A method for printing and heat treating a GH4061 alloy powder

Abstract

The present application relates to a kind of GH4061 alloy powder printing forming and heat treatment method.The method includes the following steps: preparing GH4061 alloy powder, the GH4061 alloy powder includes Ni 50-60%, Cr 15-18%, Fe 12-14%, Mo 2-5%, Nb 3-8%, Al 1-2%, Ti 0-3%, Cu 0-1%, V 0-1%, C 0.03-0.08%, B 0.005-0.01% by mass fraction, the balance is inevitable impurity;The powder is printed forming using selective laser melting process, and printing parameter includes substrate preheating temperature 50-200 ℃, laser power 190-350 W, scanning speed 600-2000 mm / s, scanning interval 0.06-0.18 mm, layer thickness 0.03-0.06 mm;Formed piece is sequentially subjected to homogenization treatment, solution treatment and two-stage aging treatment.

Description

Technical Field

[0001] This invention relates to the field of high-temperature alloy additive manufacturing technology, specifically to a method for printing and heat treatment of GH4061 alloy powder, and more particularly to a synergistic method for preparing, printing, and heat treating GH4061 alloy powder suitable for selective laser melting additive manufacturing. Background Technology

[0002] GH4061 is a high-performance iron-nickel-based superalloy with high high-temperature strength and good microstructural stability, making it suitable for high-temperature service applications such as hot-end components of commercial aerospace rocket engines. Traditional forging and casting processes suffer from difficulties in forming complex and irregularly shaped structural parts and low material utilization. Therefore, additive manufacturing has gradually become an important manufacturing direction for complex high-temperature alloy components.

[0003] However, existing GH4061 alloy powder printing and heat treatment co-processing still has the following shortcomings: First, the powder quality is unstable and has poor adaptability; printing parameters lack targeted optimization, easily leading to defects such as porosity and cracks, and insufficient forming accuracy for complex structures. Second, the heat treatment process largely borrows from traditional alloy solutions, failing to match the characteristics of the printed microstructure, making it difficult to effectively eliminate harmful phases and uniformly control the strengthening phase, resulting in poor performance stability. Third, the printing process and heat treatment system are disconnected, failing to fully consider the impact of powder characteristics on microstructure and properties, making it difficult to achieve precise control of microstructure and properties. Existing processes also suffer from insufficient standardization, significant powder waste, high production costs, an imperfect testing and evaluation system, and low product qualification rates, making it difficult to meet the high-performance and large-scale manufacturing requirements of core components for commercial aerospace.

[0004] Therefore, it is necessary to provide a GH4061 alloy powder printing and heat treatment method for additive manufacturing, so as to achieve a comprehensive improvement in powder compatibility, printing quality, heat treatment microstructure uniformity and high-temperature mechanical properties. Summary of the Invention

[0005] The purpose of this invention is to provide a method for powder printing and heat treatment of GH4061 alloy to solve the problems of insufficient powder compatibility, unreasonable printing process parameters, uneven microstructure in the printed state, and mismatch between heat treatment regime and microstructure characteristics in the existing additive manufacturing of GH4061 alloy, thereby obtaining a formed part with high forming quality and good mechanical properties at room temperature and 720℃.

[0006] According to one aspect of the present invention, a GH4061 alloy powder printing and heat treatment method, which can achieve the foregoing and other objectives and advantages, includes the following steps: GH4061 alloy powder was prepared. The GH4061 alloy powder used nickel as a matrix and adopted a multi-element synergistic strengthening design. Its chemical composition, by mass fraction, was as follows: Ni 50-60%, Cr 15-18%, Fe 12-14%, Mo 2-5%, Nb 3-8%, Al 1-2%, Ti 0-3%, Cu 0-1%, V 0-1%, C 0.03-0.08%, B 0.005-0.01%, with the balance being unavoidable impurities. Among the unavoidable impurities, O≤0.01%, N≤0.01%, P≤0.002%, and S<0.001%.

