Selective laser melting GH3536 nickel-based superalloy scanning method and GH3536 nickel-based superalloy

Abstract

The invention belongs to the technical field of metal material additive manufacturing, and discloses a selective laser melting forming GH3536 nickel-based high-temperature alloy scanning method and a GH3536 nickel-based high-temperature alloy. According to the method, the scanning strategy is optimized, and the scanning strategy of checkerboard-shaped scanning and 67-degree layer-by-layer rotation is adopted, so that the optimal scanning strategy for GH3536 selective laser melting forming is determined. According to the method, the porosity can be reduced, the microscopic structure can be optimized, the tensile property of the selective laser melting GH3536 nickel-based superalloy is improved, and the GH3536 nickel-based superalloy which is high in density and free of cracks is prepared. In addition, the tensile property of the GH3536 nickel-based superalloy is remarkably improved under the condition that the strength of the GH3536 nickel-based superalloy formed through selective laser melting is not reduced.

Description

Technical Field

[0001] The present invention relates to the technical field of metal material additive manufacturing, and in particular to a scanning method for selective laser melting forming GH3536 nickel-based high-temperature alloy and GH3536 nickel-based high-temperature alloy. Background Art

[0002] GH3536 nickel-based superalloy, also known as Hastelloy X alloy, is a typical solid solution strengthened nickel-based superalloy. Mainly based on nickel, with chromium and molybdenum as the main solid solution strengthening elements, it has good oxidation resistance and corrosion resistance, and shows good stability and load-bearing capacity in harsh environments. It is widely used in high-temperature components such as aerospace engine guide vanes, vortex exhaust pipes, combustion chamber honeycomb structures, and nuclear reactor combustion fuel jackets. However, the traditional method of manufacturing complex and high-precision GH3536 nickel-based superalloys requires longer production cycles and costs, and is prone to defects such as pores and cracks, which seriously limits the development of high-temperature component manufacturing.

[0003] Among additive manufacturing technologies, the most widely used is Selective Laser Melting. This technology stands out for its high precision and ability to produce complex parts in the process of rapid metal prototyping. SLM is an additive manufacturing process that uses laser to melt metal powder layer by layer to prepare three-dimensional structures. Compared with traditional forming processes, SLM has significant advantages in processing efficiency, material savings, and manufacturing of functional parts with complex geometries. It also has finer microstructures and extremely high dimensional accuracy. However, the GH3536 nickel-based high-temperature alloy has a tendency to crack and has pores during the selective laser melting process. Designing a suitable laser scanning strategy can not only avoid the formation of alloy defects, but also improve the plasticity of the material without reducing the strength of the material.

[0004] GH3536 nickel-based superalloy is a solid solution strengthening superalloy material. In addition to the solid solution strengthening effect, the grain boundary strengthening of GH3536 nickel-based superalloy is also one of the strengthening effects. Due to the large number of grain boundaries, the material is prone to cracking. There is a greater tendency for defects to appear during the selective laser melting process. Optimizing the scanning strategy is an effective measure to suppress defects in the alloy. However, the existing selective laser melting process for preparing GH3536 nickel-based superalloy usually adopts a scanning strategy with an interlayer rotation angle of 0° / 90° / 67°. Patents on the chessboard scanning strategy for selective laser melting of GH3536 alloy have not yet been reported. Summary of the invention

[0005] The object of the present invention is to provide a scanning method for selective laser melting forming GH3536 nickel-based high temperature alloy and GH3536 nickel-based high temperature alloy.

