Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material and preparation method thereof

Abstract

The invention provides an Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material and a preparation method of the Al-Cu-Mg-Mn-Ni-Si heat The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material disclosed by the invention is prepared on the basis of a casting forming process in combination with grain boundary strengthening, precipitated phase strengthening and excess phase strengthening mechanisms. According to the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material disclosed by the invention, thermal stability strengthening phases such as an Al9FeNi phase, a SiC phase, an Al2Cu phase, an Al6Mn phase, an Al11Ce3 phase, an Al2CuMg phase and an Al3Zr phase can be formed on a crystal boundary; the thermal stability strengthening phases have different heat-resistant temperature zones; the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material can be used for precise forming and manufacturing of aerospace light high-temperature structural parts, is excellent in machining forming performance, has good room-temperature and high-temperature mechanical properties, and has wide application prospects and high engineering application value.

Description

Technical Field

[0001] The present invention belongs to the technical field of nonferrous alloy materials, and in particular relates to an Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material and a preparation method thereof. Background Art

[0002] With the continuous development of society, the demand for energy and resources is growing rapidly, and the demand for lightweight structural materials is growing. As an indispensable means of transportation for human activities, the power components of cars, trains, airplanes, ships, etc. have an increasingly urgent demand for lightweight heat-resistant structural parts. With the increasing requirements for high power density and fuel economy of power components, the upper temperature limit of aluminum alloy materials for manufacturing hot end components has been increased from the traditional 150℃ to 300℃-400℃, so heat-resistant aluminum alloy materials and their preparation methods have become one of the hot spots in current aluminum alloy research.

[0003] Heat-resistant aluminum alloy refers to an aluminum alloy that has sufficient oxidation resistance at high temperatures and has the ability to resist plastic deformation (creep) and damage under the long-term action of temperature and load (dynamic load and static load). Due to its advantages such as high thermal conductivity and low density, heat-resistant aluminum alloy has been widely used in the aerospace field, such as cylinder heads and pistons of aircraft engines, aircraft skins, etc. It can also be used to manufacture hot end components and structural parts such as aircraft blades, helicopter propellers, and engine impellers.

[0004] Although most aluminum alloy materials have good comprehensive mechanical properties at room temperature, the high-temperature softening problem of aluminum alloy materials has always been a key problem restricting the structural design and service use of aluminum alloy materials in the medium and high temperature range. For example, for the 7050 series aluminum alloy with high room temperature mechanical properties, the tensile strength of the alloy at 200℃ and 300℃ is only 30% and 10% of that at room temperature. Therefore, for the 300℃-500℃ temperature range that is of greatest concern in the aerospace field, the design tends to use titanium alloys with high density and high price; if the medium-temperature strength of aluminum alloys can be improved so that they can be stably used in the 300℃-400℃ temperature range, they can replace some expensive titanium alloys, magnesium alloys and carbon fiber materials, achieving the dual economic benefits of lightweight structure and low-cost batch production. Summary of the invention

[0005] The inventors of this application have found that the high-temperature mechanical properties of aluminum alloys are mainly determined by two factors, namely, room temperature strength and the attenuation rate of high-temperature strength. Therefore, it is possible to improve the high-temperature mechanical properties of aluminum alloys only if both the room temperature strengthening effect and the high-temperature microstructure stability of aluminum alloys are guaranteed. And based on the research of mature high-strength aluminum alloys, the main strategy to improve heat resistance is to form a high volume fraction of thermally stable strengthening phases inside the aluminum matrix, so as to improve the high-temperature comprehensive performance of aluminum alloy materials by utilizing the effective pinning of thermally stable strengthening relative dislocations and grain boundaries.

[0006] For heat-resistant aluminum alloys, the casting process has been developed for many years and is relatively mature. It has been widely used in the automotive, aerospace, shipbuilding and other industries. For example, in the field of automobile manufacturing, alloys such as A319, A380 and ZL702A have been successfully commercialized and used in the production and manufacturing of automobile engines. Casting heat-resistant aluminum alloys are simple to process and have low manufacturing costs, but their process characteristics lead to low element solid solubility, making it difficult to form a thermally stable strengthening phase with a sufficiently high volume fraction in the aluminum alloy matrix. In addition, when the service temperature of existing cast heat-resistant aluminum alloys exceeds 200°C, the internal strengthening phases such as Mg2Si phase, Al2Cu phase, and Al2CuMg phase will gradually coarsen due to heat, and the grain boundary pinning dislocation ability will be significantly reduced, and the high-temperature mechanical properties will be severely attenuated. Therefore, the upper limit of the service temperature of the current cast heat-resistant aluminum alloy is 200°C, which is difficult to meet the technical index requirements of the service temperature of heat-resistant aluminum alloys in the aerospace field.

[0007] With the gradual maturity of rapid solidification technology, a new solution is provided for the development of dispersion-strengthened heat-resistant aluminum alloys. Compared with traditional casting processes, rapid solidification technology greatly improves the solidification rate of the alloy and the supersaturated solid solubility of alloying elements in the aluminum matrix, which promotes the formation of fine dispersed phases with higher volume fraction and thermal stability, thereby effectively improving the strength and heat resistance of the alloy. At present, the traditional preparation processes of rapid solidification heat-resistant aluminum alloys mainly include plane flow casting, gas atomization and spray deposition. All three processes have a large cooling rate. At the same time, all three processes can use different methods to decompose the molten metal into thin strips or droplets to increase the cooling rate and achieve rapid solidification. However, rapid solidification preparation of heat-resistant aluminum alloys can only prepare simple-shaped rods or block ingots, and cannot achieve precision forming of complex structure heat-resistant aluminum alloy parts. In recent years, metal additive manufacturing (AM) has gradually become a key technology for the preparation of aviation parts at home and abroad because it can prepare high-density complex components with high dimensional accuracy and good mechanical properties, and has the advantages of shortening production cycles and reducing material waste. Among them, the most promising selective laser melting (SLM) technology has brought new technological breakthroughs in improving the mechanical properties of heat-resistant aluminum alloys. Compared with rapid solidification technology, the cooling rate of the molten pool in the SLM process is at least 1-2 orders of magnitude higher (-10 7 K / s), thereby obtaining a finer microstructure and precipitating a higher concentration of heat-stable strengthening phases, significantly improving the high-temperature performance of aluminum alloys. However, during the complex thermal cycle of SLM, due to the high reflectivity, high thermal conductivity, large solidification range and poor fluidity of the existing aluminum alloy powders, the obtained aluminum alloy parts are prone to form pores and thermal cracking defects. In other words, the key factor restricting the additive manufacturing of heat-resistant aluminum alloys is that heat-resistant aluminum alloy materials suitable for SLM or other additive manufacturing processes have not been developed, and industrial-scale trial production and production cannot be achieved.

[0008] In order to solve the defects and deficiencies in the prior art, the present application provides an Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material and a preparation method thereof. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material of the present invention is prepared based on a casting forming process and combined with grain boundary strengthening, precipitation phase strengthening and excess phase strengthening mechanisms. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material of the present invention can form Al9FeNi phase, SiC phase, Al2Cu phase, Al6Mn phase, Al 11Ce3 phase, Al2CuMg phase and Al3Zr phase are thermally stable strengthening phases; these thermally stable strengthening phases have different heat-resistant temperature ranges; for example, the medium and low temperature range of 100℃-200℃ is pinned by dislocation climb and slip of Al2Cu phase and Al2CuMg phase; the medium and high temperature range of 200℃-350℃ is pinned by Al9FeNi phase, SiC phase, Al6Mn phase, Al 11 The Ce3 phase and Al3Zr pin and hinder the relative dislocation movement and grain boundary sliding, thereby increasing the upper limit of the service temperature of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material to 350°C, effectively improving the high-temperature bearing capacity of the alloy material, and significantly improving the high-temperature comprehensive mechanical properties of the alloy material. Compared with the preparation process of the rapidly solidified heat-resistant aluminum alloy material, the casting forming process of the present invention can be used to form and manufacture high-temperature load-bearing structural parts with complex shapes, and realize the precision forming and manufacturing of the structural and functional integration of high-temperature load-bearing structural parts, which greatly improves the utilization rate of aluminum alloy materials. Compared with the preparation process of the additively manufactured heat-resistant aluminum alloy material, the casting forming process of the present invention can combine the grain boundary strengthening, precipitation phase strengthening and excess phase strengthening mechanisms, which can effectively avoid the formation of pores and hot cracking defects in aluminum alloy parts, and has low manufacturing cost and short production cycle, while having good room temperature and high temperature comprehensive mechanical properties. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material of the present invention has a room temperature tensile strength of ≥400MPa, a room temperature yield strength of ≥340MPa, and a room temperature material elongation of ≥5% after double-stage aging heat treatment; a high temperature tensile strength of ≥280MPa at 200°C, and a high temperature tensile strength of ≥220MPa at 300°C; a steady-state creep rate ε at 300°C / 100MPa • ≤1×10 -8 s -1 ;350℃ oxidation weight gain rate ≤0.18mg·cm -2 ·h -1 ; 250℃ creep strength limit σ 0.2 / 100 ≥120MPa, 300℃ creep strength limitσ 0.2 / 100 ≥80MPa. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material of the present invention can be used for precision forming and manufacturing of lightweight high-temperature structural parts for aerospace, has excellent processing and forming performance, has both good room temperature and high-temperature mechanical properties, and has broad application prospects and strong engineering application value.

