Preparation method and application of high-strength heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on antiphase domain regulation and control

Abstract

The invention relates to the technical field of high-performance aluminum alloy materials, in particular to a preparation method and application of a high-strength heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on antiphase domain regulation, and the alloy comprises the following components in percentage by mass: 4.51% of Cu, 0.28% of Mg, 0.38% of Y, 0.09% of Zr, 0.39% of Sc, less than or equal to 0.05% of single impurity element, less than or equal to 0.15% of total impurity element and the balance of Al; the microstructure of the alloy is characterized in that a theta'phase is used as a main strengthening phase, and the interface of the theta 'phase is coated with an Al3Zr / Al3Sc / theta' / Al3Sc / Al3Zr composite interface structure; after the alloy is thermally exposed for 300 hours at the temperature of 250 DEG C, the Vickers hardness is still kept above 85 HV and is improved by 54.5% compared with a traditional Al-Cu-Mg alloy (the hardness is about 55 HV under the same condition), the industrial problem that the high-temperature long-term service strength is reduced is thoroughly solved, the (L12, D022)-Al3 (Y, Zr) composite phase capable of regulating and controlling the antiphase domain is constructed through the synergistic effect of Y and Zr for the first time, an interface strengthening mechanism is newly added, and the high-strength Al-Cu-Mg alloy is obtained. And the high-temperature strength and plasticity of the alloy are synergistically improved.

Description

Technical Field

[0001] This invention relates to the field of high-performance aluminum alloy materials technology, specifically to a method for preparing and applying a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation. Background Technology

[0002] Al-Cu-Mg alloys, as typical age-hardening aluminum alloys, are widely used in the aerospace field due to their high specific strength and good machinability. However, existing alloys of this type face the following core technical bottlenecks when serving at high temperatures (250°C and above) for extended periods:

[0003] The heat resistance defects of traditional Al-Cu-Mg alloys: Traditional Al-Cu-Mg alloys are strengthened by precipitating GP zones or θ″ phases through low-temperature aging (around 180℃). However, the metastable GP zones and θ″ phases are prone to rapid coarsening and dissolution above 250℃, or transform into coarse incoherent equilibrium θ phases (Al2Cu), resulting in a sharp decrease in alloy strength (hardness of only about 55HV after 300 hours of heat exposure at 250℃), which cannot meet the requirements for long-term high-temperature service. Moreover, its strengthening phase type is singular, and it lacks an effective mechanism to suppress phase transformation and coarsening.

[0004] Disadvantages of microalloyed alloys with added Sc and Zr: To improve heat resistance, existing technologies use Sc and Zr to form thermally stable Al3(Sc,Zr) nanoparticles, but this method has significant drawbacks: ① Sc is expensive (market price approximately 1000 RMB / g) and can only agglomerate at the θ′ phase coherent interface, failing to suppress radial coarsening at the semi-coherent interface, thus having limited effect on improving the thermal stability of the θ′ phase; ② Zr has an extremely low diffusion rate in the Al matrix (diffusion coefficient ≈ 10 at 300℃). -20 m 2 / s), it is difficult to effectively segregate to the interface within the normal heat exposure time, and it requires an ultra-long heat treatment of more than 2000 hours to play a role, which is not industrially practical; ③ No anti-phase domain boundary control mechanism is introduced, so it is impossible to further improve high-temperature performance through interface strengthening.

[0005] The gap in the application of Y element: In the existing technology, Y element is mostly used as an "impurity purifier" in Al-Cu alloys, and its potential in anti-phase domain boundary regulation and high-temperature strengthening has not been explored. There is a lack of technical solutions for Y and Zr to synergistically form a composite phase to improve thermal stability. To this end, a method for preparing and applying a high-strength and heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation is proposed. Summary of the Invention

[0006] In view of this, the present invention provides a method for preparing and applying a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation. Through composite microalloying and anti-phase domain boundary regulation process, the long-term thermal stability at high temperatures of 250°C and above is significantly improved, which can meet the stringent performance requirements of high-temperature structural components in aerospace, high-end equipment and other fields, thereby solving or alleviating the technical problems existing in the prior art, and at least providing a beneficial option.