[0007] The preparation method of the GH4061 alloy powder includes: placing all component metal raw materials in a vacuum induction furnace for melting at a melting temperature of 1500-1600℃ and holding for 20-30 minutes; transferring the molten metal into an atomizing tank and atomizing powder under argon protection at an atomization pressure of 2.7-3.4 MPa; and then using an ultrasonic vibrating sieve to sieve and classify the atomized metal powder to obtain alloy powder with a particle size range of 15-53 μm.

[0008] The GH4061 alloy powder was printed using additive manufacturing equipment. A model of the part to be printed was created in 3D design software, and supports were added and sliced. The part was then formed using a layer-by-layer melting and solidification process. The layer-by-layer melting and solidification forming was preferably performed using selective laser melting printing, with the laser being a 1000-1100nm infrared laser. The printing process parameters were: substrate preheating temperature 50-200℃, laser power 190-350W, scanning speed 600-2000mm / s, scanning spacing 0.06-0.18mm, and layer thickness 0.03-0.06mm.

[0009] The GH4061 alloy component after printing is subjected to heat treatment. The heat treatment includes the following steps: Homogenization treatment: Hold at 1080-1180℃ for 5-20 hours, then cool to room temperature with the furnace; Solution treatment: Heat to 1020-1070℃ at a rate of 5-10℃ / min, hold for 60-90min, and then air cool; Two-stage aging treatment: the first stage of aging involves holding at 700-750℃ for 8-20 hours, followed by cooling down to 600-650℃ at a rate of 50℃ / h; the second stage of aging involves holding at 600-650℃ for 8-10 hours, followed by air cooling to room temperature.

[0010] Compared with existing technologies, this invention has at least the following beneficial effects: First, this invention adopts a multi-component synergistic composition system, in which Nb synergistically forms a dispersed strengthening phase with Al and Ti, C forms stable carbides with Nb and Ti, and B is beneficial to improving grain boundary properties, thereby achieving a synergistic improvement of matrix strengthening, precipitation strengthening, and grain boundary strengthening; at the same time, strictly controlling the content of impurities such as O, N, P, and S helps to reduce inclusion defects and improve powder purity and the performance stability of the formed parts. Second, this invention optimizes SLM printing parameters, enabling GH4061 alloy powder to achieve crack-free, crack-free, and highly dense forming; examples show that the density of the formed parts can reach 99.2%. Third, this invention adopts a three-stage heat treatment process of "homogenization-solution-two-stage aging", in which homogenization treatment helps to eliminate the harmful Laves phase, solution treatment helps the strengthening phase to fully dissolve into the matrix, and two-stage aging helps to promote the dispersed precipitation of the γ' phase, thereby improving the uniformity of the printed microstructure and improving the stability of mechanical properties. Fourth, the examples and comparative data show that the room temperature and high temperature tensile properties of the molded parts obtained within the window of the present invention are significantly better than those of the comparative schemes that exceed the parameter window, and the performance differences between the X / Y direction and the Z direction are small, demonstrating better comprehensive mechanical properties and lower anisotropy.

[0011] The further objects and advantages of the invention will become fully apparent from the following description and accompanying drawings. Attached Figure Description

[0012] The technical solution of the present invention will be further described in detail below with reference to the accompanying drawings and embodiments. In the drawings, unless otherwise specified, the same reference numerals are used to denote the same parts. Wherein: Figure 1 This is a powder morphology image of the GH4061 alloy powder prepared in Example 1 of the present invention; Figure 2 This is a SEM image of the printed part obtained in Embodiment 1 of the present invention before heat treatment; Figure 3 This is a SEM image of the printed part obtained in Embodiment 1 of the present invention after heat treatment; Figure 4 This is a SEM image of the printed part obtained in Embodiment 2 of the present invention after heat treatment; Figure 5 This is a SEM image of the printed part obtained in Embodiment 3 of the present invention after heat treatment; Figure 6 This is a SEM image of the printed part obtained in Embodiment 4 of the present invention after heat treatment; Figure 7 This is a SEM image of the printed part obtained in Embodiment 5 of the present invention after heat treatment; Figure 8 This is a SEM image of the printed part obtained in Comparative Example 1 of the present invention after heat treatment; Figure 9 This is a SEM image of the printed part obtained in Comparative Example 2 of the present invention after heat treatment; Figure 10 This is a SEM image of the printed part obtained in Comparative Example 3 of the present invention after heat treatment. Detailed Implementation