[0006] The technical solution of the present invention is as follows: A scanning method for selective laser melting of GH3536 nickel-based high-temperature alloy, the steps are as follows:

[0007] Step S1, creating a three-dimensional solid model of GH3536 nickel-based high-temperature alloy for selective laser melting forming;

[0008] Step S2, designing the laser scanning path, determining the basic process parameters, slicing the 3D solid model, and dividing it into multiple scanning layers from bottom to top, namely the first scanning layer, the second scanning layer, the third scanning layer, ... until the Nth scanning layer, and importing the sliced ​​file into the selective laser melting forming equipment system; each scanning layer is evenly divided into a number of areas of the same shape, and adjacent areas of the first scanning layer are scanned in a manner of intersecting at a specific angle; the same area of ​​adjacent scanning layers is scanned in a manner of intersecting at a specific angle;

[0009] Step S3, fixing the substrate in a forming chamber of the selective laser melting equipment, and cleaning and leveling the surface of the substrate;

[0010] Step S4, closing the hatch, selecting the imported GH3536 nickel-based high-temperature alloy process parameters in the equipment control system, heating the substrate and starting the vacuum system;

[0011] Step S5, when the substrate temperature reaches 80°C and the oxygen content reaches 150ppm, start the device and print according to the laser scanning path of step S2;

[0012] Step S6, after printing the current scanning layer, the substrate is lowered by one layer, the powder tank is raised by one layer, the scraper spreads the powder, and prepares to print the next layer, and then enters step S7;

[0013] Step S7, repeat step S6 until all scan layers are printed.

[0014] The adjacent areas of the first scanning layer intersect at 90° or 67° and are gradually accumulated from left to right and from top to bottom.

[0015] The same area of ​​adjacent scan layers intersects at 67°.

[0016] In step S2, the laser power is set to 200-220W.

[0017] In step S2, the laser scanning speed is set to 900-1100 mm / s.

[0018] In step S2, the thickness of the scanning layer is set to 30 μm.

[0019] In step S2, the laser scanning interval is set to 100 μm.

[0020] The GH3536 nickel-based high-temperature alloy prepared by the selective laser melting forming GH3536 nickel-based high-temperature alloy scanning method has no holes and cracks inside, and has a room temperature elongation greater than 40% and a high-temperature elongation greater than 55%.

[0021] Beneficial effects of the present invention: In the process of selective laser melting forming GH3536 nickel-based high-temperature alloy, the key is to find printing process parameters and laser scanning strategies suitable for the alloy to reduce defects inside the alloy and optimize its microstructure, thereby improving its plasticity without sacrificing material strength. The scanning strategy of the technical solution of the present invention has an elongation of at least 10% higher than other scanning strategies. Under the same process parameters, the GH3536 nickel-based high-temperature alloy prepared by the present invention is free of defects such as holes and cracks by comparing the scanning strategy method of the present invention with the existing scanning strategy, thereby improving tensile plasticity. The present invention provides a chessboard-shaped scanning strategy that rotates 67° layer by layer. During the printing process, the laser moves along the lines of the chessboard to form layers of cladding. This scanning method can reduce the concentration of thermal stress because the heat input in each small area is relatively uniform, avoiding stress concentration and part deformation caused by local overheating. Without reducing the strength of the GH3536 nickel-based high-temperature alloy formed by selective laser melting, its tensile properties are significantly improved, further improving the safety of commercial GH3536 nickel-based high-temperature alloy formed parts. BRIEF DESCRIPTION OF THE DRAWINGS

[0022] Figure 1 A process flow chart showing the scanning strategy method for selective laser melting of GH3536 nickel-based high-temperature alloy of the present invention.

[0023] Figure 2 Schematic diagram of Example 1 of the present invention; (a) is the scanning path, (b) and (c) are metallographic images of the molten pool morphology, and (d) and (e) are IPF images of cross-sectional EBSD data.

[0024] Figure 3 Schematic diagram of Example 2 of the present invention; (a) is the scanning path, (b) and (c) are metallographic images of the molten pool morphology, and (d) and (e) are IPF images of cross-sectional EBSD data.

[0025] Figure 4 A schematic diagram showing comparative example 1 of the present invention; (a) is a scanning path, (b) and (c) are metallographic images of the molten pool morphology, and (d) and (e) are IPF images of cross-sectional EBSD data.

[0026] Figure 5Schematic diagram of Comparative Example 2 of the present invention; (a) is the scanning path, (b) and (c) are metallographic images of the molten pool morphology, and (d) and (e) are IPF images of cross-sectional EBSD data.