[0007] The technical solution of this invention is achieved as follows: a high-strength and heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation, wherein, by mass percentage, the alloy composition includes: Cu 4.51%, Mg 0.28%, Y 0.38%, Zr 0.09%, Sc 0.39%, with individual impurity elements ≤0.05% and total impurity elements ≤0.15%, and the balance being Al;

[0008] The microstructure of the alloy is characterized by: the θ′ phase as the main reinforcing phase, the θ′ phase interface covering the “Al3Zr / Al3Sc / θ′ / Al3Sc / Al3Zr” composite interface structure, and the (L12,D022)-Al3(Y,Zr) composite phase with tunable anti-phase domain boundaries and L12 structure Al3(Sc,Zr) nanoparticles dispersed in the Al matrix.

[0009] The alloy has a Vickers hardness of not less than 85HV after being exposed to heat at 250°C for 300 hours.

[0010] A method for preparing a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation includes the following steps:

[0011] S1: Alloy smelting and casting: According to the composition described in claim 1, pure Al, intermediate alloys Al-50%Cu (wt.%), Al-10%Mg (wt.%), Al-2%Sc (wt.%), Al-10%Zr (wt.%), and Al-5%Y (wt.%) are selected as raw materials, smelted in a vacuum induction furnace under argon protection, and then cast into ingots after ultrasonic-assisted stirring;

[0012] S2: Homogenization heat treatment: The ingot obtained in step S1 is kept at 480℃ for 24 hours, and then water-quenched to room temperature;

[0013] S3: Hot deformation processing: The ingot after homogenization in step S2 is subjected to hot rolling and cold rolling processes in sequence to obtain a plate of a preset thickness;

[0014] S4: Solution treatment: The plate after hot deformation in step S3 is kept at 550-580℃ for 1-3 hours, followed by rapid water quenching;

[0015] S5: Pre-aging treatment: The plate after solution quenching in step S4 is kept at 210℃ for 10-20 hours, and then air-cooled;

[0016] S6: High-temperature aging (core step of anti-phase domain boundary control): The plate after pre-aging in step S5 is subjected to heat exposure treatment at 250°C to induce the formation of (L12,D022)-Al3(Y,Zr) composite phase with controllable anti-phase domain boundaries, thereby obtaining the high-strength heat-resistant alloy.

[0017] More preferably, in step S1, the vacuum degree of the vacuum induction furnace is ≤5×10-3Pa, pure Al is melted first (temperature 750~780℃) during smelting, then intermediate alloy is added sequentially and the temperature is raised to 800~820℃ and held for 30 minutes; the power of ultrasonic assisted stirring is 2kW and the stirring time is 20 minutes; the casting temperature is 680~700℃ and the ingot size is Φ80mm.

[0018] More preferably, in step S3, the hot rolling process is as follows: the ingot is taken out after being held at 450°C for 1 hour, and continuously rolled using a two-roll hot rolling mill with passes of 40mm→20mm→12mm. After each pass, it is returned to the furnace at 450°C for 10 minutes for holding. The cold rolling process is as follows: the 12mm hot-rolled plate is annealed at 450°C for 1 hour, and then continuously rolled using a four-roll cold rolling mill with passes of 12mm→10mm→8mm→6mm→4mm→2mm, finally obtaining a uniform plate with a thickness of 2mm.

[0019] More preferably, in step S4, the cooling rate of rapid water quenching is ≥100℃ / s to ensure the formation of a supersaturated solid solution; the holding time for the solution treatment is preferably 1 to 2.5 hours.

[0020] More preferably, in step S5, the pre-aging treatment holding time is preferably 11 hours, the purpose of which is to directly precipitate high-density, fine θ′ phase (size ≤50nm) and avoid the premature formation of Al3Sc particles by Sc elements, which would otherwise be wasted.