[0013] The following description is intended to disclose the present invention and enable those skilled in the art to implement it. The preferred embodiments described below are merely examples, and other obvious variations will occur to those skilled in the art. The basic principles of the invention defined in the following description can be applied to other embodiments, modifications, improvements, equivalents, and other technical solutions that do not depart from the spirit and scope of the invention.

[0014] In this preferred embodiment of the application, the method is determined by combining the printing characteristics of GH4061 alloy powder and the evolution law of the printed microstructure. Regarding the printing process, when the laser power, scanning speed, scanning spacing, and layer thickness are within the range defined by this invention, it is beneficial to achieve a more stable molten pool formation and interlayer fusion, thereby obtaining higher forming quality. If the laser power is too low or the scanning speed is too low, it is not conducive to balancing forming efficiency and microstructure performance; if the laser power is too high, the scanning speed is too high, the scanning spacing is too large, or the layer thickness is too large, the forming stability decreases, and the room temperature and 720℃ high-temperature tensile properties of the obtained sample are significantly reduced. Regarding heat treatment, homogenization treatment is used to improve the inhomogeneity of the printed microstructure and reduce the influence of segregation and harmful phases; when the homogenization temperature is below 1080℃ or the holding time is insufficient, the microstructure control effect is insufficient; when the homogenization parameters deviate from the range of this invention, it is not conducive to subsequent solution treatment and aging control. Solution treatment and two-stage aging treatment are used to achieve synergistic control of the dissolution and precipitation of strengthening phases; when the solution treatment and aging parameters exceed the range defined by this invention, the comprehensive mechanical properties of the obtained component decrease. The results of the examples and comparative examples show that the printing parameter window and heat treatment parameter window defined in this invention can synergistically improve the microstructure uniformity and mechanical properties of GH4061 alloy components. Example 1

[0015] This embodiment provides a method for GH4061 alloy powder printing and heat treatment.

[0016] The powder composition is designed as follows, by mass fraction: Ni 58.4%, Cr 17.0%, Fe 13.0%, Nb 5.0%, Mo 4.0%, Al 1.2%, Ti 0.5%, Cu 0.5%, V 0.4%, C 0.04%, O 0.01%, N 0.01%, B 0.005%, P 0.002%, S < 0.001%.

[0017] The powder preparation method is as follows: all component metal raw materials are placed in a vacuum induction furnace for melting at 1500℃ and held for 20 minutes; the molten metal is then transferred to an atomizing tank and atomized under argon protection at a gas pressure of 2.7 MPa; the atomized metal powder is then ultrasonically vibrated and classified using 250-mesh and 550-mesh sieves to obtain alloy powder with a particle size range of 15-53 μm. This alloy powder exhibits good flowability, with a Hall flow rate of 14.9 s / 50 g, a sphericity of 0.91, and a hollow powder rate of 0.42%.

[0018] The printing process was performed using an SLM printer with a substrate preheating temperature of 120°C, a laser power of 240W, a scanning speed of 1000mm / s, a scanning spacing of 0.09mm, and a layer thickness of 0.04mm.

