％～0.1wt％的钼、0.05wt％～0.3wt％的锆、0.05wt％～0.3wt％的钛、0.02wt％～0.07wt％的锶、不大于0.2wt％的铁、不大于0.15wt％的不可避免夹杂物，以及余量的铝。该压铸铝硅合金具有较高屈服强度、抗拉强度和延伸率，将其用于汽车、高速列车及大飞机制造领域，不仅更有利于实现节能和环保的需要，实现汽车等产品的轻量化设计，而且延长了汽车等产品的使用寿命。

Description

高强韧压铸铝硅合金及其制备方法和应用
优先权信息
本申请请求于2023年02月03日向中国国家知识产权局提交的、专利申请号为202310110507.1、申请名称为“高强韧压铸铝硅合金及其制备方法和应用”的中国专利申请的优先权，并且其全部内容通过引用结合在本公开中。
技术领域
本公开属于金属合金制备及开发应用技术领域，具体涉及一种高强韧压铸铝硅合金及其制备方法和应用。
背景技术
节能减排是当今世界汽车产业发展的重要聚焦点之一，其中汽车轻量化是最为行之有效的解决方式。铝硅合金具有密度小、流动性好、比强度和比刚度高的优势，在汽车零部件上应用广泛。传统的汽车车身制造方法是先将单个汽车零部件进行热处理，以提高综合力学性能，之后再将数个零部件焊接或铆接拼装起来。近几年，特斯拉一体化压铸技术的实现大大降低了汽车的重量，也去除了焊接或铆接的工序，在提高效率的同时也减少了制造生产成本。然而，由于一体化压铸结构件的尺寸较大，在热处理时会产生热变形和鼓泡等问题，因此，急需开发出一种可以在非热处理状态下保持较高强韧性的压铸铝硅合金材料。
公开内容
本公开旨在至少在一定程度上解决相关技术中的技术问题之一。为此，本公开的目的在于提出一种高强韧压铸铝硅合金及其制备方法和应用。该高强韧压铸铝硅合金具有较高屈服强度、抗拉强度和延伸率，展现出优异的强韧性。
本公开的一个方面，本公开提出了一种高强韧压铸铝硅合金。根据本公开的实施例，该高强韧压铸铝硅合金包括：8.0wt％～10.0wt％的硅、0.35wt％～0.75wt％的锰、0.05wt％～0.15wt％的铬、0.01wt％～0.6wt％的镁、0.1wt％～3.0wt％的锌、0.01wt％～0.1wt％的钒、0.01wt％～0.1wt％的钼、0.05wt％～0.3wt％的锆、0.05wt％～0.3wt％的钛、0.02wt％～0.07wt％的锶、不大于0.2wt％的铁、不大于0.15wt％的不可避免夹杂物，以及余量的铝。
根据本公开上述实施例的高强韧压铸铝硅合金，通过按照上述各元素含量范围配比制 备铝硅合金，其中，因为铁是不可避免的杂质元素，但也是为保证脱模的必要元素，而铁在压铸铝硅合金中容易与铝、硅结合在压室中形成较粗大的初生富铁化合物，其为硬脆相，容易割裂基体，降低力学性能，发明人发现，添加钼可以细化初生富铁相，使得其尺寸减小，数量减少，形状转变为球状，同时钼与锰、铬、钒共同协调优化初生富铁相，从而细化、球化初生富铁相，进而提高了硅铝合金的力学性能；另一方面，提高锌的添加量，可以降低初生α-Al相的形核温度，起到细化初生α-Al晶粒的作用，实现了细晶强化，具体地，利用Thermo-Calc软件计算发现，Zn的添加量从1％提高至3％后，初生α-Al相的形核温度降低8℃，且锌与镁可以形成MgZn2相，再次对铝基体起到第二相强化的作用。由此，本申请通过上述各元素含量的整体调整，通过实现细化、球化初生富铁相、细化初生α-Al晶粒以及析出第二相强化，综合优化压铸铝硅合金组织，制备得到性能优异的压铸铝硅合金，使其在非热处理状态下便具有较高的强韧性，可以较好满足高压铸造薄壁件以及一体化压铸结构件的生产制造需求。具体地，采用上述含量配比的各元素形成的硅铝合金棒状试样的屈服强度为150MP～180MPa、抗拉强度为300MP～350MPa、延伸率为10％～15％，该硅铝合金展现出优异的强韧性。