[0009] The object of the present invention is achieved through the following technical solutions: An Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, wherein the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material comprises the following components in percentage by mass: 5.0%-8.0% Cu element, 1.2%-2.4% Mg element, 0.4%-0.8% Mn element, 0.4%-1.0% Ni element, 0.2%-0.4% Ce element, 0.1%-0.2% La element, 0.2%-0.3% Ag element, 0.1%-0.15% Zr element, 0.1%-0.15% Sc element, 0.6%-1.0% Fe element, 0.2%-0.5% Si element, 0.2%-0.5% SiC particles, and the balance is Al and unavoidable impurity components.

[0010] According to an embodiment of the present invention, the particle size of the SiC particles is 50 μm-100 μm, for example, 50 μm, 60 μm, 70 μm, 80 μm, 90 μm or 100 μm.

[0011] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes 5.0%, 5.2%, 5.5%, 5.6%, 5.8%, 6%, 6.2%, 6.5%, 6.8%, 7%, 7.2%, 7.5%, 7.6%, 7.8% or 8.0% of the Cu element.

[0012] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3% or 2.4% of the Mg element.

[0013] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes 0.4%, 0.45%, 0.5%, 0.55%, 0.6%, 0.65%, 0.7%, 0.75% or 0.8% of the Mn element.

[0014] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes 0.4%, 0.45%, 0.5%, 0.55%, 0.6%, 0.65%, 0.7%, 0.75%, 0.8%, 0.85%, 0.9%, 0.95% or 1.0% of Ni element.

[0015] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes 0.20%, 0.23%, 0.24%, 0.25%, 0.26%, 0.28%, 0.3%, 0.32%, 0.34%, 0.35%, 0.36% or 0.4% of Ce element.

[0016] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes 0.10%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19% or 0.20% of La element.

[0017] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes 0.2%, 0.21%, 0.22%, 0.23%, 0.24%, 0.25%, 0.26%, 0.27%, 0.28%, 0.29% or 0.3% of Ag element.

[0018] According to an embodiment of the present invention, the Al—Cu—Mg—Mn—Ni—Si heat-resistant aluminum alloy material includes 0.10%, 0.11%, 0.12%, 0.13%, 0.14% or 0.15% of the Zr element.

[0019] According to an embodiment of the present invention, the Al—Cu—Mg—Mn—Ni—Si heat-resistant aluminum alloy material includes 0.10%, 0.11%, 0.12%, 0.13%, 0.14% or 0.15% of the Sc element.

[0020] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes 0.6%, 0.65%, 0.7%, 0.75%, 0.8%, 0.85%, 0.9%, 0.95% or 1.0% of Fe element.

[0021] According to an embodiment of the present invention, the Al—Cu—Mg—Mn—Ni—Si heat-resistant aluminum alloy material includes 0.2%, 0.25%, 0.3%, 0.35%, 0.4%, 0.45% or 0.5% of Si element.

[0022] According to an embodiment of the present invention, the Al—Cu—Mg—Mn—Ni—Si heat-resistant aluminum alloy material includes 0.2%, 0.25%, 0.3%, 0.35%, 0.4%, 0.45% or 0.5% of SiC particles.

[0023] According to an embodiment of the present invention, the mass ratio of the Ce element to the La element is 1.38-2.36, for example, 1.40, 1.50, 1.60, 1.70, 1.80, 1.90, 2.00, 2.10, 2.20, 2.30 or 2.36. When the mass ratio of the Ce element to the La element is 1.38-2.36, the Ce element and the La element can form Al in the aluminum matrix. 11 Ce3 phase, Al4Ce phase (heat resistant 1250℃), Al 11 Ce phase (heat resistance > 400℃) and Al4La phase (heat resistance > 400℃). The existence of these phase structures can inhibit the diffusion of grain boundaries and the climb of dislocations, and significantly improve the heat resistance and creep resistance of alloy materials.

[0024] According to an embodiment of the present invention, the mass ratio of the Zr element to the Sc element is 0.75-1.35, for example, 0.75, 0.80, 0.85, 0.90, 0.95, 1.00, 1.05, 1.10, 1.15, 1.20, 1.25, 1.30 or 1.35. When the mass ratio of the Zr element to the Sc element is 0.75-1.35, the Zr element can precipitate an Al3Zr phase with a higher volume fraction in the aluminum matrix, and the Al3Zr phase effectively pins and hinders the dislocation movement and grain boundary sliding, thereby increasing the upper limit of the service temperature of the aluminum alloy material to 350°C; at the same time, the added Sc element can also realize the periodic self-assembly of the two types of Cu / Sc atoms in space through the in-situ phase transformation on the basis of the nano-precipitated Al2CuMg phase, forming a V phase with extremely high thermal stability, and significantly improving the heat resistance of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material.

[0025] According to an embodiment of the present invention, the mass ratio of the Cu element to the Mg element is 2.55-3.15, for example, 2.55, 2.6, 2.65, 2.70, 2.75, 2.80, 2.85, 2.90, 2.95, 3.00, 3.05, 3.10 or 3.15. When the mass ratio of the Cu element to the Mg element is 2.55-3.15, the Cu element can form an Al2Cu precipitation phase with the Al element, and the Al2Cu precipitation phase (including the θ phase and the θ' phase) as the main heat-resistant phase at medium and low temperatures can effectively hinder the movement of dislocations in the temperature range of 150°C-200°C, thereby improving the medium and low temperature mechanical properties of the heat-resistant aluminum alloy material; the Cu element can also form an Al2CuMg phase with the Mg element and the Al element, and the Al2CuMg phase (S phase) is also the main heat-resistant phase in the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, thereby improving the medium and low temperature mechanical properties of the heat-resistant aluminum alloy material.

[0026] According to an embodiment of the present invention, the mass ratio of the Mn element to the Fe element is 0.45-0.65, for example, 0.45, 0.50, 0.55, 0.60 or 0.65. When the mass ratio of the Mn element to the Fe element is 0.45-0.65, the addition of the Mn element can effectively avoid the formation of needle-shaped β-Fe phases in the alloy material, deteriorating the mechanical properties of the alloy material, and is also conducive to stabilizing the formation of fine Al6Mn phases, thereby facilitating the increase of the recrystallization temperature of the alloy material and improving the high-temperature creep resistance of the alloy material.

[0027] According to an embodiment of the present invention, the mass ratio of the Mg element to the Si element is 5.0-8.5, for example, 5.0, 5.5, 6.0, 6.5, 7.0, 7.5, 8.0 or 8.5. When the mass ratio of the Mg element to the Si element is 5-8.5, the Mg element and the Si element can react in the alloy melt to form a Mg2Si strengthening phase, which can effectively improve the yield strength of the alloy at room temperature, effectively hinder the slip of dislocations in the temperature range of 100°C-200°C, and improve the medium and low temperature mechanical properties of the heat-resistant aluminum alloy material.

[0028] According to an embodiment of the present invention, the mass ratio of the Fe element to the Ni element is 0.75-1.75, for example, 0.75, 0.80, 0.85, 0.90, 0.95, 1.00, 1.05, 1.10, 1.15, 1.20, 1.25, 1.30, 1.35, 1.40, 1.45, 1.50, 1.55, 1.60, 1.65, 1.70 or 1.75. When the mass ratio of the Fe element to the Ni element is 0.75-1.75, the Fe element and the Ni element can promote the precipitation of a higher volume fraction of the Al9FeNi phase in the aluminum matrix, and the Al9FeNi phase effectively pins and hinders the dislocation movement and grain boundary sliding, thereby effectively improving the heat resistance of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material in the medium and high temperature range.

[0029] According to an embodiment of the present invention, the raw materials for preparing the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material include Al-SiC-based master alloy and Al-Al9FeNi-based master alloy.

[0030] According to an embodiment of the present invention, the Al-SiC-based master alloy is formed by pressing Al powder and SiC powder; the mass of the SiC powder in the Al-SiC-based master alloy accounts for 20%-60%, such as 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55% or 60%, of the total mass of the Al-SiC-based master alloy; the mass of the Al powder in the Al-SiC-based master alloy accounts for 40%-80%, such as 40%, 45%, 50%, 55%, 60%, 65%, 70%, 75% or 80% of the total mass of the Al-SiC-based master alloy; the particle size of the Al powder is 120μm-200μm, and the particle size of the SiC powder is 50μm-100μm.

