High-thermal-conductivity high-temperature alloy for laser 3D printing and manufacturing method thereof

Abstract

The invention belongs to the field of laser 3D printing nickel-based alloy materials, and particularly provides a laser 3D printing manufacturing method of a high-thermal-conductivity high-temperature alloy. The manufacturing process comprises the steps that GH4169 and CuCrZr alloy powder are mixed, a laser powder bed is adopted for fusion printing, and a printing state nickel base alloy is obtained; the GH4169 alloy powder comprises the following components in percentage by mass: less than or equal to 0.08% of C, 15.0-25.0% of Cr, 50.0-55.0% of Ni, 2-4% of Mo, 4-6% of Nb, 0.8-1.2% of Ti, 0.3-0.7% of Al and the balance of Fe; and the CuCrZr alloy powder comprises the following components in percentage by mass: 0.3 to 0.8 percent of Cr, 0.3 to 0.6 percent of Zr and the balance of Cu. The adding proportion of the CuCrZr alloy powder is 10%-20%; the printing technology specifically comprises the steps that the laser power ranges from 200 W to 400 W, the scanning speed ranges from 600 mm / s to 1500 mm / s, the scanning distance ranges from 0.08 mm to 0.15 mm, and the layer thickness ranges from 80 micrometers to 120 micrometers. Compared with the GH4169 without adding the CuCrZr alloy powder, the heat conductivity of the alloy is improved while the strength of the GH4169 is not reduced, and the alloy has a wide application prospect.

Description

Technical Field

[0001] This invention relates to the field of additive manufacturing of nickel-based alloy materials, and in particular to a high thermal conductivity high-temperature alloy for laser 3D printing and its manufacturing method. Background Technology

[0002] GH4169 alloy manufactured by laser powder bed fusion (LPBF) 3D printing exhibits excellent high-temperature strength and corrosion resistance, and has been applied in high-end equipment fields such as aerospace and energy. Currently, the published patents regarding LPBF manufacturing of GH4169 alloy use relatively small layer thicknesses and powder particle sizes, and mainly focus on traditional mechanical properties.

[0003] Chinese patent CN202311280757.6 discloses a method for improving the strength of laser selective melting of In718 alloy by controlling the Al and C content. This patent uses GH4169 alloy powder with a particle size of 15-53 μm and a maximum layer thickness of only 30 μm. Chinese patent CN202510220672.1 discloses a heat treatment method for laser additive manufacturing of GH4169 nickel-based high-temperature alloy. This patent uses GH4169 alloy with a maximum layer thickness of only 40 μm. Chinese patent CN117758105A discloses ODS / GH4169 composite material, its preparation method, and molded parts. This patent uses GH4169 alloy powder with a particle size of 25-53 μm and a printing layer thickness of only 20-30 μm. The thinner the scanning layer thickness, the more layers are cut at a fixed height, resulting in longer printing times. From a cost perspective, low printing efficiency often leads to equipment usage costs accounting for more than 50% of production costs.

[0004] Thermal conductivity directly determines the heat transfer efficiency and temperature field distribution of components: In aero engines, insufficient thermal conductivity of alloy components can easily lead to local overheating, causing a decline in mechanical properties, thermal stress concentration and cracking failure, threatening equipment safety; In nuclear reactors, heat accumulation not only affects reaction efficiency, but also accelerates material aging, increases maintenance costs and safety risks. Improving the thermal conductivity of alloys helps to solve the heat dissipation problem of key components.

[0005] Therefore, this invention proposes a method for manufacturing GH4169 alloy with higher thermal conductivity to overcome the shortcomings of the prior art. Summary of the Invention

[0006] To address the drawbacks of laser powder bed fusion technology in preparing GH4169 alloy, such as thin printing layers, low printing efficiency, small powder particle size, high preparation cost, and insufficient thermal conductivity, this invention provides a method for preparing a high thermal conductivity high-temperature alloy for laser 3D printing. By using thick, large-particle-size powders and adding CuCrZr alloy powder to the GH4169 alloy raw material powder, a method for preparing a high-density, high-thermal-conductivity, and high-efficiency, low-cost nickel-based alloy material is achieved.