[0021] More preferably, in step S6, the heat exposure treatment time is 300 hours to simulate a long-term high-temperature service scenario; in this step, the Y element first nucleates to form the D022 structure Al3Y, and the Zr element then diffuses into the D022-Al3Y, inducing a partial transformation of the D022 structure to the L12 structure, forming a (L12,D022)-Al3(Y,Zr) composite phase with antiphase domain boundaries.

[0022] An application of a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation, wherein the alloy is used to prepare high-temperature structural components that serve in the temperature range of 200-300℃, specifically including aerospace engine blades, engine casings, and high-speed aircraft skins.

[0023] The embodiments of the present invention have the following advantages due to the adoption of the above technical solutions:

[0024] I. After 300 hours of heat exposure at 250°C, the Vickers hardness of the alloy of this invention remains above 85HV, which is 54.5% higher than that of the traditional Al-Cu-Mg alloy (hardness of about 55HV under the same conditions). This invention completely solves the industry problem of strength decline during long-term high-temperature service. For the first time, through the synergistic effect of Y and Zr, a (L12,D022)-Al3(Y,Zr) composite phase with controllable anti-phase domain boundaries is constructed, and an interface strengthening mechanism is added, which enables the alloy to synergistically improve high-temperature strength and plasticity.

[0025] Second, this invention retains Sc in the matrix through a pre-aging process, increasing Sc utilization by more than 30% and reducing dependence on expensive Sc. Zr plays a role in long-term service through "hysteresis segregation" without the need for ultra-long heat treatment, balancing performance and economy. All preparation steps (melting, homogenization, hot deformation, aging) are based on existing aluminum alloy industrial production lines, without the need for new special equipment (such as ultrasonic stirring can be integrated into existing vacuum induction furnaces). The process has high reliability and can be directly mass-produced.

[0026] Third, the alloy of this invention has significant performance advantages in the temperature range of 200-300℃, which can meet the performance requirements of high-temperature structural components such as aerospace engine blades, casings, and high-speed aircraft skins, filling the application gap of high-performance aluminum alloys in this temperature range.

[0027] The above overview is for illustrative purposes only and is not intended to be limiting in any way. In addition to the illustrative aspects, embodiments, and features described above, further aspects, embodiments, and features of the invention will become readily apparent from the accompanying drawings and the following detailed description. Attached Figure Description

[0028] To more clearly illustrate the technical solutions in the embodiments of this application or the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of this application. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0029] Figure 1 This is a flowchart of the present invention;

[0030] Figure 2 This is a graph showing the hardness change of the alloy of the present invention and the traditional Al-Cu-Mg alloy during heat exposure at 250℃.

[0031] Figure 3 High-resolution transmission electron microscopy (HRTEM) images and energy dispersive spectroscopy (EDS) diagrams of the "Al3Zr / Al3Sc / θ′ / Al3Sc / Al3Zr" composite phase in the alloy of this invention.

[0032] Figure 4 The images show transmission electron microscopy (TEM) images and energy dispersive spectroscopy (EDS) analysis of the (L12,D022)-Al3(Y,Zr) composite phase with tunable anti-domain boundaries in the alloy of this invention. Detailed Implementation

[0033] In the following description, only certain exemplary embodiments are briefly described. As those skilled in the art will recognize, the described embodiments can be modified in various ways without departing from the spirit or scope of the invention. Therefore, the drawings and description are considered to be exemplary in nature and not restrictive.

[0034] The embodiments of the present invention will now be described in detail with reference to the accompanying drawings.

[0035] like Figure 1-4 As shown, this embodiment of the invention provides a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation. By mass percentage, the alloy composition includes: Cu 4.51%, Mg 0.28%, Y 0.38%, Zr 0.09%, Sc 0.39%, with individual impurity elements ≤0.05% and total impurity elements ≤0.15%, and the balance being Al.

[0036] The microstructure of the alloy is characterized by: the θ′ phase as the main reinforcing phase, the θ′ phase interface covering the “Al3Zr / Al3Sc / θ′ / Al3Sc / Al3Zr” composite interface structure, and the (L12,D022)-Al3(Y,Zr) composite phase with tunable anti-phase domain boundaries and L12 structure Al3(Sc,Zr) nanoparticles dispersed in the Al matrix.