[0031] According to an embodiment of the present invention, the Al-Al9FeNi-based master alloy is formed by pressing Al powder and Al9FeNi powder; the mass of the Al9FeNi powder in the Al-Al9FeNi-based master alloy accounts for 5%-10% of the total mass of the Al-Al9FeNi-based master alloy, such as 5%, 6%, 7%, 8%, 9% or 10%; the mass of the Al powder in the Al-Al9FeNi-based master alloy accounts for 90%-95% of the total mass of the Al-Al9FeNi-based master alloy, such as 90%, 91%, 92%, 93%, 94% or 95%; the particle size of the Al powder is 120μm-200μm, and the particle size of the Al9FeNi powder is 150μm-250μm.

[0032] According to an embodiment of the present invention, the raw materials for preparing the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material also include high-purity aluminum ingots, high-purity magnesium ingots, Al-Cu master alloys, Al-Mn master alloys, Al-Ni master alloys, Al-Si master alloys, Al-Ce master alloys, Al-La master alloys, Al-Ag master alloys, Al-Zr master alloys, Al-Sc master alloys, Al-Fe master alloys and Al-Ti-C master alloys.

[0033] According to an embodiment of the present invention, the grain boundary phase of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes Al9FeNi phase, SiC phase, Al2Cu phase, Al6Mn phase, Al 11 Ce3 phase, Al2CuMg phase and Al3Zr phase.

[0034] According to an embodiment of the present invention, the volume fraction of the Al9FeNi phase accounts for 0.24%-0.30% of the total volume fraction of all phases, the volume fraction of the SiC phase accounts for 0.08%-0.12% of the total volume fraction of all phases, the volume fraction of the Al2Cu phase accounts for 0.32%-0.35% of the total volume fraction of all phases, the volume fraction of the Al6Mn phase accounts for 0.08%-0.10% of the total volume fraction of all phases, and the volume fraction of the Al2Cu phase accounts for 0.32%-0.35% of the total volume fraction of all phases. 11 The volume fraction of the Ce3 phase accounts for 0.12%-0.15% of the total volume fraction of all phases, the volume fraction of the Al2CuMg phase accounts for 0.28%-0.32% of the total volume fraction of all phases, and the volume fraction of the Al3Zr phase accounts for 0.18%-0.24% of the total volume fraction of all phases.

[0035] According to an embodiment of the present invention, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material further includes a TiC phase, and the volume fraction of the TiC phase accounts for 0.015%-0.025% of the total volume fraction of all phases.

[0036] According to the embodiment of the present invention, the room temperature tensile strength of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material after double-stage aging heat treatment is ≥400MPa, the room temperature yield strength is ≥340MPa, and the room temperature material elongation is ≥5%; the high temperature tensile strength at 200°C is ≥280MPa, and the high temperature tensile strength at 300°C is ≥220MPa; the steady-state creep rate ε at 300°C / 100MPa is • ≤1×10 -8 s -1 ;350℃ oxidation weight gain rate ≤0.18mg·cm -2 ·h -1 ; 250℃ creep strength limit σ 0.2 / 100 ≥120MPa, 300℃ creep strength limitσ 0.2 / 100 ≥80MPa.

[0037] The present invention also provides a method for preparing the above Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, the method comprising the following steps: (1) Ingredients and weighing: according to the composition ratio of the above Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, weigh high-purity aluminum ingots, high-purity magnesium ingots, Al-Cu master alloys, Al-Mn master alloys, Al-Ni master alloys, Al-Si master alloys, Al-Ce master alloys, Al-La master alloys, Al-Ag master alloys, Al-Zr master alloys, Al-Sc master alloys, Al-Fe master alloys, Al-SiC-based master alloys, Al-Al9FeNi-based master alloys and Al-Ti-C master alloys; (2) Melting: Mix the high-purity aluminum ingot and the Al-Cu master alloy, and heat them to 760℃-780℃ until the high-purity aluminum ingot and the Al-Cu master alloy are completely melted; continue to heat them to 780℃-800℃, add Al-Ni master alloy, Al-Si master alloy, Al-Fe master alloy and Al-Ag master alloy, and stir until the Al-Ni master alloy, Al-Si master alloy, Al-Fe master alloy and Al-Ag master alloy are completely melted; cool them to 750℃-760℃, add Al-Mn master alloy, Al-Ce master alloy, Al-La master alloy, Al-Zr master alloy, and Gold and Al-Sc master alloy, stirring until Al-Mn master alloy, Al-Ce master alloy, Al-La master alloy, Al-Zr master alloy and Al-Sc master alloy are completely melted; continue to cool to 740°C-750°C, add Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy, stirring until Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are completely melted; continue to cool to 730°C-740°C, add high-purity magnesium ingot, stir until the high-purity magnesium ingot is completely melted, and obtain an alloy melt; (3) Refining: Control the temperature of the alloy melt at 735°C-745°C, add a refining agent, and perform a refining treatment on the alloy melt; (4) Degassing: The temperature of the alloy melt is lowered to 730°C-735°C, argon and nitrogen are first introduced for rotary spray degassing, and then the temperature of the alloy melt is lowered to 725°C-730°C, a solid powder degassing agent is added, and the alloy melt is degassed by solid powder; (5) Casting: Let the degassed alloy melt stand for 10-15 minutes before casting; (6) Heat treatment: After the alloy melt is cast, the heat-resistant aluminum alloy material is taken out after cooling, and the heat-resistant aluminum alloy material is subjected to solid solution quenching treatment and aging heat treatment to prepare the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material.

[0038] According to the implementation scheme of the present invention, in step (1), high-purity aluminum ingots, high-purity magnesium ingots, Al-Cu master alloys, Al-Mn master alloys, Al-Ni master alloys, Al-Si master alloys, Al-Ce master alloys, Al-La master alloys, Al-Ag master alloys, Al-Zr master alloys, Al-Sc master alloys and Al-Fe master alloys, Al-SiC-based master alloys, Al-Al9FeNi-based master alloys, and Al-Ti-C master alloys are washed with high-pressure industrial tap water to remove oil stains on the surface of the raw materials, and then baked in a baking furnace at 100°C-120°C for 15min-20min to dry and dehydrate.

[0039] According to an embodiment of the present invention, in step (1), the purity of the high-purity aluminum ingot is ≥99.99%. The purity of the high-purity magnesium ingot is ≥99.99%. The Al-Cu master alloy is, for example, an Al-20Cu master alloy or an Al-30Cu master alloy, and the purity of the Al-Cu master alloy is ≥99%. The purity of the Al-Cu master alloy refers to the sum of the contents of the Al element and the Cu element in the master alloy. The Al-Mn master alloy is, for example, an Al-9Mn master alloy, an Al-10Mn master alloy or an Al-11Mn master alloy, and the purity of the Al-Mn master alloy is ≥99%. The purity of the Al-Mn master alloy refers to the sum of the contents of the Al element and the Mn element in the master alloy. The Al-Ni master alloy is, for example, an Al-10Ni master alloy or an Al-50Ni master alloy, and the purity of the Al-Ni master alloy is ≥99%. The purity of the Al-Ni master alloy refers to the sum of the contents of the Al element and the Ni element in the master alloy. The Al-Si master alloy is, for example, an Al-10Si master alloy, an Al-12Si master alloy, or an Al-50Si master alloy, and the purity of the Al-Si master alloy is ≥99%, and the purity of the Al-Si master alloy refers to the sum of the contents of the Al element and the Si element in the master alloy. The Al-Ce master alloy is, for example, an Al-6Ce master alloy, an Al-10Ce master alloy, or an Al-20Ce master alloy, and the purity of the Al-Ce master alloy is ≥99%, and the purity of the Al-Ce master alloy refers to the sum of the contents of the Al element and the Ce element in the master alloy. The Al-La master alloy is, for example, an Al-5La master alloy, an Al-10La master alloy, or an Al-15La master alloy, and the purity of the Al-La master alloy is ≥99%, and the purity of the Al-La master alloy refers to the sum of the contents of the Al element and the La element in the master alloy. The Al-Ag master alloy is, for example, an Al-10Ag master alloy or an Al-20Ag master alloy, and the purity of the Al-Ag master alloy is ≥99%, and the purity of the Al-Ag master alloy refers to the sum of the contents of the Al element and the Ag element in the master alloy. The Al-Zr master alloy is, for example, an Al-4Zr master alloy, an Al-5Zr master alloy, or an Al-6Zr master alloy, and the purity of the Al-Zr master alloy is ≥99%, and the purity of the Al-Zr master alloy refers to the sum of the contents of the Al element and the Zr element in the master alloy. The Al-Sc master alloy is, for example, an Al-2Sc master alloy or an Al-5Sc master alloy, and the purity of the Al-Sc master alloy is ≥99%, and the purity of the Al-Sc master alloy refers to the sum of the contents of the Al element and the Sc element in the master alloy.The Al-Fe master alloy is, for example, an Al-5Fe master alloy or an Al-10Fe master alloy. The purity of the Al-Fe master alloy is ≥99%. The purity of the Al-Fe master alloy refers to the sum of the contents of the Al element and the Fe element in the master alloy.