[0007] To achieve the above objectives, the present invention adopts the following technical solution.

[0008] A laser 3D printing manufacturing method for a high thermal conductivity high-temperature alloy includes the following steps: Step 1: Prepare GH4169 alloy powder and CuCrZr alloy powder raw materials; Step 2: GH4169 alloy powder and CuCrZr alloy mixed powder are melted together using a laser powder bed melting method to obtain GH4169 alloy.

[0009] Furthermore, the mass of CuCrZr alloy powder is 10% to 20% of the total mass of the alloy mixed powder.

[0010] Furthermore, the particle size of GH4169 alloy powder is 54~105μm, and the particle size of CuCrZr alloy powder is 54~105μm.

[0011] Furthermore, the process parameters for laser powder bed melting include: laser power of 200~400W, scanning rate of 600~1500mm / s, scanning spacing of 0.08~0.15mm, and layer thickness of 80~120μm.

[0012] Furthermore, the GH4169 alloy powder comprises the following elements: C≤0.08%, Cr: 15.0~25.0%, Ni: 50.0~55.0%, Mo: 2~4%, Nb: 4~6%, Ti: 0.8~1.2%, Al: 0.3~0.7%, with the balance being Fe; the CuCrZr alloy powder comprises the following elements: Cu balance, Cr: 0.3~0.8%, Zr: 0.3~0.6%, where all percentages are mass percentages.

[0013] The above-mentioned GH4169 alloy has a density of ≥99%, a tensile strength of 1013~1189MPa, a yield strength of 655~793MPa, a thermal conductivity of 10.8~15.1, and an elongation of 28.7%~32.5%.

[0014] Compared with the prior art, the beneficial effects of the present invention are as follows.

[0015] This invention optimizes the alloy formula, increases the amount of free electrons in the alloy, and accelerates the heat conduction process with higher electron mobility, breaking through the limitations of low electron mobility and hindered heat transfer in traditional GH4169 alloy, and improving thermal conductivity.

[0016] Compared to the traditional GH4169, the alloy of this invention has a lower liquid-solid transition temperature, a wider solidification temperature range, and a longer liquid-solid transition time. This allows the material to be in a more stable transition state during solidification. At the end of the solidification stage, a low-melting-temperature eutectic phase (γ+Laves) exists, and the liquid and solid phases intertwine, resulting in a large amount of liquid phase that can better fill and connect the voids. This allows the voids to be partially or completely healed through "backfilling," contributing to improved alloy density. On the other hand, the Cu content should not be too high, as excessive Cu content can easily lead to an increase in void defects during the printing process.

[0017] Currently, the most widely researched and applied method for preparing nickel-based alloy powders is the gas atomization method. However, this method suffers from a low yield of fine powder; powder particles smaller than 53 μm account for less than 40% of the total. Therefore, powder particles of 54–105 μm are typically treated as waste powder. This invention uses GH4169 powder with a particle size range of 54–105 μm, fully utilizing the waste powder generated during the current LPBF method for producing GH4169, thus significantly reducing costs. Simultaneously, the use of a larger layer thickness of 70–120 μm also significantly improves printing efficiency.

[0018] Furthermore, according to the material mechanics thermal stress formula σ=αEΔT (where α is the coefficient of linear expansion, E is the elastic modulus, and ΔT is the temperature difference), thermal stress is directly proportional to the temperature difference. Increasing the thermal conductivity to reduce the ΔT of components can effectively alleviate cracking and deformation caused by thermal stress concentration. Attached Figure Description

[0019] To more clearly illustrate the technical solutions of the embodiments of this application, the accompanying drawings used in the embodiments will be further described below.

[0020] Figure 1 The graph shows the relationship between the mechanical properties and density of GH4169 alloys with different CuCrZr contents prepared in this invention.