[0027] Figure 6 Schematic diagram of comparative example 3 of the present invention; (a) is the scanning path, (b) and (c) are metallographic images of the molten pool morphology, and (d) and (e) are IPF images of cross-sectional EBSD data.

[0028] Figure 7 The engineering stress-strain curves of room temperature stretching of GH3536 nickel-based high-temperature alloy formed by selective laser melting in the five scanning strategies of the present invention are shown.

[0029] Figure 8 The engineering stress-strain curves of high-temperature stretching of GH3536 nickel-based high-temperature alloy formed by selective laser melting in the five scanning strategies of the present invention are shown.

[0030] Fig. 9 Indicates the three-dimensional model of the sample to be established. DETAILED DESCRIPTION

[0031] A scanning method for selective laser melting of GH3536 nickel-based high-temperature alloy, the steps are as follows:

[0032] Step S1, creating a three-dimensional solid model of GH3536 nickel-based high-temperature alloy for selective laser melting forming;

[0033] Step S2, designing the laser scanning path, determining the basic process parameters, slicing the 3D solid model, and dividing it into multiple scanning layers from bottom to top, namely the first scanning layer, the second scanning layer, the third scanning layer, ... until the Nth scanning layer, and importing the sliced ​​file into the selective laser melting forming equipment system; each scanning layer is evenly divided into a number of areas of the same shape, and adjacent areas of the first scanning layer are scanned in a manner of intersecting at a specific angle; the same area of ​​adjacent scanning layers is scanned in a manner of intersecting at a specific angle;

[0034] Step S3, fixing the substrate in a forming chamber of the selective laser melting equipment, and cleaning and leveling the surface of the substrate;

[0035] Step S4, closing the hatch, selecting the imported GH3536 nickel-based high-temperature alloy process parameters in the equipment control system, heating the substrate and starting the vacuum system;

[0036] Step S5, when the substrate temperature reaches 80°C and the oxygen content reaches 150ppm, start the device and print according to the laser scanning path of step S2;

[0037] Step S6, after printing the current scanning layer, the substrate is lowered by one layer, the powder tank is raised by one layer, the scraper spreads the powder, and prepares to print the next layer, and then enters step S7;

[0038] Step S7, repeat step S6 until all scanning layers are printed.

[0039] Furthermore, adjacent areas of the first scanning layer intersect at 90° or 67° and are gradually accumulated from left to right and from top to bottom.

[0040] Furthermore, in step S2, for the formed rectangular block sample, each scanning layer is divided into a plurality of square areas, and these areas are scanned in the form of intersecting at a certain angle in the subsequent scanning layer. For example, when the size of the printed sample is 20mm×50mm×20mm, the entire area of ​​the 20mm×50mm scanning layer is divided into a plurality of 5mm×5mm small areas, and the scanning tracks of each small area of ​​the first scanning layer are 90° or 67° to the adjacent areas, and the second scanning layer is rotated 67° with the previous scanning layer, and rotates continuously in sequence, and repeats every 360 layers.

[0041] Furthermore, the same regions of adjacent scanning layers intersect at 67°.

[0042] Furthermore, in step S2, the laser power is set to 200-220W.

[0043] Furthermore, in step S2, the laser scanning speed is set to 900-1100 mm / s.

[0044] Furthermore, in step S2, the thickness of the scanning layer is set to 30 μm.

[0045] Furthermore, in step S2, the laser scanning interval is set to 100 μm.

[0046] Furthermore, in step S5, the substrate preheating temperature is 100° C., and the oxygen content of the forming environment is 150 ppm.

[0047] Furthermore, the method further includes step S8, wherein after the forming is completed, the substrate temperature is waited to drop to room temperature, the cabin door is opened, the powder is cleaned, the substrate is taken out of the forming cabin, and the sample is removed by wire cutting.

[0048] A GH3536 nickel-based high-temperature alloy prepared by the selective laser melting forming GH3536 nickel-based high-temperature alloy scanning method, wherein the obtained GH3536 nickel-based high-temperature alloy has no holes or cracks inside.

[0049] Furthermore, the size of the block sample used for microstructure observation of the GH3536 nickel-based high-temperature alloy is set to 12 mm×12 mm×12 mm; the size of the block sample used for tensile property testing is set to 20 mm×50 mm×20 mm.