[0019] The heat treatment process is as follows: First, the temperature is held at 1180℃ for 15 hours, then cooled to room temperature in the furnace; next, the temperature is increased to 1050℃ at a rate of 10℃ / min, held for 60 minutes, and then air-cooled; then, a two-stage aging treatment is performed: the first stage aging is held at 730℃ for 8 hours, then cooled to 650℃ at a rate of 50℃ / h; the second stage aging is held at 650℃ for 8 hours, then air-cooled to room temperature. The resulting molded part has a density of 99.2%.

[0020] The tensile mechanical properties of the heat-treated specimens were tested at room temperature and at 720℃. The data are shown in Table 1 below. Table 1 Unless otherwise specified, the sampling directions of the samples in Tables 1 to 8 are defined as follows: X / Y direction indicates the direction parallel to the formed substrate, and Z direction indicates the direction along the additive manufacturing deposition construction direction; wherein, Y-1 and Y-2 represent two sets of duplicate samples obtained along the direction parallel to the substrate, and Z-1 and Z-2 represent two sets of duplicate samples obtained along the deposition construction direction, and "-1" and "-2" are only used to distinguish different sample numbers under the same sampling direction.

[0021] The results show that the tensile strength in the X / Y direction is 1242-1243 MPa, the yield strength is 863-864 MPa, and the elongation is 29.0%-30.0%; the tensile strength in the Z direction is 1200-1204 MPa, the yield strength is 828-829 MPa, and the elongation is 31.5%; at 720℃, the tensile strength in the X / Y direction is 866-882 MPa, the yield strength is 716-718 MPa, and the elongation is 11.0%-11.5%; the tensile strength in the Z direction is 860-867 MPa, the yield strength is 712-714 MPa, and the elongation is 11.0%-13.5%. Figure 1As shown, the GH4061 alloy powder prepared in Example 1 has a relatively regular near-spherical morphology, and the powder particles are relatively uniformly distributed. No obvious large proportion of irregular particles or serious satellite powder adhesion phenomenon was observed.

[0022] Combination Figure 2 and Figure 3 It can be seen that the printed GH4061 alloy component has obvious microstructure inhomogeneity; after the three-stage heat treatment of the present invention, the microstructure uniformity is significantly improved, and the effects of segregation and harmful phases are weakened. Example 2

[0023] In this embodiment, the powder composition design and powder preparation method are the same as in Example 1. The printing process uses an SLM printer with a substrate preheating temperature of 120°C, a laser power of 260W, a scanning speed of 1000mm / s, a scanning spacing of 0.09mm, and a layer thickness of 0.04mm. The heat treatment process is as follows: holding at 1150°C for 10 hours, then cooling to room temperature in the furnace; heating to 1050°C at a rate of 10°C / min, holding for 60 minutes, followed by air cooling; first-stage aging at 720°C for 12 hours, then cooling to 650°C at a rate of 50°C / h; second-stage aging at 620°C for 12 hours, followed by air cooling to room temperature. The resulting molded part has a density of 99.2%.

[0024] The tensile mechanical properties of the heat-treated specimens were tested at room temperature and 720℃. The data are shown in Table 2 below. Table 2 Tensile property test results show that the tensile strength in the X / Y direction at room temperature is 1237-1239 MPa, and the tensile strength in the Z direction is 1195-1218 MPa; at 720℃, the tensile strength in the X / Y direction is 818-834 MPa, and the tensile strength in the Z direction is 826-874 MPa. Good plasticity and low anisotropy are observed in all directions. Example 3

[0025] In this embodiment, the powder composition design and powder preparation method are the same as in Example 1. The printing process uses an SLM printer with a substrate preheating temperature of 120°C, a laser power of 280W, a scanning speed of 1000mm / s, a scanning spacing of 0.09mm, and a layer thickness of 0.04mm. The heat treatment process is as follows: holding at 1150°C for 5 hours, then cooling to room temperature in the furnace; heating to 1050°C at a rate of 10°C / min, holding for 60 minutes, followed by air cooling; first-stage aging at 730°C for 15 hours, then cooling to 650°C at a rate of 50°C / hour; second-stage aging at 620°C for 15 hours, followed by air cooling to room temperature. The resulting molded part has a density of 99.2%.