另外，根据本公开上述实施例的高强韧压铸铝硅合金还可以具有如下技术特征：
在本公开的一些实施例中，高强韧压铸铝硅合金还包括不大于0.01wt％的钙。由此，可以提高硅铝合金的强塑性。
在本公开的一些实施例中，所述钒和所述钼的总质量为0.05wt％～0.15wt％，优选0.1wt％。由此，可以避免析出粗大的初生富铁相。
在本公开的一些实施例中，所述锆和所述钛的质量比为(0.5～2)：1，优选1：1。由此，可以细化初生α-Al晶粒，实现细晶强化。
本公开的第二个方面，本公开提出了一种制备上述高强韧压铸铝硅合金的方法。根据本公开的实施例，该方法包括：
(1)按质量分数分别称取硅、锰、铬、镁、锌、钒、钼、锆、钛、锶和铝混合后进行熔炼处理后浇铸切割，以便得到铸锭；
(2)对所述铸锭加热熔化，以便得到熔体；
(3)对所述熔体进行压铸，以便得到高强韧压铸铝硅合金。
由此，通过将上述含量范围内的硅、锰、铬、镁、锌、钒、钼、锆、钛、锶和铝混合后进行熔炼处理后浇铸切割得到铸锭，再对铸锭加热熔化后进行压铸得到高强韧压铸铝硅合金，其中，添加钼可以细化初生富铁相，同时钼与锰、铬、钒共同协调来细化、球化初 生富铁相，进而提高了硅铝合金的力学性能；另一方面，提高锌的添加量，可以降低初生α-Al相的形核温度，起到细化初生α-Al晶粒的作用，实现了细晶强化，且锌与镁可以形成MgZn2相，再次对铝基体起到第二相强化的作用。由此，采用本申请的方法可以制备得到具有较高屈服强度、抗拉强度和延伸率的压铸铝硅合金。
另外，根据本公开上述制备高强韧压铸铝硅合金的方法还可以具有如下技术特征：
在本公开的一些实施例中，步骤(2)中，所述铸锭加热的温度为730℃～750℃。
在本公开的一些实施例中，步骤(3)中，所述压铸工艺参数包括：所述熔体的浇铸温度为690℃～710℃，模具温度140℃～160℃，模具型腔内部的真空度低于10kPa，三级低速压射速度0.2-0.2-(0.2～0.4)m/s，高速压射速度2.5m/s～3.5m/s，高速蓄能器压力值12.5MPa～13.7MPa，增压蓄能器压力值12.5MPa～13.7MPa。
本公开的第三个方面，本公开提出了一种铝硅合金部件。根据本公开的实施例，所述铝硅合金部件包括上述高强韧压铸铝硅合金或采用上述方法制备得到的高强韧压铸铝硅合金。由此，该铝硅合金部件使用寿命长，力学性能优异。
本公开的第四个方面，本公开提出了上述高强韧压铸铝硅合金或采用上述方法制备得到的高强韧压铸铝硅合金在汽车、高速列车及大飞机制造领域中的用途。由此，不仅更有利于实现节能和环保的需要，实现汽车等产品的轻量化设计，而且延长了汽车等产品的使用寿命。
本公开的附加方面和优点将在下面的描述中部分给出，部分将从下面的描述中变得明显，或通过本公开的实践了解到。
附图说明
此处所说明的附图用来提供对本申请的进一步理解，构成本申请的一部分，本申请的示意性实施例及其说明用于解释本申请，并不构成对本申请的不当限定。在附图中：