[0050] When the laser power is between 200 and 220 W, the laser scanning speed is within the range of 900 to 1100 mm / s, the scanning layer thickness is 30 μm, and the laser scanning spacing is 100 μm, the GH3536 nickel-based superalloy is prepared by five different scanning strategies. By adjusting the laser energy input density, the powder undermelting and overmelting phenomena are avoided, and the formation of holes and keyholes is reduced; at the same time, by reducing the residual stress generated during the forming process and optimizing the microstructure, the sensitivity of cracking of the GH3536 nickel-based superalloy formed by selective laser melting is reduced. A process window for preparing defect-free GH3536 nickel-based superalloy under five different scanning strategies (two embodiments and three comparative examples) is provided, which provides a reasonable process window for the selective laser melting of GH3536 nickel-based superalloy with different scanning strategies. The microstructure of the GH3536 nickel-based superalloy under five different scanning strategies is compared, and its tensile properties under two temperature conditions are analyzed, and a new chessboard scanning strategy is proposed. By adjusting the scanning path, the residual stress in the forming process can be reduced and the microstructure can be optimized, thereby improving tensile plasticity. The present invention provides a chessboard scanning strategy with a layer-by-layer rotation of 67°, which significantly improves the tensile properties of the GH3536 nickel-based high-temperature alloy formed by selective laser melting without reducing its strength, and further improves the safety of commercial GH3536 nickel-based high-temperature alloy formed parts.

[0051] The following examples use gas atomized GH3536 nickel-based high-temperature alloy powder provided by the Institute of Metal Research, Chinese Academy of Sciences. The powder particle size distribution range is 19 to 44 μm. The EP-M150 selective laser melting additive manufacturing equipment with a laser beam with a spot diameter of 60 μm is used, the maximum power is 500 W, the maximum scanning speed is 10 m / s, and inert argon is used as the protective gas.

[0052] like Figure 1 As shown, this embodiment provides a scanning strategy method for preparing GH3536 nickel-based high-temperature alloy by selective laser melting. The present invention is further described in detail below in conjunction with the accompanying drawings and specific embodiments:

[0053] Example 1

[0054] like Figure 2 As shown in (a), this embodiment adopts a chessboard-shaped scanning strategy of rotating 67° layer by layer. The adjacent areas of the first scanning layer are scanned in a 90° intersection manner; the same area of ​​the adjacent scanning layer is scanned in a 67° intersection manner; the steps are as follows:

[0055] Step S1, using VoxelDance Additive software to build a solid model of GH3536 nickel-based high-temperature alloy. The block size for microstructure observation is 12 mm×12 mm×12 mm, and the block size for tensile property testing is 20 mm×50 mm×20 mm.

[0056] Step S2, the three-dimensional solid model is layered through EPHatch software. At the same time, the laser scanning strategy and process parameters are planned, and the slice file is imported into the selective laser melting forming equipment system. Among them, the specific contents of the laser scanning strategy include: if the block sample is printed, the entire scanning area is divided into multiple small areas of size N mm×N mm in the same scanning layer, the scanning path of each small area of ​​the first scanning layer is 90° between adjacent areas, and the second scanning layer is 67° rotated with the previous scanning layer, and rotated continuously, and repeated every 360 layers. The specific contents of the printing process parameters include: laser power of 200~220W, laser scanning speed of 900~1100mm / s, scanning layer thickness of 30μm, laser scanning spacing of 100μm, and then proceed to step S3.

[0057] Step S3, fix the substrate in the forming chamber of the selective laser melting equipment, clean the surface of the substrate and level it, and then proceed to step S4.

[0058] Step S4, close the hatch. In the selective laser melting forming control system, select the imported process parameters of GH3536 nickel-based high-temperature alloy, heat the substrate, turn on the vacuum system, and go to step S5.

[0059] Step S5, when the substrate temperature (80°C) and oxygen content (150ppm) reach the standard, start the selective laser melting forming equipment, print according to the laser scanning strategy of the first scanning layer, and then go to step S6.