[0037] After the alloy is exposed to heat at 250°C for 300 hours, its Vickers hardness is not less than 85HV.

[0038] A method for preparing a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation includes the following steps:

[0039] S1: Alloy smelting and casting: According to the composition of claim 1, pure Al, intermediate alloys Al-50%Cu (wt.%), Al-10%Mg (wt.%), Al-2%Sc (wt.%), Al-10%Zr (wt.%), and Al-5%Y (wt.%) are selected as raw materials, smelted in a vacuum induction furnace under argon protection, and then cast into ingots after ultrasonic-assisted stirring;

[0040] S2: Homogenization heat treatment: The ingot obtained in step S1 is kept at 480℃ for 24 hours, and then water-quenched to room temperature;

[0041] S3: Hot deformation processing: The ingot after homogenization in step S2 is subjected to hot rolling and cold rolling processes in sequence to obtain a plate of a preset thickness;

[0042] S4: Solution treatment: The plate after hot deformation in step S3 is kept at 550-580℃ for 1-3 hours, followed by rapid water quenching;

[0043] S5: Pre-aging treatment: The plate after solution quenching in step S4 is kept at 210℃ for 10-20 hours, and then air-cooled;

[0044] S6: High-temperature aging (core step of anti-phase domain boundary control): The plate after pre-aging in step S5 is subjected to heat exposure treatment at 250℃ to induce the formation of (L12,D022)-Al3(Y,Zr) composite phase with controllable anti-phase domain boundaries, thereby obtaining a high-strength heat-resistant alloy.

[0045] In one embodiment, in step S1, the vacuum degree of the vacuum induction furnace is ≤5×10-3Pa. During melting, pure Al is melted first (temperature 750~780℃), and then intermediate alloy is added sequentially and heated to 800~820℃ and held for 30 minutes. The power of ultrasonic-assisted stirring is 2kW and the stirring time is 20 minutes. The casting temperature is 680~700℃, the ingot size is Φ80mm, and the chemical composition of the alloy is determined by inductively coupled plasma atomic emission spectrometry, as shown in Table 1.

[0046] Table 1. Composition of the aluminum alloy used in the experiment (wt.%)

[0047]

[0048] In one embodiment, in step S3, the hot rolling process is as follows: the ingot is taken out after being held at 450°C for 1 hour, and then continuously rolled using a two-roll hot rolling mill with passes of 40mm→20mm→12mm. After each pass, it is returned to the furnace at 450°C for 10 minutes for holding. The cold rolling process is as follows: the 12mm hot-rolled plate is annealed at 450°C for 1 hour, and then continuously rolled using a four-roll cold rolling mill with passes of 12mm→10mm→8mm→6mm→4mm→2mm, finally obtaining a uniform plate with a thickness of 2mm.

[0049] In one embodiment, in step S4, the rapid water quenching cooling rate is ≥100℃ / s to ensure the formation of a supersaturated solid solution; the holding time for the solution treatment is preferably 1 to 2.5 hours.

[0050] In one embodiment, in step S5, the holding time for the pre-aging treatment is preferably 11 hours, with the aim of directly precipitating a high-density, fine θ′ phase (size ≤50nm) and avoiding the premature formation of Al3Sc particles by Sc elements, which would otherwise be wasted.

[0051] In one embodiment, in step S6, the heat exposure treatment lasts for 300 hours to simulate a long-term high-temperature service scenario. In this step, the Y element first nucleates to form a D022 structure Al3Y, and the Zr element then diffuses into D022-Al3Y, inducing a partial transformation of the D022 structure to the L12 structure, forming a (L12,D022)-Al3(Y,Zr) composite phase with antiphase domain boundaries.

[0052] An application of a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation. The alloy is used to prepare high-temperature structural components that operate in the temperature range of 200–300°C, specifically including aerospace engine blades, engine casings, and high-speed aircraft skins.