[0040] According to an embodiment of the present invention, in step (1), the Al-SiC-based master alloy is defined as above. The Al-Al9FeNi-based master alloy is defined as above.

[0041] According to an embodiment of the present invention, in step (1), the Al-Ti-C master alloy is in the form of wire, and the diameter of the wire is 4 mm to 6 mm. The composition of the Al-Ti-C master alloy is, for example, AlTi5C 0.18 、AlTi3C 0.15 or AlTi5C 1.2 .

[0042] According to an embodiment of the present invention, in step (2), the melting is carried out in a graphite crucible, and the heating method of the graphite crucible is resistance heating or gas heating.

[0043] According to an embodiment of the present invention, in step (2), the stirring is performed by stirring the alloy melt with a slag spoon.

[0044] According to the implementation scheme of the present invention, in step (2), by adding different alloy raw materials in different temperature ranges, a high volume fraction of heat-resistant strengthening phase can be precipitated in the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material. Exemplarily, by adding high-purity aluminum ingots and Al-Cu master alloys in the temperature range of 760°C-780°C, it is beneficial to the precipitation of a high volume fraction of Al2Cu phase; by adding Al-Ni master alloys, Al-Si master alloys, Al-Fe master alloys and Al-Ag master alloys in the temperature range of 780°C-800°C, it is beneficial to the precipitation of a high volume fraction of Al9FeNi phase; by adding Al-Mn master alloys, Al-Ce master alloys, Al-La master alloys, Al-Zr master alloys and Al-Sc master alloys in the temperature range of 750°C-760°C, it is beneficial to the precipitation of a high volume fraction of Al6Mn phase, Al-Si master alloys, Al-Fe master alloys and Al-Ag master alloys. 11 Ce3 phase, Al4Ce phase, Al 11The method is advantageous for the precipitation of Ce phase, Al4La phase and Al3Zr phase; by adding Al-SiC based master alloy, Al-Al9FeNi based master alloy and Al-Ti-C master alloy in the temperature range of 740℃-750℃, it is beneficial for the precipitation of Al9FeNi phase, SiC phase and TiC phase with high volume fraction; by adding high purity magnesium ingot in the temperature range of 730℃-740℃, it is beneficial for the precipitation of Al2CuMg phase and Mg2Si phase with high volume fraction.

[0045] According to an embodiment of the present invention, in step (2), the amount of the Al-Ti-C master alloy added is 0.12%-0.18% of the total mass of the alloy melt, such as 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17% or 0.18%.

[0046] According to an embodiment of the present invention, in step (3), the refining treatment time is 10 min-15 min.

[0047] According to an embodiment of the present invention, in step (3), the refining agent includes CaF2, MgCl2, KCl and KNO3; wherein the mass of CaF2 accounts for 45%-50% of the total mass of the refining agent, such as 45%, 46%, 47%, 48%, 49% or 50%; the mass of MgCl2 accounts for 25%-30% of the total mass of the refining agent, such as 25%, 26%, 27%, 28%, 29% or 30%; the mass of KCl accounts for 10%-12% of the total mass of the refining agent, such as 10%, 11% or 12%; the mass of KNO3 accounts for 8%-20% of the total mass of the refining agent, such as 8%, 9%, 10%, 11%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, 19% or 20%.

[0048] According to an embodiment of the present invention, in step (3), the mass of the refining agent accounts for 0.25%-0.35% of the total mass of the alloy melt, for example, 0.25%, 0.26%, 0.27%, 0.28%, 0.29%, 0.30%, 0.31%, 0.32%, 0.33%, 0.34% or 0.35%.

[0049] According to an embodiment of the present invention, in step (3), the refining agent is added by pressing a bell jar into the bottom of the alloy melt; illustratively, the refining agent is placed in the bell jar, and then the bell jar is pressed into the bottom of the alloy melt, left to stand for 4 min-5 min, the bell jar is taken out, and then the alloy melt is stirred for 8 min-10 min.

[0050] According to an embodiment of the present invention, in step (4), the time of the rotary blowing is 5 min-10 min.

[0051] According to an embodiment of the present invention, in step (4), the volume ratio of argon gas to nitrogen gas is 3:1-4:1.

[0052] According to an embodiment of the present invention, in step (4), the degassing time of the solid powder is 10 min-15 min.

[0053] According to an embodiment of the present invention, in step (4), the solid powder degassing agent comprises C2Cl6, TiO2 and CaO; wherein the mass of C2Cl6 accounts for 60%-65% of the total mass of the solid powder degassing agent, such as 60%, 61%, 62%, 63%, 64% or 65%; the mass of TiO2 accounts for 20%-25% of the total mass of the solid powder degassing agent, such as 20%, 21%, 22%, 23%, 24% or 25%; the mass of CaO accounts for 10%-20% of the total mass of the solid powder degassing agent, such as 10%, 11%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, 19% or 20%; the particle size of C2Cl6 is 60μm-120μm; the particle size of TiO2 is 50μm-80μm; the particle size of CaO is 120μm-200μm.

[0054] According to an embodiment of the present invention, in step (4), the mass of the solid powder degassing agent accounts for 0.25%-0.35% of the total mass of the alloy melt, for example, 0.25%, 0.26%, 0.27%, 0.28%, 0.29%, 0.30%, 0.31%, 0.32%, 0.33%, 0.34% or 0.35%.

[0055] According to an embodiment of the present invention, in step (4), the solid powder degassing agent is wrapped with aluminum foil before being added to the alloy melt, and then baked at a temperature range of 100°C-150°C for 15min-30min to prevent water vapor in the air absorbed by the surface of the solid powder from being introduced into the aluminum alloy melt, causing the melt gas content to be too high and generating pinholes or loose defects.

[0056] According to an embodiment of the present invention, in step (5), the casting temperature is 650°C-680°C.

[0057] According to an embodiment of the present invention, in step (5), casting is carried out in a sand mold, a gypsum mold, an investment shell mold, a metal mold or a semi-continuous casting crystallizer.

[0058] According to an embodiment of the present invention, in step (5), the casting process parameters are process parameters known in the art.

[0059] According to the implementation scheme of the present invention, in step (5), before casting, a two-stage ceramic filter is used to filter and purify the alloy melt before the furnace; the material of the ceramic filter is Al2O3 or Y2O3, the specification of the first-stage ceramic filter is 15PPI-20PPI, and the thickness is 15mm-20mm; the specification of the second-stage ceramic filter is 25PPI-40PPI, and the thickness is 20mm-25mm.

[0060] According to an embodiment of the present invention, in step (6), the cooling method is natural cooling or water flow cooling.

[0061] According to an embodiment of the present invention, in step (6), the solution temperature is 520°C-540°C, such as 520°C, 525°C, 530°C, 535°C or 540°C; the solution time is 6h-10h, such as 7h, 8h or 9h.

[0062] According to an embodiment of the present invention, in step (6), during the solution quenching treatment, the quenching transfer time is ≤20s, the quenching medium is industrial tap water, and the temperature of the quenching medium is 25°C-50°C.

[0063] According to an embodiment of the present invention, in step (6), the aging heat treatment is a two-stage aging heat treatment system, the first-stage aging heat treatment insulation temperature is 120°C-140°C, the first-stage aging heat treatment insulation time is 8h-10h, the second-stage aging heat treatment insulation temperature is 170°C-190°C, the second-stage aging heat treatment insulation time is 2h-4h, and the second-stage aging heat treatment is naturally cooled to room temperature after completion.

[0064] Beneficial effects of the present invention: The invention provides an Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material and a preparation method thereof.

[0065] The present invention forms a high-melting-point excess phase Al9FeNi phase (melting point is 960°C) and SiC phase (melting point is 2700°C) in the alloy melt by adding Al-Al9FeNi-based master alloy and Al-SiC-based master alloy during the preparation process of the alloy melt (preferably in the temperature range of 740°C-750°C); specifically, the introduction of the Al-Al9FeNi-based master alloy can achieve uniform distribution of fine Al9FeNi phases in the alloy melt, and can also ensure that the Al9FeNi phase is dispersed along the grain boundaries of the aluminum matrix to pin dislocation movement; the introduction of the Al-SiC-based master alloy can form a large number of uniform and fine heat-resistant excess phase SiC phases in the alloy melt, thereby improving the heat resistance of the heat-resistant aluminum alloy material, and on the other hand, effectively improves the wear resistance of the heat-resistant aluminum alloy material.

[0066] The present invention further improves the heat resistance of the heat-resistant aluminum alloy material by adding an Al-Ti-C master alloy during the preparation process of the alloy melt (preferably in the temperature range of 740°C-750°C) to form a high-melting-point TiC phase (melting point is 3100°C) in the alloy melt; at the same time, it can also effectively refine the grain size of the alloy melt and improve the grain boundary strengthening effect of the heat-resistant aluminum alloy material.