[0060] Step S6, after completing the current scanning layer, the substrate is lowered by one layer, the powder tank is raised by one layer, the scraper spreads the powder, and prepares for printing the next scanning layer, and then goes to step S7.

[0061] Step S7, repeat step S6 until all printing layers are completed, and then go to step S8.

[0062] Step S8, wait for the substrate temperature to drop to room temperature, open the cabin door, clean the powder, take out the sample from the forming cabin, remove the sample by wire cutting, and go to step S9.

[0063] Step S9, using an optical microscope and electron backscatter diffraction to observe the structure of the sample cross section / vertical section, the metallographic image and IPF image are respectively Figure 2 (b), (c) and Figure 2As shown in (d) and (e), there are no holes or cracks inside the formed sample, and the process proceeds to step S10.

[0064] Step S10, performing room temperature and high temperature (815°C) tensile property tests on the deposited sample. Figure 7 , Figure 8 As shown, after room temperature tensile performance test, the yield strength and tensile strength are 652MPa and 767MPa respectively, and the elongation is 39.5%. After 815℃ high temperature tensile performance test, the yield strength and tensile strength are 236MPa and 348MPa respectively, and the elongation is 58.7%.

[0065] Example 2

[0066] like Figure 3 As shown in (a), this embodiment adopts a chessboard-shaped scanning strategy of rotating 67° layer by layer. The adjacent areas of the first scanning layer are scanned in a 67° intersection manner; the same area of ​​the adjacent scanning layers is scanned in a 67° intersection manner; the steps are as follows:

[0067] Step S1, using VoxelDance Additive software to build a solid model of GH3536 nickel-based high-temperature alloy. The block size for microstructure observation is 12 mm×12 mm×12 mm, and the block size for tensile property testing is 20 mm×50 mm×20 mm.

[0068] Step S2, the three-dimensional solid model is layered through EPHatch software. At the same time, the laser scanning strategy and process parameters are planned, and the slice file is imported into the selective laser melting forming equipment system. Among them, the specific contents of the laser scanning strategy include: if the block sample is printed, the entire scanning area is divided into multiple small areas of size N mm×N mm in the same scanning layer, the scanning path of each small area of ​​the first scanning layer is 90° between adjacent areas, and the second scanning layer is 67° rotated with the previous scanning layer, and rotated continuously, and repeated every 360 layers. The specific contents of the printing process parameters include: laser power of 200~220W, laser scanning speed of 900~1100mm / s, scanning layer thickness of 30μm, laser scanning spacing of 100μm, and then proceed to step S3.

[0069] Step S3, fix the substrate in the forming chamber of the selective laser melting equipment, clean the surface of the substrate and level it, and then proceed to step S4.

[0070] Step S4, close the hatch. In the selective laser melting forming control system, select the imported process parameters of GH3536 nickel-based high-temperature alloy, heat the substrate, turn on the vacuum system, and go to step S5.

[0071] Step S5, when the substrate temperature (80°C) and oxygen content (150ppm) reach the standard, start the selective laser melting forming equipment, print according to the laser scanning strategy of the first scanning layer, and then go to step S6.

[0072] Step S6, after completing the current scanning layer, the substrate is lowered by one layer, the powder tank is raised by one layer, the scraper spreads the powder, and prepares for printing the next scanning layer, and then goes to step S7.

[0073] Step S7, repeat step S6 until all printing layers are completed, and then go to step S8.

[0074] Step S8, wait for the substrate temperature to drop to room temperature, open the cabin door, clean the powder, take out the sample from the forming cabin, remove the sample by wire cutting, and go to step S9.

[0075] Step S9, using an optical microscope and electron backscatter diffraction to observe the structure of the sample cross section / vertical section, the metallographic image and IPF image are respectively Figure 3 (b), (c) and Figure 3 As shown in (d) and (e), there are no holes or cracks inside the formed sample, and the process proceeds to step S10.