图1是本公开实施例1的铝硅合金的初生富铁相与初生α-Al相组织的扫描表征图；
图2是本公开实施例的铝硅合金的热力学计算结果图；
图3是本公开实施例1的铝硅合金的异质核心AlSi(Ti,Zr)x的扫描表征图；
图4是本公开实施例1的铝硅合金共晶硅变质结果扫描表征图；
图5是本公开实施例1的铝硅合金的力学性能结果测试图；
图6是本公开实施例2的铝硅合金的力学性能结果测试图；
图7是本公开实施例3的铝硅合金的力学性能结果测试图。
具体实施方式
下面参考具体实施例，对本公开进行描述，需要说明的是，这些实施例仅仅是描述性的，而不以任何方式限制本公开。
本公开的一个方面，本公开提出了一种高强韧压铸铝硅合金。根据本公开的实施例，该高强韧压铸铝硅合金包括：8.0wt％～10.0wt％的硅、0.35wt％～0.75wt％的锰、0.05wt％～0.15wt％的铬、0.01wt％～0.6wt％的镁、0.1wt％～3.0wt％的锌、0.01wt％～0.1wt％的钒、0.01wt％～0.1wt％的钼、0.05wt％～0.3wt％的锆、0.05wt％～0.3wt％的钛、0.02wt％～0.07wt％的锶、不大于0.2wt％的铁、不大于0.15wt％的不可避免夹杂物，以及余量的铝。
根据本公开上述实施例的高强韧压铸铝硅合金，通过按照上述各元素含量范围配比制备铝硅合金，其中，因为铁是不可避免的杂质元素，但也是为保证脱模的必要元素，而铁在压铸铝硅合金中容易与铝、硅结合在压室中形成较粗大的初生富铁化合物，其为硬脆相，容易割裂基体，降低力学性能，发明人发现，添加钼可以细化初生富铁相，使得其尺寸减小，数量减少，形状转变为球状，同时钼与锰、铬、钒共同协调优化初生富铁相，从而细化、球化初生富铁相，进而提高了硅铝合金的力学性能；另一方面，提高锌的添加量，可以降低初生α-Al相的形核温度，起到细化初生α-Al晶粒的作用，实现了细晶强化，具体地，利用Thermo-Calc软件计算发现，Zn的添加量从1％提高至3％后，初生α-Al相的形核温度降低8℃，且锌与镁可以形成MgZn2相，再次对铝基体起到第二相强化的作用。由此，本申请通过上述各元素含量的整体调整，通过实现细化、球化初生富铁相、细化初生α-Al晶粒以及析出第二相强化综合优化压铸铝硅合金组织，制备得到性能优异的压铸铝硅合金，使其在非热处理状态下便具有较高的强韧性，可以较好满足高压铸造薄壁件以及一体化压铸结构件的生产制造需求。具体地，采用上述含量配比的各元素形成硅铝合金的棒状试样的屈服强度为150MP～180MPa、抗拉强度为300MP～350MPa、延伸率为10％～15％，该硅铝合金展现出优异的强韧性。
根据本公开的实施例，高强韧压铸铝硅合金还包括不大于0.01wt％的钙。发明人发现，如果添加不大于0.01wt％的钙，锶与Ca形成复合变质，可以使共晶硅处于较高的变质等级，进而片状的共晶硅将完全转化为细小均匀的纤维状共晶硅，有利于提高硅铝合金的强塑性，另一方面，Ca添加后可在铝熔体表面形成氧化膜，防止内部氧化，并减少吸气，保护熔体。由此，本申请的高强韧压铸铝硅合金还包括不大于0.01wt％的钙，可以提高硅铝合金的强塑性，且有效保护铝熔体。
根据本公开的实施例，钒和钼的总质量为0.05wt％～0.15wt％，优选0.1wt％。发明人发 现，以Mn和Cr元素为主，适当降低钒和钼元素的含量，即使钒和钼的总质量为0.05wt％～0.15wt％，可以使初生富铁相析出温度基本维持在582～585℃，从而避免析出粗大的初生富铁相。由此，本申请的钒和钼的总质量为0.05wt％～0.15wt％，可以避免析出粗大的初生初生富铁相。