[0021] Figure 2 The thermal conductivity and density diagrams of GH4169 alloys with different CuCrZr alloy contents prepared according to this invention are shown.

[0022] Figure 3 This is a metallographic molten pool morphology diagram of Embodiment 4 of the present invention. Detailed Implementation

[0023] The present invention is further illustrated below with reference to the specification and embodiments, making its technical content clearer and easier to understand. The present invention can be embodied in many different embodiments, and the scope of protection of the present invention is not limited to the embodiments mentioned herein.

[0024] A laser 3D printing manufacturing method for a high thermal conductivity high-temperature alloy includes the following steps: Step 1: Prepare GH4169 alloy powder and CuCrZr alloy powder raw materials; Step 2: GH4169 alloy powder and CuCrZr alloy mixed powder are melted together using a laser powder bed melting method to obtain GH4169 alloy.

[0025] Furthermore, the mass of CuCrZr alloy powder is 10% to 20% of the total mass of the alloy mixed powder.

[0026] Furthermore, the particle size of GH4169 alloy powder is 54~105μm, and the particle size of CuCrZr alloy powder is 54~105μm.

[0027] Furthermore, the process parameters for laser powder bed melting include: laser power of 200~400W, scanning rate of 600~1500mm / s, scanning spacing of 0.08~0.15mm, and layer thickness of 80~120μm.

[0028] Furthermore, the GH4169 alloy powder comprises the following elements: C≤0.08%, Cr: 15.0~25.0%, Ni: 50.0~55.0%, Mo: 2~4%, Nb: 4~6%, Ti: 0.8~1.2%, Al: 0.3~0.7%, with the balance being Fe; the CuCrZr alloy powder comprises the following elements: Cu balance, Cr: 0.3~0.8%, Zr: 0.3~0.6%, where all percentages are mass percentages.

[0029] The above-mentioned GH4169 alloy has a density of ≥99%, a tensile strength of 1013~1189MPa, a yield strength of 655~793MPa, a thermal conductivity of 10.8~15.1, and an elongation of 28.7%~32.5%.

[0030] Example 1.

[0031] The alloy powders GH4169 and CuCrZr, with alloy element contents as shown in Table 1, were used in a mass ratio of 90:10. The particle size of both GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 200W, the scanning rate to 600mm / s, the scanning spacing to 0.08mm, and the layer thickness to 80μm.

[0032] After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0033] The nickel-based alloy formed part of Example 1 has a tensile strength of 1093 MPa, a yield strength of 678 MPa, an elongation of 30.4%, a thermal conductivity of 12.1 W / (m*K), and a density of 99.6%.

[0034] Example 2.

[0035] The alloy powders GH4169 and CuCrZr, with alloy element contents as shown in Table 1, were used in a mass ratio of 90:10. The particle size of both GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 300W, the scanning rate to 1050mm / s, the scanning interval to 0.12mm, and the layer thickness to 100μm. After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0036] The nickel-based alloy formed part of Example 2 has a tensile strength of 1101 MPa, a yield strength of 682 MPa, an elongation of 30.5%, a thermal conductivity of 11.9 W / (m*K), and a density of 99.3%.

[0037] Example 3.

[0038] The alloy powders GH4169 and CuCrZr, with alloy element contents as shown in Table 1, were used in a mass ratio of 90:10. The particle size of both GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 400W, the scanning rate to 1500mm / s, the scanning spacing to 0.15mm, and the layer thickness to 120μm. After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0039] The nickel-based alloy formed part of Example 3 has a tensile strength of 1083 MPa, a yield strength of 698 MPa, an elongation of 30.6%, a thermal conductivity of 12.3 W / (m*K), and a density of 99.4%.

[0040] Example 4.

[0041] The alloy powders GH4169 and CuCrZr, with the alloy element contents shown in Table 1, were used in a mass ratio of 85:15. The particle size of both the GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 200W, the scanning rate to 600mm / s, the scanning spacing to 0.08mm, and the layer thickness to 80μm. After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0042] The nickel-based alloy formed part of Example 4 has a tensile strength of 1127 MPa, a yield strength of 713 MPa, an elongation of 32.1%, a thermal conductivity of 13.4 W / (m*K), and a density of 99.6%.