[0026] The tensile mechanical properties of the heat-treated specimens were tested at room temperature and 720℃. The data are shown in Table 3 below. Table 3 Test results show that at room temperature, the X / Y tensile strength is 1273-1275 MPa, the yield strength is 881-883 MPa, and the elongation is 26.5%-27.5%; the Z-direction tensile strength is 1216-1239 MPa, the yield strength is 817-860 MPa, and the elongation is 29.0%-31.5%. At 720℃, the X / Y tensile strength is 866-898 MPa, the yield strength is 745-747 MPa, and the elongation is 12.5%-13.5%; the Z-direction tensile strength is 872-896 MPa, the yield strength is 722-726 MPa, and the elongation is 12.0%-13.0%. Example 4

[0027] In this embodiment, the powder composition design and powder preparation method are the same as in Example 1. The SLM printing process parameters are: substrate preheating temperature 50℃, laser power 190W, scanning speed 600mm / s, scanning spacing 0.06mm, and layer thickness 0.03mm. The heat treatment process is as follows: homogenization is carried out at 1080℃ for 8 hours, followed by furnace cooling to room temperature; the temperature is increased to 1020℃ at a rate of 5℃ / min and held for 90 minutes, followed by air cooling; the first aging process is carried out at 700℃ for 20 hours, followed by cooling to 600℃ at a rate of 50℃ / h; the second aging process is carried out at 600℃ for 10 hours, followed by air cooling to room temperature.

[0028] The heat-treated specimens were subjected to room temperature and 720℃ high-temperature tensile mechanical property tests. The data are shown in Table 4 below. Table 4 Performance test results show that this embodiment can still achieve good room temperature and 720℃ high temperature tensile properties near the lower limit conditions. Example 5

[0029] In this embodiment, the powder composition design and powder preparation method are the same as in Example 1. The SLM printing process parameters are: substrate preheating temperature 200℃, laser power 350W, scanning speed 2000mm / s, scanning spacing 0.18mm, and layer thickness 0.06mm. The heat treatment process is as follows: homogenization is carried out at 1180℃ for 5 hours, followed by furnace cooling to room temperature; the temperature is increased to 1070℃ at a rate of 10℃ / min, held for 60 minutes, and then air-cooled; the first-stage aging is carried out at 750℃ for 8 hours, followed by cooling to 650℃ at a rate of 50℃ / h; the second-stage aging is carried out at 650℃ for 8 hours, followed by air cooling to room temperature.

[0030] The tensile mechanical properties of the heat-treated specimens were tested at room temperature and 720℃. The data are shown in Table 5 below. Table 5 Performance test results show that this embodiment can still achieve good room temperature and 720℃ high temperature tensile properties near the upper limit conditions.

[0031] Combination Figures 4 to 7 It can be seen that within the parameter range defined in Examples 2 to 5 of the present invention, the obtained samples all exhibit a relatively uniform microstructure after heat treatment, which corresponds to their good room temperature and high temperature tensile properties at 720℃.

[0032] Comparative Example 1 In this comparative example, the powder composition design and powder preparation method are the same as in Example 1. The SLM printing process parameters are: substrate preheating temperature 200℃, laser power 380W, scanning speed 2200mm / s, scanning spacing 0.20mm, and layer thickness 0.08mm. The heat treatment process is as follows: homogenization is carried out at 1200℃ for 4 hours, followed by furnace cooling to room temperature; the temperature is increased to 1090℃ at 12℃ / min and held for 50 minutes, followed by air cooling; the first aging is carried out at 770℃ for 6 hours, followed by cooling to 670℃ at 50℃ / h; the second aging is carried out at 670℃ for 6 hours, followed by air cooling to room temperature.