根据本公开的实施例，锆和钛的质量比为(0.5～2)：1，优选1：1。发明人发现，控制锆和钛的质量比在一定范围内，有利于析出AlSi(Ti,Zr)x相，AlSi(Ti,Zr)x相与铝基体具有较好的晶格匹配关系，能够成为初生α-Al相的形核核心，从而达到细化初生α-Al晶粒的作用。由此，本申请采用锆和钛的质量比为(0.5～2)：1，可以细化初生α-Al晶粒，实现细晶强化。
本公开的第二个方面，本公开提出了一种制备上述高强韧压铸铝硅合金的方法。根据本公开的实施例，该方法包括：
S100：按质量分数分别称取硅、锰、铬、镁、锌、钒、钼、锆、钛、锶和铝混合后进行熔炼处理后浇铸切割
该步骤中，按质量分数分别称取硅、锰、铬、镁、锌、钒、钼、锆、钛、锶和铝混合后进行熔炼处理，并控制Fe元素含量低于0.2wt％，其他杂质元素含量之和低于0.15wt.％，浇铸切割成3kg左右的块状铸锭。需要说明的是，考虑到成本因素，可选用Al-Mn中间合金、Al-Cr中间合金、Al-V中间合金、Al-Mo中间合金、Al-Zr中间合金、Al-Ti中间合金、Al-Ca中间合金、Al-Sr中间合金等做原料，只要最后保证上述各元素含量在本申请的含量范围内即可。
S200：对铸锭加热熔化。
该步骤中，将S100得到的块状铸锭放入压铸机熔炼炉内加热，待合金熔化后在内部通入氩气，同时借助搅拌器实现搅拌均匀，以便除去熔体内部的气体和夹杂，最后静置熔体15分钟后，扒渣除去表面的氧化夹杂物。进一步地，铸锭加热的温度为730℃～750℃。
S300：对熔体进行压铸
该步骤中，待S200得到的熔体降温至710～720℃，准备进行压铸，压铸工艺参数包括：熔体的浇铸温度为690℃～710℃，模具温度140℃～160℃，模具型腔内部的真空度低于10kPa，三级低速压射速度0.2-0.2-(0.2～0.4)m/s，高速压射速度2.5m/s～3.5m/s，高速蓄能器压力值12.5MPa～13.7MPa，增压蓄能器压力值12.5MPa～13.7MPa。
由此，通过将上述含量范围内的硅、锰、铬、镁、锌、钒、钼、锆、钛、锶和铝混合后进行熔炼处理后浇铸切割得到铸锭，再对铸锭加热熔化后进行压铸得到高强韧压铸铝硅 合金，其中，添加钼可以细化初生富铁相，同时钼与锰、铬、钒共同协调来细化、球化初生富铁相，进而提高了硅铝合金的力学性能；另一方面，提高锌的添加量，可以降低初生α-Al相的形核温度，起到细化初生α-Al晶粒的作用，实现了细晶强化，且锌与镁可以形成MgZn2相，再次对铝基体起到第二相强化的作用。由此，采用本申请的方法可以制备得到具有较高屈服强度、抗拉强度和延伸率的压铸铝硅合金。需要说明的是，针对上述高强韧压铸铝硅合金所描述的特征和优点同样适用于该方法，此处不再赘述。
本公开的第三个方面，本公开提出了一种铝硅合金部件。根据本公开的实施例，铝硅合金部件包括上述高强韧压铸铝硅合金或采用上述方法制备得到的高强韧压铸铝硅合金。由此，该铝硅合金部件使用寿命长，力学性能优异。需要说明的是，针对上述高强韧压铸铝硅合金及其制备方法所描述的特征和优点同样适用于该铝硅合金部件，此处不再赘述。