[0067] The present invention adds Al-Cu master alloy during the preparation process of alloy melt (preferably in the temperature range of 760°C-780°C), and the Cu element can form Al2Cu precipitation phase in the alloy melt. The Al2Cu precipitation phase (including θ phase and θ' phase) serves as the main heat-resistant phase at medium and low temperatures, and can effectively hinder the movement of dislocations in the temperature range of 150°C-200°C, thereby improving the medium and low temperature mechanical properties of the heat-resistant aluminum alloy material.

[0068] The present invention forms an Al2CuMg phase in the alloy melt by adding a high-purity magnesium ingot during the preparation process of the alloy melt (preferably in the temperature range of 730°C-740°C). The Al2CuMg phase (S phase) is also the main heat-resistant phase in the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, which can improve the heat resistance of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material.

[0069] The present invention adds an Al-Sc master alloy during the preparation of the alloy melt (preferably in the temperature range of 750°C-760°C), and the Sc element can be deposited on the nano-precipitation phase Al2CuMg phase in the double-stage aging heat treatment stage, and the periodic self-assembly of the two types of Cu / Sc atoms in space is achieved through an in-situ phase transformation approach to form a V phase with extremely high thermal stability, thereby significantly improving the heat resistance of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material.

[0070] The present invention adds an Al-Zr master alloy during the preparation of the alloy melt (preferably in the temperature range of 750°C-760°C), and the Zr element can react in the alloy melt to generate a large number of fine Al3Zr phases. The Al3Zr phase has an L12 lattice structure and its stability at high temperatures can reach 400°C. It can pin dislocations and grain boundaries to delay the high-temperature softening of the alloy material, and at the same time can refine the grain size and reduce grain boundary slip in the high-temperature stage.

[0071] The present invention adds an Al-Mn master alloy during the preparation of the alloy melt (preferably in the temperature range of 750°C-760°C). The addition of the Mn element can avoid the formation of a needle-shaped β-Fe phase in the alloy material, which deteriorates the mechanical properties of the alloy material, and can also generate a stable and fine Al6Mn phase. The Al6Mn phase can withstand a high temperature of 200°C-300°C for a long time, thereby increasing the recrystallization temperature of the alloy material and improving the high-temperature creep resistance of the alloy material.

[0072] In the present invention, Al-Ce master alloy and Al-La master alloy are added during the preparation process of the alloy melt (preferably in the temperature range of 750°C-760°C). The addition of Ce element and La element can form Al4Ce phase (heat resistant to 1250°C), Al 11 Ce phase (heat resistance > 400℃) and Al4La phase (heat resistance > 400℃). The existence of these phase structures can inhibit the diffusion of grain boundaries and the climb of dislocations, and significantly improve the heat resistance and creep resistance of alloy materials.

[0073] The present invention adds an Al-Si master alloy during the preparation of the alloy melt (preferably in the temperature range of 780°C-800°C). The addition of the Si element can react in the alloy melt to form a Mg2Si strengthening phase. The Mg2Si strengthening phase can effectively improve the yield strength of the alloy at room temperature, effectively hinder the slip of dislocations in the temperature range of 100°C-200°C, and improve the medium and low temperature mechanical properties of the heat-resistant aluminum alloy material.

[0074] The present invention adds Al-Fe master alloy and Al-Ni master alloy during the preparation process of the alloy melt (preferably in the temperature range of 780°C-800°C). The addition of Fe element and Ni element can promote the precipitation of Al9FeNi phase with a higher volume fraction in the aluminum matrix. Al9FeNi phase effectively pins and hinders dislocation movement and grain boundary sliding, and effectively improves the heat resistance of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material in the medium and high temperature range.

[0075] The present invention adds Al-Ag master alloy during the preparation of alloy melt (preferably in the temperature range of 780°C-800°C). The addition of Ag element can promote the precipitation density and quantity of Al2CuMg phase in the primary aging heat treatment stage, and further improve the heat resistance of Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material.

[0076] The room temperature tensile strength of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material after double-stage aging heat treatment is ≥400MPa, the room temperature yield strength is ≥340MPa, and the room temperature material elongation is ≥5%; the high temperature tensile strength of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material after double-stage aging heat treatment is ≥280MPa at 200°C, and the high temperature tensile strength is ≥220MPa at 300°C; the steady-state creep rate ε at 300°C / 100MPa is • ≤1×10 -8 s -1 ;350℃ oxidation weight gain rate ≤0.18mg·cm -2 ·h -1 ; 250℃ creep strength limit σ 0.2 / 100 ≥120MPa, 300℃ creep strength limitσ 0.2 / 100 ≥80MPa. BRIEF DESCRIPTION OF THE DRAWINGS

[0077] Figure 1 Shown is the solidification cooling curve of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 1.

[0078] Figure 2 The figure shows the mass distribution of Cu element in each solidified phase of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 1.

[0079] Figure 3 Shown are the room temperature mechanical properties test results of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 1.

[0080] Figure 4 Shown is the curve of the solidification crystallization latent heat of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 2 changing with the solidification temperature.

[0081] Figure 5 Shown is the curve of the room temperature material strength limit of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 2 as a function of the solidification cooling rate.

[0082] Figure 6 Shown is a curve showing the change of mass fraction of precipitation phase of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 2 with solidification temperature.

[0083] Figure 7 Shown are the room temperature elongation test results of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 3. DETAILED DESCRIPTION

[0084] The technical scheme of the present invention will be further described in detail below in conjunction with specific embodiments. It should be understood that the following embodiments are only exemplary descriptions and explanations of the present invention and should not be construed as limiting the scope of protection of the present invention. All technologies implemented based on the above content of the present invention are included in the scope that the present invention is intended to protect.

[0085] Unless otherwise specified, the experimental methods used in the following examples are all conventional methods; the reagents, materials, etc. used in the following examples, unless otherwise specified, can be obtained from commercial channels.

[0086] Example 1 The present embodiment provides an Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, which includes the following components in mass fractions: 5.0% Cu element, 1.8% Mg element, 0.45% Mn element, 0.9% Ni element, 0.21% Ce element, 0.15% La element, 0.22% Ag element, 0.1% Zr element, 0.1% Sc element, 0.7% Fe element, 0.3% Si element, 0.2% SiC particles, and the remainder is Al and unavoidable impurity components.

[0087] The preparation method of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material comprises the following steps: (1) Ingredients and weighing: according to the composition ratio of the above-mentioned Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, high-purity aluminum ingots, high-purity magnesium ingots, Al-20Cu master alloy, Al-10Mn master alloy, Al-10Ni master alloy, Al-12Si master alloy, Al-6Ce master alloy, Al-5La master alloy, Al-10Ag master alloy, Al-4Zr master alloy, Al-2Sc master alloy, Al-6Fe master alloy, Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are weighed; the above-mentioned raw materials are washed with high-pressure industrial tap water to remove oil stains on the surface of the raw materials, and then baked in a baking furnace at 100° C. for 15 minutes for drying and dehydration; (2) Melting: Place high-purity aluminum ingot and Al-20Cu master alloy into a graphite crucible. The graphite crucible is heated by resistance heating and heated to 760°C until the high-purity aluminum ingot and Al-20Cu master alloy are completely melted. Continue to heat the crucible to 780°C, add Al-10Ni master alloy, Al-12Si master alloy, Al-6Fe master alloy and Al-10Ag master alloy into the graphite crucible, and stir the alloy melt with a slag spoon until the Al-10Ni master alloy, Al-12Si master alloy, Al-6Fe master alloy and Al-10Ag master alloy are completely melted. Cool the crucible to 750°C, add Al-10Mn master alloy, Al-6Ce master alloy and Al-5La master alloy into the graphite crucible. Gold, Al-4Zr master alloy and Al-2Sc master alloy, and stir the alloy melt with a slag spoon until the Al-10Mn master alloy, Al-6Ce master alloy, Al-5La master alloy and Al-4Zr master alloy are completely melted; continue to cool to 740°C, add Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy in a graphite crucible, and stir with a slag spoon until the Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are completely melted; continue to cool to 730°C, add a high-purity magnesium ingot in the graphite crucible, and stir with a slag spoon until the high-purity magnesium ingot is completely melted to obtain an alloy melt; (3) Refining: controlling the temperature of the alloy melt at 735° C., adding a refining agent to refine the alloy melt for 10 min. The refining agent in the refining step is composed of CaF2, MgCl2, KCl and KNO3, wherein CaF2 accounts for 45% of the total weight of the refining agent, MgCl2 accounts for 25% of the total weight of the refining agent, KCl accounts for 10% of the total weight of the refining agent, and KNO3 accounts for 20% of the total weight of the refining agent. The refining agent accounts for 0.25% of the total weight of the alloy melt. When adding the refining agent, a bell jar is used to press the bottom of the alloy melt in a graphite crucible. After the bell jar is used to press the alloy melt, it is allowed to stand for 4 min, and then the bell jar is taken out to stir the alloy melt for 8 min. (4) Degassing: The temperature of the alloy melt is controlled at 730°C, and a composite degassing process is used for degassing. Argon and nitrogen are first introduced for rotary spraying degassing. The rotary spraying time is 5 minutes, and the gas volume ratio of argon and nitrogen is 3:1; then the temperature is lowered to 725°C, and a solid powder degassing agent is added for degassing for 10 minutes; the solid powder degassing agent in the degassing step is composed of C2Cl6, TiO2 and CaO, C2Cl6 accounts for 60% of the total weight of the solid powder degassing agent, and the particle size is 60μm; TiO2 accounts for 20% of the total weight of the solid powder degassing agent, and the particle size is 50μm; CaO accounts for 20% of the total weight of the solid powder degassing agent, and the particle size is 120μm; the solid powder degassing agent is wrapped with aluminum foil before being added to the alloy melt, and then baked at a temperature range of 100°C for 15 minutes after wrapping; (5) Casting: After the alloy melt is refined and degassed, it is allowed to stand in a graphite crucible for 10 minutes and then cast in a sand mold at a casting temperature of 650°C. In the casting step, a double-stage ceramic filter is used to filter and purify the alloy melt before casting. The ceramic filter is made of Al2O3, and the specification of the first-stage ceramic filter is 15PPI and the thickness is 15mm; the specification of the second-stage ceramic filter is 25PPI and the thickness is 20mm. (6) Heat treatment: After the alloy melt is cast, it is naturally cooled and then the heat-resistant aluminum alloy material is taken out from the sand mold. The heat-resistant aluminum alloy material is subjected to a solution heat preservation treatment in a solution heat preservation furnace. The solution heat preservation temperature is 520°C, the solution heat preservation time is 6 hours, the quenching transfer time is 15 seconds, the quenching medium is industrial tap water, and the quenching medium temperature is 25°C. After the solution heat preservation, the heat-resistant aluminum alloy material is subjected to a two-stage aging heat treatment, wherein the first-stage aging heat treatment insulation temperature is 120°C, the first-stage aging heat treatment insulation time is 8 hours, the second-stage aging heat treatment insulation temperature is 170°C, the second-stage aging heat treatment insulation time is 2 hours, and after the second-stage aging heat treatment is naturally cooled to room temperature, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material is prepared. The upper limit of the service temperature of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material is 350°C.