[0043] Example 5.

[0044] The alloy powders GH4169 and CuCrZr, with the alloy element contents shown in Table 1, were used in a mass ratio of 85:15. The particle size of both the GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 300W, the scanning rate to 1050mm / s, the scanning interval to 0.12mm, and the layer thickness to 100μm. After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0045] The nickel-based alloy formed part of Example 5 has a tensile strength of 1189 MPa, a yield strength of 737 MPa, an elongation of 31.7%, a thermal conductivity of 13.3 W / (m*K), and a density of 99.8%.

[0046] Example 6.

[0047] The alloy powders GH4169 and CuCrZr, with the alloy element contents shown in Table 1, were used in a mass ratio of 85:15. The particle size of both the GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 400W, the scanning rate to 1500mm / s, the scanning spacing to 0.15mm, and the layer thickness to 120μm. After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0048] The nickel-based alloy formed part of Example 6 has a tensile strength of 1128 MPa, a yield strength of 721 MPa, an elongation of 31.4%, a thermal conductivity of 13.7 W / (m*K), and a density of 99.7%.

[0049] Example 7.

[0050] The alloy powders GH4169 and CuCrZr, with alloy element contents as shown in Table 1, were used in a mass ratio of 80:20. The particle size of both GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 200W, the scanning rate to 600mm / s, the scanning spacing to 0.08mm, and the layer thickness to 80μm. After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0051] The nickel-based alloy formed part of Example 7 has a tensile strength of 1143 MPa, a yield strength of 755 MPa, an elongation of 32.2%, a thermal conductivity of 13.9 W / (m*K), and a density of 99.7%.

[0052] Example 8.

[0053] The alloy powders GH4169 and CuCrZr, with the alloy element contents shown in Table 1, were used in a mass ratio of 80:20. The particle size of both GH4169 and CuCrZr alloy powders was 54~105μm.

[0054] GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 300W, the scanning rate to 1050mm / s, the scanning interval to 0.12mm, and the layer thickness to 100μm. After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0055] The nickel-based alloy formed part of Example 8 has a tensile strength of 1169 MPa, a yield strength of 777 MPa, an elongation of 32.5%, a thermal conductivity of 14.2 W / (m*K), and a density of 99.5%.

[0056] Example 9.

[0057] The alloy powders GH4169 and CuCrZr, with alloy element contents as shown in Table 1, were used in a mass ratio of 80:20. The particle size of both GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 400W, the scanning rate to 1500mm / s, the scanning spacing to 0.15mm, and the layer thickness to 120μm. After printing, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the formed part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks, namely GH4169 alloy.

[0058] The nickel-based alloy formed part of Example 9 has a tensile strength of 1180 MPa, a yield strength of 793 MPa, an elongation of 31.6%, a thermal conductivity of 15.1 W / (m*K), and a density of 99.4%.

[0059] Comparative Example 1.

[0060] The alloy powder with the alloy element content shown in Table 1 was used, and the particle size of the GH4169 alloy powder used was 54~105μm. GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 200W, the scanning rate to 600mm / s, the scanning spacing to 0.08mm, and the layer thickness to 80μm. After printing is completed, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the molded part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks.

[0061] The nickel-based alloy formed part of Comparative Example 1 has a tensile strength of 1013 MPa, a yield strength of 655 MPa, an elongation of 29.1%, a thermal conductivity of 11.2 W / (m*K), and a density of 99.1%.

[0062] Comparative Example 2.

[0063] The alloy powders GH4169 and CuCrZr, with the alloy element contents shown in Table 1, were used in a mass ratio of 95:5. The particle size of both the GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 200W, the scanning rate to 600mm / s, the scanning spacing to 0.08mm, and the layer thickness to 80μm. After printing is completed, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the molded part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks.