[0076] Step S10, performing room temperature and high temperature (815°C) tensile property tests on the deposited sample. Figure 7 , Figure 8 As shown, after the room temperature tensile performance test, the yield strength and tensile strength are 581MPa and 677MPa respectively, and the elongation is 40.0%; after the 815℃ high temperature tensile performance test, the yield strength and tensile strength are 236MPa and 350MPa respectively, and the elongation is 53.6%.

[0077] Comparative Example 1

[0078] like Figure 4 As shown in (a), this comparative example adopts a scanning strategy with a rotation angle of 0° to selectively laser melt the GH3536 nickel-based high-temperature alloy. The sample preparation steps are basically the same as those in the embodiment, except that:

[0079] In step S2, the specific contents of the laser scanning strategy are as follows: the laser scanning path of each scanning layer is a horizontal reciprocating scanning, and the paths of odd and even layers are exactly the same. There is no rotation between layers, and the scanning is continuous. The specific contents of the printing process parameters include: laser power is 210W, laser scanning speed is 1000mm / s, scanning layer thickness is 30μm, and laser scanning spacing is 100μm.

[0080] The sample cross-section and longitudinal section were observed using an optical microscope and electron backscatter diffraction. The metallographic images and IPF images are Figure 4 (b), (c) and Figure 4 As shown in (d) and (e), there are a small number of holes and cracks inside the formed specimens, and no other forming defects are observed.

[0081] The tensile properties of the deposited samples were tested at room temperature and high temperature (815°C). Figure 7 , Figure 8 As shown, after room temperature tensile performance test, the yield strength and tensile strength are 524MPa and 578MPa respectively, and the elongation is 5%. After 815℃ high temperature tensile performance test, the yield strength and tensile strength are 208MPa and 325MPa respectively, and the elongation is 40.1%.

[0082] Comparative Example 2

[0083] like Figure 5 As shown in (a), this comparative example adopts a scanning strategy with a rotation angle of 90° to selectively laser melt the GH3536 nickel-based high-temperature alloy. The sample preparation steps are basically the same as those in the embodiment, except that:

[0084] In step S2, the specific contents of the laser scanning strategy are as follows: the laser path of the first scanning layer scans back and forth on the horizontal opposite sides; the laser path of the second scanning layer scans back and forth with the first layer in a clockwise rotation direction of 90°; the laser path of the third scanning layer scans back and forth with the second layer in a clockwise rotation direction; the laser path of the fourth scanning layer scans back and forth with the third layer in a clockwise rotation direction of 90°. The layers rotate 90° relative to each other, rotate continuously, and repeat every 4 layers. The specific contents of the printing process parameters include: laser power of 210W, laser scanning speed of 1000mm / s, scanning layer thickness of 30μm, and laser scanning spacing of 100μm.

[0085] The sample cross-section and longitudinal section were observed using an optical microscope and electron backscatter diffraction. The metallographic images and IPF images are Figure 5 (b), (c) and Figure 5 As shown in (d) and (e), there are a small number of holes inside the formed specimen, and no cracks or unfused defects are observed.

[0086] The tensile properties of the deposited samples were tested at room temperature and high temperature (815°C). Figure 7 , Figure 8 As shown, after room temperature tensile performance test, the yield strength and tensile strength are 587MPa and 669MPa respectively, and the elongation is 27.3%. After 815℃ high temperature tensile performance test, the yield strength and tensile strength are 220MPa and 322MPa respectively, and the elongation is 41.0%.

[0087] Comparative Example 3

[0088] like Figure 6As shown in (a), this comparative example adopts a scanning strategy with a rotation angle of 67° to selectively laser melt the GH3536 nickel-based high-temperature alloy. The sample preparation steps are basically the same as those in the embodiment, except that:

[0089] In step S2, the specific contents of the laser scanning strategy are as follows: the laser path of the first scanning layer is horizontally reciprocating scanning, and the laser path of the second layer is 67° with the first layer and reciprocating scanning. The laser scanning direction between layers is relatively rotated 67°, and the rotation is continuous, and repeated every 360 layers. The specific contents of the printing process parameters include: laser power is 210W, laser scanning speed is 1000mm / s, scanning layer thickness is 30μm, and laser scanning spacing is 100μm.