[0088] The Al-SiC-based master alloy in the batching and weighing steps is formed by pressing Al powder and SiC powder, wherein the mass proportion of SiC powder in the Al-SiC-based master alloy is 20%, the particle size of Al powder is 120 μm, and the particle size of SiC powder is 50 μm; the Al-Al9FeNi-based master alloy is formed by pressing Al powder and Al9FeNi powder, wherein the mass proportion of Al9FeNi powder in the Al-Al9FeNi-based master alloy is 5%, the particle size of Al powder is 120 μm, and the particle size of Al9FeNi powder is 150 μm; the specification of the Al-Ti-C master alloy is wire, the wire diameter is 4 mm, and the added mass of the Al-Ti-C master alloy accounts for 0.12% of the total weight of the melt.

[0089] Table 1 Comparison of comprehensive properties of Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 1 and ZL114A alloy

[0090] Comparative Example 1 The other operations are the same as those in Example 1, except that the Al-SiC-based master alloy and the Al-Al9FeNi-based master alloy are not added during the batching process: (1) Batching and weighing: According to the component proportions of the above-mentioned Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, high-purity aluminum ingots, high-purity magnesium ingots, Al-20Cu master alloys, Al-10Mn master alloys, Al-10Ni master alloys, Al-12Si master alloys, Al-6Ce master alloys, Al-5La master alloys, Al-10Ag master alloys, Al-4Zr master alloys, Al-2Sc master alloys, Al-6Fe master alloys and Al-Ti-C master alloys are weighed.

[0091] Table 2 Comparison of mechanical properties of heat-resistant aluminum alloys prepared in Example 1 and Comparative Example 1

[0092] Comparative Example 2 The other operations are the same as those in Example 1, except that the temperature during the melting process is different: (2) Melting: Place high-purity aluminum ingots, Al-20Cu master alloy, Al-10Mn master alloy, Al-10Ni master alloy, Al-12Si master alloy, Al-6Ce master alloy, Al-5La master alloy, Al-10Ag master alloy, Al-4Zr master alloy, Al-2Sc master alloy, Al-6Fe master alloy, Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy into a graphite crucible and heat to 760°C until the high-purity aluminum The ingots, Al-20Cu master alloy, Al-10Mn master alloy, Al-10Ni master alloy, Al-12Si master alloy, Al-6Ce master alloy, Al-5La master alloy, Al-10Ag master alloy, Al-4Zr master alloy, Al-2Sc master alloy, Al-6Fe master alloy, Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are melted; the temperature is lowered to 730° C., a high-purity magnesium ingot is added into a graphite crucible, and a slag spoon is used to stir until the high-purity magnesium ingot is completely melted to obtain an alloy melt.

[0093] Table 3 Comparative effect of heat-resistant phase volume fraction of heat-resistant aluminum alloy prepared in Example 1 and Comparative Example 2

[0094] Example 2 The present embodiment provides an Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, which includes the following components in percentage by mass: 6.5% Cu element, 2.3% Mg element, 0.56% Mn element, 0.82% Ni element, 0.35% Ce element, 0.15% La element, 0.26% Ag element, 0.15% Zr element, 0.14% Sc element, 0.88% Fe element, 0.43% Si element, 0.3% SiC particles, and the remainder is Al and unavoidable impurity components.

[0095] The preparation method of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material comprises the following steps: (1) Ingredients and weighing: according to the composition ratio of the above-mentioned Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, high-purity aluminum ingots, high-purity magnesium ingots, Al-20Cu master alloy, Al-10Mn master alloy, Al-10Ni master alloy, Al-12Si master alloy, Al-6Ce master alloy, Al-5La master alloy, Al-10Ag master alloy, Al-4Zr master alloy, Al-2Sc master alloy, Al-6Fe master alloy, Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are weighed; the above-mentioned raw materials are washed with high-pressure industrial tap water to remove oil stains on the surface of the raw materials, and then baked in a baking furnace at 120° C. for 20 minutes for drying and dehydration; (2) Melting: Place high-purity aluminum ingot and Al-20Cu master alloy into a graphite crucible. The graphite crucible is heated by resistance heating and heated to 780°C until the high-purity aluminum ingot and Al-20Cu master alloy are completely melted. Continue to heat to 800°C, add Al-10Ni master alloy, Al-12Si master alloy, Al-6Fe master alloy and Al-10Ag master alloy into the graphite crucible, and stir the alloy melt with a slag spoon until Al-10Ni master alloy, Al-12Si master alloy, Al-6Fe master alloy and Al-10Ag master alloy are completely melted. Cool down to 760°C, add Al-10Mn master alloy, Al-6Ce master alloy and Al-5La master alloy into the graphite crucible. , Al-4Zr master alloy and Al-2Sc master alloy, and use a slag spoon to continuously stir the alloy melt until the Al-10Mn master alloy, Al-6Ce master alloy, Al-5La master alloy and Al-4Zr master alloy are completely melted; continue to cool to 750°C, add Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy into a graphite crucible, and use a slag spoon to stir until the Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are completely melted; continue to cool to 740°C, add a high-purity magnesium ingot into a graphite crucible, and use a slag spoon to stir until the high-purity magnesium ingot is completely melted to obtain an alloy melt; (3) Refining: controlling the temperature of the alloy melt at 745°C, adding a refining agent to refine the alloy melt for 15 minutes; the refining agent in the refining step is composed of CaF2, MgCl2, KCl and KNO3, wherein CaF2 accounts for 50% of the total weight of the refining agent, MgCl2 accounts for 30% of the total weight of the refining agent, KCl accounts for 12% of the total weight of the refining agent, and KNO3 accounts for 8% of the total weight of the refining agent; the refining agent accounts for 0.35% of the total weight of the alloy melt, and when adding the refining agent, a bell jar is used to press the bottom of the alloy melt in the graphite crucible, and after the bell jar is pressed into the alloy melt, the alloy melt is allowed to stand for 5 minutes, and then the bell jar is taken out to stir the alloy melt for 10 minutes; (4) Degassing: The temperature of the alloy melt is controlled at 740°C, and a composite degassing process is used for degassing. Argon and nitrogen are first introduced for rotary spraying degassing. The rotary spraying time is 10 minutes, and the gas volume ratio of argon and nitrogen is 4:1; then the temperature is lowered to 735°C, and a solid powder degassing agent is added for degassing for 15 minutes. The solid powder degassing agent in the degassing step is composed of C2Cl6, TiO2 and CaO, wherein C2Cl6 accounts for 65% of the total weight of the solid powder degassing agent and has a particle size of 120 μm; TiO2 accounts for 25% of the total weight of the solid powder degassing agent and has a particle size of 80 μm; CaO accounts for 10% of the total weight of the solid powder degassing agent and has a particle size of 200 μm; the solid powder degassing agent is wrapped with aluminum foil before being added to the alloy melt, and then baked at a temperature range of 150°C for 30 minutes after wrapping; (5) Casting: After the alloy melt is refined and degassed, it is allowed to stand in a graphite crucible for 5 minutes and then cast in an investment shell mold at a casting temperature of 680°C. In the casting step, a double-stage ceramic filter is used to filter and purify the alloy melt before casting. The ceramic filter is made of Y2O3, and the specification of the first-stage ceramic filter is 20PPI and the thickness is 20mm; the specification of the second-stage ceramic filter is 40PPI and the thickness is 25mm. (6) Heat treatment: After the alloy melt is cast, it is naturally cooled and then taken out from the investment shell mold. The heat-resistant aluminum alloy material is subjected to a solution heat preservation treatment in a solution heat preservation furnace. The solution heat preservation temperature is 540°C, the solution heat preservation time is 10 hours, the quenching transfer time is 12 seconds, the quenching medium is industrial tap water, and the quenching medium temperature is 50°C. After the solution heat preservation, the heat-resistant aluminum alloy material is subjected to a two-stage aging heat treatment, wherein the first-stage aging heat treatment insulation temperature is 140°C, the first-stage aging heat treatment insulation time is 10 hours, the second-stage aging heat treatment insulation temperature is 190°C, the second-stage aging heat treatment insulation time is 4 hours, and after the second-stage aging heat treatment is naturally cooled to room temperature, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material is prepared. The upper limit of the service temperature of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material is 350°C.