[0064] The nickel-based alloy formed part of Comparative Example 2 has a tensile strength of 1059 MPa, a yield strength of 663 MPa, an elongation of 30.5%, a thermal conductivity of 11.4 W / (m*K), and a density of 99.2%.

[0065] Comparative Example 3.

[0066] The alloy powders GH4169 and CuCrZr, with alloy element contents as shown in Table 1, were used, with a mass ratio of 75:25. The particle size of both GH4169 and CuCrZr alloy powders was 54~105μm. GH4169 alloy powder and CuCrZr alloy powder were mixed. 316L steel balls with a diameter of 2mm were placed in a stainless steel ball mill jar. The mixed powder was then placed in the stainless steel ball mill jar for ball milling. The mixed powder obtained after ball milling is placed in a vacuum drying oven to obtain the dried mixed powder, which is the nickel-based alloy mixed powder material for laser powder bed melting and forming; GH4169 alloy was selected as the printing substrate. The surface was sanded to expose a flat and bright upper surface. After sanding, it was cleaned and dried with ethanol, and then placed in a laser powder bed melting and forming equipment. The laser power for laser powder bed melting was set to 200W, the scanning rate to 600mm / s, the scanning spacing to 0.08mm, and the layer thickness to 80μm. After printing is completed, the substrate is removed from the equipment. After the substrate temperature drops to room temperature, the substrate is separated from the molded part by wire cutting to obtain a nickel-based alloy block without macroscopic cracks.

[0067] The nickel-based alloy formed part of Comparative Example 3 has a tensile strength of 1061 MPa, a yield strength of 669 MPa, an elongation of 28.7%, a thermal conductivity of 15.8 W / (m*K), and a density of 99.2%.

[0068] Table 1. Composition of GH4169 alloy powder (mass fraction).

[0069] Table 2. Composition of CuCrZr alloy powder (mass fraction).

[0070] The above description is merely a preferred embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any variations or substitutions that can be easily conceived by those skilled in the art within the technical scope disclosed in the present invention should 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 laser 3D printing manufacturing method for a high thermal conductivity high-temperature alloy, characterized in that, Includes the following steps: Step 1: Prepare GH4169 alloy powder and CuCrZr alloy powder raw materials; Step 2: GH4169 alloy powder and CuCrZr alloy mixed powder are melted together using a laser powder bed melting method to obtain GH4169 alloy.

2. The laser 3D printing manufacturing method for high thermal conductivity high-temperature alloys according to claim 1, characterized in that, The mass of CuCrZr alloy powder is 10% to 20% of the total mass of the alloy mixed powder.

3. The laser 3D printing manufacturing method for high thermal conductivity high-temperature alloys according to claim 1, characterized in that, The particle size of GH4169 alloy powder is 54~105μm, and the particle size of CuCrZr alloy powder is 54~105μm.

4. The laser 3D printing manufacturing method for high thermal conductivity high-temperature alloys according to claim 1, characterized in that, The process parameters for laser powder bed melting include: laser power of 200~400W, scanning rate of 600~1500mm / s, scanning spacing of 0.08~0.15mm, and layer thickness of 80~120μm.

5. The laser 3D printing manufacturing method for high thermal conductivity high-temperature alloys according to claim 1, characterized in that, GH4169 alloy powder contains the following elements: C≤0.08%, Cr: 15.0~25.0%, Ni: 50.0~55.0%, Mo: 2~4%, Nb: 4~6%, Ti: 0.8~1.2%, Al: 0.3~0.7%, with the balance being Fe; CuCrZr alloy powder contains the following elements: Cu balance, Cr: 0.3~0.8%, Zr: 0.3~0.6%, where all percentages are by mass.

6. A GH4169 alloy prepared by laser 3D printing manufacturing method of a high thermal conductivity high-temperature alloy according to any one of claims 1-5, characterized in that, The GH4169 alloy has a density of ≥99%, a tensile strength of 1013~1189MPa, a yield strength of 655~793MPa, a thermal conductivity of 10.8~15.1, and an elongation of 28.7%~32.5%.

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