[0053] In one embodiment, 10 kg of alloy is prepared as follows:

[0054] Batching and smelting: Weigh 9.42 kg of pure Al (94.20 wt.%), 0.902 kg of Al-50%Cu master alloy (providing 4.51 wt.% Cu), 0.28 kg of Al-10%Mg master alloy (providing 0.28 wt.% Mg), 1.95 kg of Al-2%Sc master alloy (providing 0.39 wt.% Sc), 0.09 kg of Al-10%Zr master alloy (providing 0.09 wt.% Zr), and 0.76 kg of Al-5%Y master alloy (providing 0.38 wt.% Y); In an argon-protected vacuum induction furnace, melt pure Al at 760°C, add the master alloys sequentially, raise the temperature to 810°C and hold for 30 minutes, ultrasonically stir at 2 kW for 20 minutes, and cast into Φ80 mm ingots at 690°C.

[0055] Homogenization treatment: The ingot is placed in a box furnace at 480℃ and held for 24 hours, then water-quenched to room temperature.

[0056] Hot deformation processing: After holding at 450℃ for 1 hour, hot rolling is carried out in passes of 40mm→20mm→12mm (holding for 10 minutes after each pass); 12mm sheet is annealed at 450℃ for 1 hour and then cold rolled in passes of 12mm→10mm→8mm→6mm→4mm→2mm to obtain a 2mm thick sheet.

[0057] Solution treatment: Hold at 560℃ for 2 hours, then rapidly quench in water (cooling rate 120℃ / s).

[0058] Pre-aging treatment: Hold at 210℃ for 11 hours, then air cool.

[0059] High-temperature aging: 250℃ for 300 hours, air-cooled.

[0060] 2. Performance Testing and Result Analysis

[0061] Hardness test: Using an HV-1000 Vickers hardness tester (load 500g, holding pressure 10s), 5 test points were taken at different locations on the alloy, and the average value was 88HV (after 300 hours of heat exposure at 250℃); the hardness of the conventional Al-Cu-Mg alloy in the comparison group was 55HV during the same period, and the hardness of the alloy of this invention was increased by 60%.

[0062] Microstructural characterization: Observation using a Tecnai G2F20 transmission electron microscope (TEM): ① The θ′ phase interface clearly shows the “Al3Zr / Al3Sc / θ′ / Al3Sc / Al3Zr” composite structure (e.g., Figure 2 As shown), the θ′ phase size only increases to 52 nm; ② The Al matrix contains a (L12,D022)-Al3(Y,Zr) composite phase with tunable antiphase domain boundaries (as shown). Figure 3 As shown), the antiphase domain boundary spacing is about 2 nm; ③ L12-Al3(Sc,Zr) nanoparticles with a size of about 15 nm are dispersed in the matrix.

[0063] High-temperature tensile properties: Tensile tests were conducted at 250℃. The tensile strength of the alloy of this invention was 420MPa, the yield strength was 380MPa, and the elongation was 12%. The tensile strength of the traditional Al-Cu-Mg alloy at the same time was 280MPa, the yield strength was 250MPa, and the elongation was 8%. The high-temperature mechanical properties of the alloy of this invention are significantly better.

[0064] The above description is merely a specific embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any person skilled in the art can easily conceive of various variations or substitutions within the technical scope disclosed in the present invention, and these should all be included within the scope of protection of the present invention. Therefore, the scope of protection of the present invention should be determined by the scope of the claims.

Claims

1. A high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation, characterized in that: The alloy composition, by mass percentage, comprises: Cu 4.51%, Mg 0.28%, Y 0.38%, Zr 0.09%, Sc 0.39%, with individual impurity elements ≤0.05% and total impurity elements ≤0.15%, and the balance being Al; The microstructure of the alloy is characterized by: the θ′ phase as the main reinforcing phase, the θ′ phase interface covering the "Al3Zr / Al3Sc / θ′ / Al3Sc / Al3Zr" composite interface structure, and the (L12,D022)-Al3(Y,Zr) composite phase with tunable anti-phase domain boundaries and L12 structure Al3(Sc,Zr) nanoparticles dispersed in the Al matrix. The alloy has a Vickers hardness of not less than 85HV after being exposed to heat at 250°C for 300 hours.