[0096] The Al-SiC-based master alloy in the batching and weighing steps is formed by pressing Al powder and SiC powder, wherein the mass proportion of SiC powder in the Al-SiC-based master alloy is 60%, the particle size of Al powder is 200 μm, and the particle size of SiC powder is 100 μm; the Al-Al9FeNi-based master alloy is formed by pressing Al powder and Al9FeNi powder, wherein the mass proportion of Al9FeNi powder in the Al-Al9FeNi-based master alloy is 10%, the particle size of Al powder is 200 μm, and the particle size of Al9FeNi powder is 250 μm; the specification of the Al-Ti-C master alloy is wire, the wire diameter is 6 mm, and the added mass of the Al-Ti-C master alloy accounts for 0.18% of the total weight of the melt.

[0097] Table 4 Comparison of comprehensive properties of Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 2 and ZL205A alloy

[0098] Example 3 The present embodiment provides an Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, which includes the following components in percentage by mass: 7.9% Cu element, 2.4% Mg element, 0.64% Mn element, 0.56% Ni element, 0.29% Ce element, 0.18% La element, 0.28% Ag element, 0.12% Zr element, 0.13% Sc element, 0.98% Fe element, 0.29% Si element, 0.5% SiC particles, and the remainder is Al and unavoidable impurity components.

[0099] (1) Ingredients and weighing: according to the composition ratio of the above-mentioned Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, high-purity aluminum ingots, high-purity magnesium ingots, Al-20Cu master alloy, Al-10Mn master alloy, Al-10Ni master alloy, Al-12Si master alloy, Al-6Ce master alloy, Al-5La master alloy, Al-10Ag master alloy, Al-4Zr master alloy, Al-2Sc master alloy, Al-6Fe master alloy, Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are weighed; the above-mentioned raw materials are washed with high-pressure industrial tap water to remove oil stains on the surface of the raw materials, and then baked in a baking furnace at 110° C. for 18 minutes for drying and dehydration; (2) Melting: Place high-purity aluminum ingot and Al-20Cu master alloy into a graphite crucible, heat the graphite crucible with gas, and heat it to 770°C until the high-purity aluminum ingot and Al-20Cu master alloy are completely melted; continue to heat it to 790°C, add Al-10Ni master alloy, Al-12Si master alloy, Al-6Fe master alloy and Al-10Ag master alloy into the graphite crucible, and stir the alloy melt with a slag spoon until the Al-10Ni master alloy, Al-12Si master alloy, Al-6Fe master alloy and Al-10Ag master alloy are completely melted; cool it to 755°C, add Al-10Mn master alloy, Al-6Ce master alloy, Al-5La master alloy into the graphite crucible, and stir the alloy melt with a slag spoon. Gold, Al-4Zr master alloy and Al-2Sc master alloy, and stir the alloy melt with a slag spoon until the Al-10Mn master alloy, Al-6Ce master alloy, Al-5La master alloy and Al-4Zr master alloy are completely melted; continue to cool to 745°C, add Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy in a graphite crucible, and stir with a slag spoon until the Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are completely melted; continue to cool to 735°C, add a high-purity magnesium ingot in the graphite crucible, and stir with a slag spoon until the high-purity magnesium ingot is completely melted to obtain an alloy melt; (3) Refining: controlling the temperature of the alloy melt at 740°C, adding a refining agent to refine the alloy melt for 12 minutes; the refining agent in the refining step is composed of CaF2, MgCl2, KCl and KNO3, wherein CaF2 accounts for 47% of the total weight of the refining agent, MgCl2 accounts for 27% of the total weight of the refining agent, KCl accounts for 11% of the total weight of the refining agent, and KNO3 accounts for 15% of the total weight of the refining agent; the refining agent accounts for 0.30% of the total weight of the alloy melt, and when adding the refining agent, a bell jar is used to press the bottom of the alloy melt in the graphite crucible, and after the bell jar is pressed into the alloy melt, the alloy melt is allowed to stand for 4.5 minutes, and then the bell jar is taken out to stir the alloy melt for 9 minutes; (4) Degassing: The temperature of the alloy melt is cooled to 735°C, and a composite degassing process is used for degassing. Argon and nitrogen are first introduced for rotary spraying degassing. The rotary spraying time is 8 minutes, and the gas volume ratio of argon and nitrogen is 3.5:1; then the temperature is cooled to 730°C and a solid powder degassing agent is added for degassing for 12 minutes; the solid powder degassing agent in the degassing step is composed of C2Cl6, TiO2 and CaO, C2Cl6 accounts for 64% of the total weight of the solid powder degassing agent, and the particle size is 90 μm; TiO2 accounts for 22% of the total weight of the solid powder degassing agent, and the particle size is 60 μm; CaO accounts for 14% of the total weight of the solid powder degassing agent, and the particle size is 160 μm; before adding the solid powder degassing agent to the alloy melt, it is wrapped with aluminum foil and baked at a temperature range of 120°C for 25 minutes after wrapping; (5) Casting: After the alloy melt is refined and degassed, it is allowed to stand in a graphite crucible for 14 minutes and then cast in a metal mold at a casting temperature of 665°C. In the casting preparation step, a double-stage ceramic filter is used to filter and purify the alloy melt before casting. The ceramic filter is made of Y2O3, and the specification of the first-stage ceramic filter is 20PPI and the thickness is 20mm; the specification of the second-stage ceramic filter is 25PPI and the thickness is 20mm. (6) Heat treatment: After the alloy melt is cast, it is naturally cooled and then the heat-resistant aluminum alloy material is taken out from the metal mold. The heat-resistant aluminum alloy material is subjected to a solution heat preservation treatment in a solution heat preservation furnace. The solution heat preservation temperature is 530°C, the solution heat preservation time is 8h, the quenching transfer time is 12s, the quenching medium is industrial tap water, and the quenching medium temperature is 35°C. After the solution heat preservation, the heat-resistant aluminum alloy material is subjected to a two-stage aging heat treatment, wherein the first-stage aging heat treatment insulation temperature is 130°C, the first-stage aging heat treatment insulation time is 9h, the second-stage aging heat treatment insulation temperature is 180°C, the second-stage aging heat treatment insulation time is 3h, and after the second-stage aging heat treatment is naturally cooled to room temperature, the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material is prepared. The upper limit of the service temperature of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material is 350°C.

[0100] The Al-SiC-based master alloy in the batching and weighing steps is formed by pressing Al powder and SiC powder, wherein the mass proportion of SiC powder in the Al-SiC-based master alloy is 40%, the particle size of Al powder is 160 μm, and the particle size of SiC powder is 80 μm; the Al-Al9FeNi-based master alloy is formed by pressing Al powder and Al9FeNi powder, wherein the mass proportion of Al9FeNi powder in the Al-Al9FeNi-based master alloy is 8%, the particle size of Al powder is 180 μm, and the particle size of Al9FeNi powder is 200 μm; the specification of the Al-Ti-C master alloy is wire, the wire diameter is 5 mm, and the added mass of the Al-Ti-C master alloy accounts for 0.15% of the total weight of the melt.

[0101] Table 5 Comparison of comprehensive properties of Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy prepared in Example 3 and A319 alloy

[0102] The above is an explanation of the embodiments of the present invention. However, the present invention is not limited to the above embodiments. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present invention shall be included in the protection scope of the present invention.