本公开的第四个方面，本公开提出了上述高强韧压铸铝硅合金或采用上述方法制备得到的高强韧压铸铝硅合金在汽车、高速列车及大飞机制造领域中的用途。由此，不仅更有利于实现节能和环保的需要，实现汽车等产品的轻量化设计，而且延长了汽车等产品的使用寿命。需要说明的是，针对上述高强韧压铸铝硅合金及其制备方法所描述的特征和优点同样适用于该交通工具，此处不再赘述。
下面参考具体实施例，对本公开进行描述，需要说明的是，这些实施例仅仅是描述性的，而不以任何方式限制本公开。
实施例1
(1)按照计量分数称量合金原料纯Al、结晶Si、Al-Mn中间合金、Al-Cr中间合金、纯Mg、纯Zn、Al-V中间合金、Al-Mo中间合金、Al-Zr中间合金、Al-Ti中间合金、Al-Ca中间合金、Al-Sr中间合金，配置好后进行熔炼处理。控制各元素符合含量要求，并控制Fe元素含量低于0.2wt％，其他杂质元素含量之和低于0.15wt％，浇铸切割成3kg左右的块状铸锭。具体地，硅铝合金的具体元素含量为：Si：9.60wt％；Mn：0.41wt％；Cr：0.08wt％；Mg：0.02wt％；Zn：0.18wt％；V：0.07wt％；Mo：0.03wt％；Zr：0.14wt％；Ti：0.16wt％；Ca：0.005wt％；Sr：0.02wt％；Fe：0.11wt％；
(2)将块状铸锭放入压铸机熔炼炉内加热，温度设置为750℃，待合金熔化后在内部通入氩气，同时借助搅拌器实现搅拌均匀，以便除去熔体内部的气体和夹杂。静置熔体15分钟后，扒渣除去熔体表面的氧化夹杂物。
(3)待熔体降温至710℃，进行压铸试验。
所采用的压铸工艺参数为浇铸温度710℃，模具温度150℃，三级低速压射速度0.2-0.2-0.2m/s，高速压射速度3.0m/s，高速ACC13.7MPa，增压ACC13.7MPa，确保模具型腔内部的真空度低于10kPa。
对实施例1制备的压铸铝硅合金棒状试样进行组织分析和力学性能测试，相关结果如下：
如图1所示，常规的压铸铝硅合金中的初生富铁相尺寸为粗大的块状，尺寸在10μm左右，从图1可以看出，本申请添加Mn、Cr、Mo和V元素后，对初生富铁相的尺寸和形貌得到了很好的调控，其尺寸在1μm左右，且形貌趋于球状。常规的压铸铝硅合金中的初生α-Al相尺寸粗大且枝晶发达，尺寸接近50μm，最大的尺寸可高于100μm，从图1中可以观察到实施例1的初生α-Al相，尺寸较小，枝晶化程度不高，趋于球状，尺寸在20μm左右。
借助Thermo-Calc软件对硅铝合金添加3wt％Zn前后的凝固路径进行计算，如图2所示，初生α-Al相的析出点从604℃降低到596℃，下降了8℃，为凝固形核提供了更大的过冷度，促进了初生α-Al相晶粒细化。说明本申请通过提高Zn元素含量可以降低初生α-Al相的形核温度，从而促进了初生α-Al相晶粒细化。
如图3所示，合金中添加了Ti和Zr元素以促进晶粒细化，实施例1中控制锆和钛的质量比为7：8，有利于在凝固初期析出AlSi(Ti,Zr)x相，该相与初生α-Al相具有较好的晶格错配度，可以为初生α-Al相的形核提供形核核心，有利于晶粒细化。
如图4所示，Sr与Ca形成复合变质，确保共晶硅处于较高的变质等级，从而将板片状的共晶硅完全变质为细小纤维状的共晶硅组织，图4中的共晶硅已完全纤维化，且尺寸细小，达到微米级，有利于合金的强韧性。