[0033] The heat-treated specimens were subjected to room temperature and 720℃ high-temperature tensile mechanical property tests. The data are shown in Table 6 below. Table 6 Test results show that the tensile properties of this comparative example decreased significantly at both room temperature and 720℃. At room temperature, the X / Y tensile strength was only 765-766 MPa, and the Z tensile strength was 680-682 MPa; at 720℃, the X / Y tensile strength was only 603-605 MPa, and the Z tensile strength was 518-520 MPa.

[0034] Comparative Example 2 In this comparative example, the powder composition design and powder preparation method are the same as in Example 1. The SLM printing process parameters are: substrate preheating temperature 30℃, laser power 160W, scanning speed 500mm / s, scanning spacing 0.04mm, and layer thickness 0.02mm. The heat treatment process is as follows: homogenization is carried out at 1060℃ for 10h, followed by furnace cooling to room temperature; the temperature is increased to 1000℃ at 3℃ / min and held for 100min, followed by air cooling; the first aging is carried out at 680℃ for 22h, followed by cooling to 580℃ at 50℃ / h; the second aging is carried out at 580℃ for 12h, followed by air cooling to room temperature.

[0035] The heat-treated specimens were subjected to room temperature and 720℃ high-temperature tensile mechanical property tests. The data are shown in Table 7 below. Table 7 Test results show that the overall mechanical properties of this comparative example are also significantly inferior to those of the embodiments of the present invention.

[0036] Combination Figure 8 and Figure 9 It can be seen that when the printing parameters and heat treatment parameters exceed the limits of this invention, the resulting sample has a poor microstructure and the corresponding mechanical properties decrease significantly.

[0037] Comparative Example 3 In this comparative example, the powder composition design, powder preparation method, and SLM printing process parameters are the same as in Example 1. The only difference is that the homogenization step is omitted in the heat treatment, and the "solution + two-stage aging" process is directly adopted. That is, the temperature is increased to 1050℃ at 10℃ / min, held for 60min, and then air-cooled; the first-stage aging is held at 730℃ for 8h, and then cooled to 650℃ at 50℃ / h; the second-stage aging is held at 650℃ for 8h, and then air-cooled to room temperature.

[0038] The tensile mechanical properties of the heat-treated specimens were tested at room temperature and 720℃. The data are shown in Table 8 below. Table 8 Combination Figure 10 It can be seen that when the homogenization step is omitted, the microstructure uniformity of the obtained sample is worse than that of Example 1, and the corresponding room temperature and high temperature tensile properties at 720℃ are also significantly reduced, indicating that the homogenization step plays an important role in the microstructure control and performance improvement of the printed GH4061 alloy component.

[0039] Comparative Example 3 shows that when only solution treatment and two-stage aging treatment are used, without homogenization treatment, the room temperature and 720°C high-temperature tensile properties of the obtained component are significantly lower than those of Example 1. This demonstrates that homogenization treatment is not a dispensable routine step, but a crucial process for improving the microstructure and overall mechanical properties of printed GH4061 alloy components.

[0040] By comparing Examples 1 to 5 with Comparative Examples 1 and 2, it can be seen that when the printing parameters and heat treatment parameters are within the range defined by this invention, higher room temperature and 720°C high-temperature tensile properties can be obtained; however, when the parameters exceed the upper limit or fall below the lower limit, the overall material performance decreases significantly. This indicates that the process window defined by this invention is not arbitrarily selected, but rather matched with the printing characteristics and heat treatment microstructure evolution of GH4061 alloy powder.

[0041] Those skilled in the art should understand that the embodiments of the present invention described above and shown in the accompanying drawings are merely examples and do not limit the present invention. The objectives of the present invention have been fully and effectively achieved. The functions and structural principles of the present invention have been demonstrated and explained in the embodiments, and any modifications or variations of the embodiments of the present invention may be made without departing from the stated principles.