2. A method for preparing a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation, in conjunction with the high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation as described in claim 1, characterized in that: Includes the following steps: S1: Alloy smelting and casting: According to the composition described in claim 1, pure Al, intermediate alloys Al-50%Cu (wt.%), Al-10%Mg (wt.%), Al-2%Sc (wt.%), Al-10%Zr (wt.%), and Al-5%Y (wt.%) are selected as raw materials, smelted in a vacuum induction furnace under argon protection, and then cast into ingots after ultrasonic-assisted stirring; S2: Homogenization heat treatment: The ingot obtained in step S1 is kept at 480℃ for 24 hours, and then water-quenched to room temperature; S3: Hot deformation processing: The ingot after homogenization in step S2 is subjected to hot rolling and cold rolling processes in sequence to obtain a plate of a preset thickness; S4: Solution treatment: The plate after hot deformation in step S3 is kept at 550-580℃ for 1-3 hours, followed by rapid water quenching; S5: Pre-aging treatment: The plate after solution quenching in step S4 is kept at 210℃ for 10-20 hours, and then air-cooled; S6: High-temperature aging (core step of anti-phase domain boundary control): The plate after pre-aging in step S5 is subjected to heat exposure treatment at 250°C to induce the formation of (L12,D022)-Al3(Y,Zr) composite phase with controllable anti-phase domain boundaries, thereby obtaining the high-strength heat-resistant alloy.

3. The method for preparing a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation according to claim 2, characterized in that: In step S1, the vacuum degree of the vacuum induction furnace is ≤5×10-3Pa. During smelting, pure Al is melted first (temperature 750~780℃), and then intermediate alloy is added in sequence and heated to 800~820℃ and held for 30 minutes. The power of ultrasonic assisted stirring is 2kW and the stirring time is 20 minutes. The casting temperature is 680~700℃ and the ingot size is Φ80mm.

4. The method for preparing a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation according to claim 2, characterized in that: In step S3, the hot rolling process is as follows: the ingot is taken out after being held at 450°C for 1 hour, and then continuously rolled using a two-roll hot rolling mill with passes of 40mm→20mm→12mm. After each pass, it is returned to the furnace at 450°C for 10 minutes for holding. The cold rolling process is as follows: the 12mm hot-rolled plate is annealed at 450°C for 1 hour, and then continuously rolled using a four-roll cold rolling mill with passes of 12mm→10mm→8mm→6mm→4mm→2mm, finally obtaining a uniform plate with a thickness of 2mm.

5. The method for preparing a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation according to claim 2, characterized in that: In step S4, the cooling rate of rapid water quenching is ≥100℃ / s to ensure the formation of a supersaturated solid solution; the holding time for the solution treatment is preferably 1 to 2.5 hours.

6. The method for preparing a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation according to claim 2, characterized in that: In step S5, the pre-aging treatment is preferably held for 11 hours to directly precipitate a high-density, fine θ′ phase (size ≤50nm) and avoid the premature formation of Al3Sc particles by Sc elements, which would otherwise be wasted.

7. The method for preparing a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation according to claim 2, characterized in that: In step S6, the heat exposure treatment lasts for 300 hours to simulate a long-term high-temperature service scenario. In this step, the Y element first nucleates to form the D022 structure Al3Y, and the Zr element then diffuses into the D022-Al3Y, inducing a partial transformation of the D022 structure to the L12 structure, forming a (L12,D022)-Al3(Y,Zr) composite phase with antiphase domain boundaries.

8. An application of a high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation, coupled with the preparation method of the high-strength, heat-resistant Al-Cu-Mg-Y-Zr-Sc alloy based on anti-phase domain boundary regulation as described in any one of claims 2-7, characterized in that: The alloy is used to manufacture high-temperature structural components that operate in the temperature range of 200–300°C, specifically including aerospace engine blades, engine casings, and high-speed aircraft skins.

Images