如图5所示，通过两组平行试验，可以发现该压铸铝硅合金的拉伸强度和屈服强度都很高，抗拉强度可达320MPa，屈服强度可到170MPa，与此同时，还能保持将近11％的延伸率，说明本申请的压铸铝硅合金展现了优异的综合力学性能，可以较好满足高压铸造薄壁件以及一体化压铸结构件的生产制造需求。
实施例2
(1)按照计量分数称量合金原料纯Al、结晶Si、Al-Mn中间合金、Al-Cr中间合金、纯Mg、纯Zn、Al-V中间合金、Al-Mo中间合金、Al-Zr中间合金、Al-Ti中间合金、Al-Ca中间合金、Al-Sr中间合金，配置好后进行熔炼处理。控制各元素符合含量要求，并控制Fe元素含量低于0.2wt％，其他杂质元素含量之和低0.15wt％，浇铸切割成3kg左右的块状铸 锭。具体地，硅铝合金的具体元素含量为：Si：8.58wt％；Mn：0.46wt％；Cr：0.12wt％；Mg：0.43wt％；Zn：0.37wt％；V：0.08wt％；Mo：0.01wt％；Zr：0.14wt％；Ti：0.13wt％；Ca：0.001wt％；Sr：0.06wt％；Fe：0.08wt％；
(2)将块状铸锭放入压铸机熔炼炉内加热，温度设置为750℃，待合金熔化后在内部通入氩气，同时借助搅拌器实现搅拌均匀，以便除去熔体内部的气体和夹杂。静置熔体15分钟后，扒渣除去熔体表面的氧化夹杂物。
(3)待熔体降温至710℃，进行压铸试验。
所采用的压铸工艺参数为浇铸温度710℃，模具温度150℃，三级低速压射速度0.2-0.2-0.2m/s，高速压射速度3.0m/s，高速ACC13.7MPa，增压ACC13.7MPa，确保模具型腔内部的真空度低于10kPa。
对实施例2制备的压铸铝硅合金棒状试样进行组织分析和力学性能测试，相关结果如图6所示。从图6可以看出，实施例2制备的压铸铝硅合金的抗拉强度为318MPa，屈服强度为174MPa，延伸率为10.17％。
实施例3
(1)按照计量分数称量合金原料纯Al、结晶Si、Al-Mn中间合金、Al-Cr中间合金、纯Mg、纯Zn、Al-V中间合金、Al-Mo中间合金、Al-Zr中间合金、Al-Ti中间合金、Al-Ca中间合金、Al-Sr中间合金，配置好后进行熔炼处理。控制各元素符合含量要求，并控制Fe元素含量低于0.2wt％，其他杂质元素含量之和低0.15wt％，浇铸切割成3kg左右的块状铸锭。具体地，硅铝合金的具体元素含量为：Si：8.67wt％；Mn：0.40wt％；Cr：0.05wt％；Mg：0.43wt％；Zn：0.47wt％；V：0.06wt％；Mo：0.02wt％；Zr：0.23wt％；Ti：0.17wt％；Ca：0.004wt％；Sr：0.04wt％；Fe：0.09wt％；
(2)将块状铸锭放入压铸机熔炼炉内加热，温度设置为750℃，待合金熔化后在内部通入氩气，同时借助搅拌器实现搅拌均匀，以便除去熔体内部的气体和夹杂。静置熔体15分钟后，扒渣除去熔体表面的氧化夹杂物。
(3)待熔体降温至710℃，进行压铸试验。
所采用的压铸工艺参数为浇铸温度710℃，模具温度150℃，三级低速压射速度0.2-0.2-0.2m/s，高速压射速度3.0m/s，高速ACC13.7MPa，增压ACC13.7MPa，确保模具型腔内部的真空度低于10kPa。
对实施例3制备的压铸铝硅合金棒状试样进行组织分析和力学性能测试，相关结果如 图7所示。从图7可以看出，实施例3制备的压铸铝硅合金的抗拉强度为315MPa，屈服强度为179MPa，延伸率为10.23％。