Claims

1. An Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, wherein: The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material includes the following components in percentage by mass: 5.0%-8.0% Cu element, 1.2%-2.4% Mg element, 0.4%-0.8% Mn element, 0.4%-1.0% Ni element, 0.2%-0.4% Ce element, 0.1%-0.2% La element, 0.2%-0.3% Ag element, 0.1%-0.15% Zr element, 0.1%-0.15% Sc element, 0.6%-1.0% Fe element, 0.2%-0.5% Si element, 0.2%-0.5% SiC particles, and the balance is Al and unavoidable impurity components.

2. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material according to claim 1, wherein: The mass ratio of the Ce element to the La element is 1.38-2.36; and / or, the mass ratio of the Zr element to the Sc element is 0.75-1.35; and / or, the mass ratio of the Cu element to the Mg element is 2.55-3.15; and / or, the mass ratio of the Mn element to the Fe element is 0.45-0.65; and / or, the mass ratio of the Mg element to the Si element is 5.0-8.5; and / or, the mass ratio of the Fe element to the Ni element is 0.75-1.

75.

3. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material according to claim 1, wherein: The raw materials for preparing the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material include Al-SiC-based master alloy and Al-Al9FeNi-based master alloy.

4. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material according to claim 3, wherein: The Al-SiC-based master alloy is formed by pressing Al powder and SiC powder; the mass of the SiC powder in the Al-SiC-based master alloy accounts for 20%-60% of the total mass of the Al-SiC-based master alloy; the mass of the Al powder in the Al-SiC-based master alloy accounts for 40%-80% of the total mass of the Al-SiC-based master alloy; the particle size of the Al powder is 120μm-200μm, and the particle size of the SiC powder is 50μm-100μm; The Al-Al9FeNi-based master alloy is formed by pressing Al powder and Al9FeNi powder; the mass of the Al9FeNi powder in the Al-Al9FeNi-based master alloy accounts for 5%-10% of the total mass of the Al-Al9FeNi-based master alloy; the mass of the Al powder in the Al-Al9FeNi-based master alloy accounts for 90%-95% of the total mass of the Al-Al9FeNi-based master alloy; the particle size of the Al powder is 120μm-200μm, and the particle size of the Al9FeNi powder is 150μm-250μm.

5. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material according to claim 1, wherein: The grain boundary phases of the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material include Al9FeNi phase, SiC phase, Al2Cu phase, Al6Mn phase, Al 11 Ce3 phase, Al2CuMg phase and Al3Zr phase; the volume fraction of the Al9FeNi phase accounts for 0.24%-0.30% of the total volume fraction of all phases, the volume fraction of the SiC phase accounts for 0.08%-0.12% of the total volume fraction of all phases, the volume fraction of the Al2Cu phase accounts for 0.32%-0.35% of the total volume fraction of all phases, the volume fraction of the Al6Mn phase accounts for 0.08%-0.10% of the total volume fraction of all phases, the Al 11 The volume fraction of the Ce3 phase accounts for 0.12%-0.15% of the total volume fraction of all phases, the volume fraction of the Al2CuMg phase accounts for 0.28%-0.32% of the total volume fraction of all phases, and the volume fraction of the Al3Zr phase accounts for 0.18%-0.24% of the total volume fraction of all phases.

6. The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material according to any one of claims 1 to 5, wherein: The Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material has a room temperature tensile strength of ≥400MPa, a room temperature yield strength of ≥340MPa, and a room temperature material elongation of ≥5% after double-stage aging heat treatment; a high temperature tensile strength of ≥280MPa at 200°C, and a high temperature tensile strength of ≥220MPa at 300°C; a steady-state creep rate ε at 300°C / 100MPa • ≤1×10 -8 s -1 ;350℃ oxidation weight gain rate ≤0.18mg·cm -2 ·h -1 ; 250℃ creep strength limit σ 0.2 / 100 ≥120MPa, 300℃ creep strength limitσ 0.2 / 100 ≥80MPa.

7. A method for preparing the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material according to any one of claims 1 to 6, the method comprising the following steps: (1) Ingredients and weighing: according to the composition ratio of the above Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material, weigh high-purity aluminum ingots, high-purity magnesium ingots, Al-Cu master alloys, Al-Mn master alloys, Al-Ni master alloys, Al-Si master alloys, Al-Ce master alloys, Al-La master alloys, Al-Ag master alloys, Al-Zr master alloys, Al-Sc master alloys, Al-Fe master alloys, Al-SiC-based master alloys, Al-Al9FeNi-based master alloys and Al-Ti-C master alloys; (2) Melting: Mix the high-purity aluminum ingot and the Al-Cu master alloy, and heat them to 760℃-780℃ until the high-purity aluminum ingot and the Al-Cu master alloy are completely melted; continue to heat them to 780℃-800℃, add Al-Ni master alloy, Al-Si master alloy, Al-Fe master alloy and Al-Ag master alloy, and stir until the Al-Ni master alloy, Al-Si master alloy, Al-Fe master alloy and Al-Ag master alloy are completely melted; cool them to 750℃-760℃, add Al-Mn master alloy, Al-Ce master alloy, Al-La master alloy, Al-Zr master alloy, and Gold and Al-Sc master alloy, stirring until Al-Mn master alloy, Al-Ce master alloy, Al-La master alloy, Al-Zr master alloy and Al-Sc master alloy are completely melted; continue to cool to 740°C-750°C, add Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy, stirring until Al-SiC-based master alloy, Al-Al9FeNi-based master alloy and Al-Ti-C master alloy are completely melted; continue to cool to 730°C-740°C, add high-purity magnesium ingot, stir until the high-purity magnesium ingot is completely melted, and obtain an alloy melt; (3) Refining: Control the temperature of the alloy melt at 735°C-745°C, add a refining agent, and perform a refining treatment on the alloy melt; (4) Degassing: The temperature of the alloy melt is lowered to 730°C-735°C, argon and nitrogen are first introduced for rotary spray degassing, and then the temperature of the alloy melt is lowered to 725°C-730°C, a solid powder degassing agent is added, and the alloy melt is degassed by solid powder; (5) Casting: Let the degassed alloy melt stand for 10-15 minutes before casting; (6) Heat treatment: After the alloy melt is cast, the heat-resistant aluminum alloy material is taken out after cooling, and the heat-resistant aluminum alloy material is subjected to solid solution quenching treatment and aging heat treatment to prepare the Al-Cu-Mg-Mn-Ni-Si heat-resistant aluminum alloy material.

8. The preparation method according to claim 7, wherein: In step (2), the amount of the Al-Ti-C master alloy added is 0.12%-0.18% of the total mass of the alloy melt; In step (3), the refining treatment time is 10min-15min; In step (3), the refining agent includes CaF2, MgCl2, KCl and KNO3; Among them, the mass of CaF2 accounts for 45%-50% of the total mass of the refining agent; the mass of MgCl2 accounts for 25%-30% of the total mass of the refining agent; the mass of KCl accounts for 10%-12% of the total mass of the refining agent; the mass of KNO3 accounts for 8%-20% of the total mass of the refining agent; In step (3), the mass of the refining agent accounts for 0.25%-0.35% of the total mass of the alloy melt.

9. The preparation method according to claim 7 or 8, wherein: In step (4), the time of the rotary spraying is 5 min-10 min; In step (4), the solid powder is degassed for 10 min to 15 min; In step (4), the solid powder degassing agent includes C2Cl6, TiO2 and CaO; Among them, the mass of C2Cl6 accounts for 60%-65% of the total mass of the solid powder degassing agent; the mass of TiO2 accounts for 20%-25% of the total mass of the solid powder degassing agent; the mass of CaO accounts for 10%-20% of the total mass of the solid powder degassing agent; the particle size of C2Cl6 is 60μm-120μm; the particle size of TiO2 is 50μm-80μm; the particle size of CaO is 120μm-200μm; In step (4), the mass of the solid powder degassing agent accounts for 0.25%-0.35% of the total mass of the alloy melt.

10. The preparation method according to claim 7 or 8, wherein: In step (5), the casting temperature is 650°C-680°C; In step (5), before casting, a double-stage ceramic filter is used to filter and purify the alloy melt before the furnace; the material of the ceramic filter is Al2O3 or Y2O3, the specification of the first-stage ceramic filter is 15PPI-20PPI, and the thickness is 15mm-20mm; the specification of the second-stage ceramic filter is 25PPI-40PPI, and the thickness is 20mm-25mm; In step (6), the solution temperature is 520°C-540°C; the solution time is 6h-10h; In step (6), the aging heat treatment is a two-stage aging heat treatment system, the first-stage aging heat treatment insulation temperature is 120°C-140°C, the first-stage aging heat treatment insulation time is 8h-10h, the second-stage aging heat treatment insulation temperature is 170°C-190°C, the second-stage aging heat treatment insulation time is 2h-4h, and the second-stage aging heat treatment is naturally cooled to room temperature after completion.

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