[0090] The sample cross-section and longitudinal section were observed using an optical microscope and electron backscatter diffraction. The metallographic images and IPF images are Figure 6 (b), (c) and Figure 6 As shown in (d) and (e), there are a small number of holes inside the formed specimen, and no cracks or unfused defects are observed.

[0091] The tensile properties of the deposited samples were tested at room temperature and high temperature (815°C). Figure 7 , Figure 8 As shown, after the room temperature tensile performance test, the yield strength and tensile strength are 582MPa and 674MPa respectively, and the elongation is 34.5%. After the 815℃ high temperature tensile performance test, the yield strength and tensile strength are 217MPa and 346MPa respectively, and the elongation is 49.8%.

[0092] The results of the embodiments and comparative examples show that the present invention uses a selective laser melting forming device and adopts a chessboard-shaped + 67° rotation scanning strategy to form the GH3536 nickel-based high-temperature alloy. The formed alloy has fewer internal defects, a higher tensile mechanical property elongation, and a small decrease in strength. In actual production engineering applications, the use range of the GH3536 nickel-based high-temperature alloy can be increased.

Claims

1. A scanning method for selective laser melting of GH3536 nickel-based high-temperature alloy, characterized in that: Here are the steps: Step S1, creating a three-dimensional solid model of GH3536 nickel-based high-temperature alloy for selective laser melting forming; Step S2, designing the laser scanning path, determining the basic process parameters, slicing the 3D solid model, and dividing it into multiple scanning layers from bottom to top, namely the first scanning layer, the second scanning layer, the third scanning layer, ... until the Nth scanning layer, and importing the sliced ​​file into the selective laser melting forming equipment system; each scanning layer is evenly divided into a number of areas of the same shape, and adjacent areas of the first scanning layer are scanned in a manner of intersecting at a specific angle; the same area of ​​adjacent scanning layers is scanned in a manner of intersecting at a specific angle; Step S3, fixing the substrate in a forming chamber of the selective laser melting equipment, and cleaning and leveling the surface of the substrate; Step S4, closing the hatch, selecting the imported GH3536 nickel-based high-temperature alloy process parameters in the equipment control system, heating the substrate and starting the vacuum system; Step S5, when the substrate temperature reaches 80°C and the oxygen content reaches 150ppm, start the device and print according to the laser scanning path of step S2; Step S6, after printing the current scanning layer, the substrate is lowered by one layer, the powder tank is raised by one layer, the scraper spreads the powder, and prepares to print the next layer, and then enters step S7; Step S7, repeat step S6 until all scan layers are printed.

2. The scanning method for selective laser melting of GH3536 nickel-based high-temperature alloy according to claim 1 is characterized in that: The adjacent areas of the first scanning layer intersect at 90° or 67° and are gradually accumulated from left to right and from top to bottom.

3. The scanning method for selective laser melting of GH3536 nickel-based high-temperature alloy according to claim 1 is characterized in that: The same area of ​​adjacent scan layers intersects at 67°.

4. The scanning method for preparing GH3536 nickel-based high-temperature alloy by selective laser melting according to any one of claims 1 to 3, wherein: In step S2, the laser power is set to 200-220W.

5. The scanning method for preparing GH3536 nickel-based high-temperature alloy by selective laser melting according to any one of claims 1 to 3, wherein: In step S2, the laser scanning speed is set to 900-1100 mm / s.

6. The scanning method for preparing GH3536 nickel-based high-temperature alloy by selective laser melting according to any one of claims 1 to 3, wherein: In step S2, the thickness of the scanning layer is set to 30 μm.

7. The scanning method for preparing GH3536 nickel-based high-temperature alloy by selective laser melting according to any one of claims 1 to 3, wherein: In step S2, the laser scanning interval is set to 100 μm.

8. A GH3536 nickel-based high-temperature alloy prepared by the scanning method for selective laser melting of GH3536 nickel-based high-temperature alloy according to any one of claims 1 to 8, characterized in that: There are no holes or cracks inside, the elongation at room temperature is greater than 40%, and the elongation at high temperature is greater than 55%.

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