Claims

1. A method for GH4061 alloy powder printing and heat treatment, characterized in that, Includes the following steps: S1. Prepare GH4061 alloy powder, wherein the GH4061 alloy powder comprises, by mass fraction: Ni 50-60%, Cr 15-18%, Fe 12-14%, Mo 2-5%, Nb 3-8%, Al 1-2%, Ti 0-3%, Cu 0-1%, V 0-1%, C 0.03-0.08%, B 0.005-0.01%, with the balance being unavoidable impurities; wherein the unavoidable impurities are O≤0.01%, N≤0.01%, P≤0.002%, and S<0.001%; S2. The GH4061 alloy powder is printed into shape using an additive manufacturing process, wherein the additive manufacturing process is selective laser melting printing, and the printing parameters include: substrate preheating temperature 50-200℃, laser power 190-350W, scanning speed 600-2000mm / s, scanning spacing 0.06-0.18mm, and layer thickness 0.03-0.06mm; and S3. The formed part obtained in step S2 is subjected to heat treatment, which includes the following steps in sequence: homogenization treatment: holding at 1080-1180℃ for 5-20h and then cooling to room temperature in the furnace; solution treatment: heating to 1020-1070℃ at 5-10℃ / min, holding for 60-90min and then air cooling; two-stage aging treatment: first-stage aging at 700-750℃ for 8-20h and then cooling to 600-650℃ at 50℃ / h; second-stage aging at 600-650℃ for 8-10h and then air cooling to room temperature.

2. The method according to claim 1, characterized in that, In step S1, the GH4061 alloy powder is prepared by the following steps: all component metal raw materials are placed in a vacuum induction furnace, melted at 1500-1600℃ and held for 20-30 minutes; the melted metal is transferred into an atomizing tank and atomized under argon protection at 2.7-3.4 MPa; the atomized metal powder is sieved and classified to obtain alloy powder with a particle size range of 15-53 μm.

3. The method according to claim 1, characterized in that, In step S1, the particle size range of the GH4061 alloy powder is 15–53 μm.

4. The method according to claim 1, characterized in that, In step S2, the laser used in the selective laser melting printing process is a 1000-1100nm infrared laser.

5. The method according to claim 1, characterized in that, In step S2, the substrate preheating temperature is 120℃, the laser power is 240~280W, the scanning speed is 1000mm / s, the scanning spacing is 0.09mm, and the layer thickness is 0.04mm.

6. The method according to claim 1, characterized in that, In step S3, the homogenization treatment conditions are 1180℃ for 15 hours, the solution treatment conditions are to heat to 1050℃ at 10℃ / min and hold for 60 minutes, the first aging conditions are to hold at 730℃ for 8 hours and then cool down to 650℃ at 50℃ / h, and the second aging conditions are to hold at 650℃ for 8 hours.

7. The method according to claim 1, characterized in that, In step S3, the homogenization treatment conditions are 1150℃ for 10h, the solution treatment conditions are to raise the temperature to 1050℃ at 10℃ / min and hold for 60min, the first aging conditions are to hold at 720℃ for 12h and then lower the temperature to 650℃ at 50℃ / h, and the second aging conditions are to hold at 620℃ for 12h.

8. The method according to claim 1, characterized in that, In step S3, the homogenization treatment conditions are 1150℃ for 5 hours, the solution treatment conditions are to raise the temperature to 1050℃ at 10℃ / min and hold for 60 minutes, the first aging conditions are to hold at 730℃ for 15 hours and then lower the temperature to 650℃ at 50℃ / h, and the second aging conditions are to hold at 620℃ for 15 hours.

9. The method according to claim 1, characterized in that, In step S3, the homogenization treatment temperature is 1150-1180℃, the solution treatment temperature is 1050℃, the first aging temperature is 720-730℃, and the second aging temperature is 620-650℃.

10. The method according to claim 1, characterized in that, In step S2, the substrate preheating temperature is 50-120℃, the laser power is 190-280W, the scanning speed is 600-1000mm / s, the scanning spacing is 0.06-0.09mm, and the layer thickness is 0.03-0.04mm.

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