上面结合附图对本申请的实施例进行了描述，但是本申请并不局限于上述的具体实施方式，上述的具体实施方式仅仅是示意性的，而不是限制性的，本领域的普通技术人员在本申请的启示下，在不脱离本申请宗旨和权利要求所保护的范围情况下，还可做出很多形式，均属于本申请的保护之内。

Claims (12)

  1. 一种高强韧压铸铝硅合金，其中，包括：8.0wt％～10.0wt％的硅、0.35wt％～0.75wt％的锰、0.05wt％～0.15wt％的铬、0.01wt％～0.6wt％的镁、0.1wt％～3.0wt％的锌、0.01wt％～0.1wt％的钒、0.01wt％～0.1wt％的钼、0.05wt％～0.3wt％的锆、0.05wt％～0.3wt％的钛、0.02wt％～0.07wt％的锶、不大于0.2wt％的铁、不大于0.15wt％的不可避免夹杂物，以及余量的铝。
  2. 根据权利要求1所述的高强韧压铸铝硅合金，其中，还包括不大于0.01wt％的钙。
  3. 根据权利要求1或2所述的高强韧压铸铝硅合金，其中，所述钒和所述钼的总质量为0.05wt％～0.15wt％。
  4. 根据权利要求1-3中任一项所述的高强韧压铸铝硅合金，其中，所述钒和所述钼的总质量为0.1wt％。
  5. 根据权利要求1-4中任一项所述的高强韧压铸铝硅合金，其中，所述锆和所述钛的质量比为(0.5～2)：1。
  6. 根据权利要求1-5中任一项所述的高强韧压铸铝硅合金，其中，所述锆和所述钛的质量比为1：1。
  7. 根据权利要求1-6中任一项所述的高强韧压铸铝硅合金，其中，形成的棒状试样的屈服强度为150MP～180MPa、抗拉强度为300MP～350MPa、延伸率为10％～15％。
  8. 一种制备权利要求1-7中任一项所述高强韧压铸铝硅合金的方法，其中，包括：
    (1)按质量分数分别称取硅、锰、铬、镁、锌、钒、钼、锆、钛、锶和铝混合后进行熔炼处理后浇铸切割，以便得到铸锭；
    (2)对所述铸锭加热熔化，以便得到熔体；
    (3)对所述熔体进行压铸，以便得到高强韧压铸铝硅合金。
  9. 根据权利要求8所述的方法，其中，步骤(2)中，所述铸锭加热的温度为730℃～750℃。
  10. 根据权利要求8所述的方法，其中，步骤(3)中，所述压铸工艺参数包括：所述熔体的浇铸温度为690℃～710℃，模具温度140℃～160℃，模具型腔内部的真空度低于10kPa，三级低速压射速度0.2-0.2-(0.2～0.4)m/s，高速压射速度2.5m/s～3.5m/s，高速蓄能器压力值12.5MPa～13.7MPa，增压蓄能器压力值12.5MPa～13.7MPa。
  11. 一种铝硅合金部件，其中，所述铝硅合金部件包括权利要求1-7中任一项所述的高强韧压铸铝硅合金或采用权利要求8-10中任一项所述的方法制备得到的高强韧压铸铝硅合金。
  12. 权利要求1-7中任一项所述的高强韧压铸铝硅合金或采用权利要求8-10中任一项所述的方法制备得到的高强韧压铸铝硅合金在汽车、高速列车及大飞机制造领域中的用途。
PCT/CN2023/098373 2023-02-03 2023-06-05 高强韧压铸铝硅合金及其制备方法和应用 Ceased WO2024159682A1 (zh)

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