A method of densification treatment of a metal additively manufactured component

Abstract

The application discloses a kind of metal additive manufacturing component densification processing method, belong to metal additive manufacturing technical field.The metal additive manufacturing component densification processing method of the application includes the following steps: metal additive manufacturing component is prepared using additive manufacturing;The metal additive manufacturing component is treated by low-temperature low-pressure hot isostatic pressing, and dense alloy component is obtained.The method of the application (low-temperature low-pressure HIP processing to metal additive manufacturing component with defect) can realize the closure of metal additive manufacturing component porosity, unfused, microcrack and other defects, while can avoid the problem of the organization of existing high-temperature high-pressure HIP processing process is thick, affects the mechanical and fatigue performance of component;And the method of the application can simplify process flow, shorten post-processing time.

Description

Technical Field

[0001] This invention relates to the field of metal additive manufacturing technology, and in particular to a method for densifying metal additive manufacturing components. Background Technology

[0002] Metal additive manufacturing is one of the important manufacturing methods for key metal components in aerospace, medical, consumer electronics, automotive, and mold industries. Because its forming process is independent of the complexity of the component and does not require specialized tools and fixtures, it is suitable for manufacturing components with relatively complex geometries. However, during the additive manufacturing process, the molten metal in the pool cools very rapidly, resulting in a non-equilibrium solidification process. The solidified structure is in a metastable state, and a large amount of residual stress accumulates inside the component. Furthermore, defects such as porosity, lack of fusion, process holes, and even microcracks are unavoidable in the microstructure. These solidification characteristics and defects inevitably reduce the mechanical and fatigue properties of the component.

[0003] In the field of metal additive manufacturing, commonly used methods for eliminating internal defects include hot isostatic pressing (HIP), solution aging heat treatment, and laser remelting. Solution aging heat treatment can only optimize the distribution of component segregation and precipitates in metal additive manufacturing and alleviate localized micropores, but it cannot eliminate primary internal defects such as porosity, lack of fusion, and macroscopic looseness. Furthermore, it easily induces grain coarsening, stress redistribution leading to microcracks, and precipitate segregation exacerbating defect sensitivity, potentially causing part deformation and fluctuations in mechanical properties. Laser remelting is only effective for shallow defects; it cannot eliminate deep-seated internal pores, and the remelted zone is prone to thermal stress and microcracks, resulting in low efficiency and unsuitability for the overall densification of large parts. While HIP can eliminate internal defects, prolonged high-temperature and high-pressure environments can lead to the growth of the part's microstructure, increased internal accumulated stress levels, and even deformation and cracking, rendering the part unusable and creating difficulties for subsequent heat treatment and machining. Therefore, how to eliminate internal defects in metal additive manufacturing while ensuring the yield of finished parts has become a pressing technical challenge for those skilled in the art. Summary of the Invention

[0004] The purpose of this invention is to provide a method for densification of metal additive manufacturing components to solve the problems existing in the prior art.

[0005] To achieve the above objectives, the present invention provides the following solution: a method for densification treatment of metal additive manufacturing components, comprising the following steps: Metal additive manufacturing components are prepared using additive manufacturing techniques. The metal additive manufacturing component is subjected to low-temperature, low-pressure hot isostatic pressing to obtain a densified alloy component.

[0006] Preferably, the temperature of the low-temperature low-pressure hot isostatic pressing (HIP) treatment is 700-750°C, the pressure is 60-120 MPa, and the heat and pressure holding time is 3-6 hours.

[0007] Preferably, the heating rate of the low-temperature, low-pressure hot isostatic pressing treatment is 5–6 °C / min.

[0008] Preferably, after the low-temperature, low-pressure hot isostatic pressing treatment, the process further includes a step of cooling the furnace to room temperature.

[0009] Low-temperature, low-pressure hot isostatic pressing can eliminate internal defects in components, thereby reducing the possibility of stress concentration and plastic deformation during service. It can also improve the strengthening phase and microstructure, thus significantly extending the fatigue life of the alloy.

[0010] The healing of voids during HIP (High-Intensity Interval) processing is caused by creep in the material surrounding the voids in the alloy. Temperature and pressure jointly drive solute atom diffusion, and their interaction influences the healing rate of the creep voids. Selecting a relatively low temperature, just above the limit within the creep temperature range results in slower solute atom diffusion and a longer diffusion healing period, which can promote defect closure.

[0011] Preferably, the metal additive manufacturing component comprises a Ti6Al4V alloy component.

[0012] Preferably, the method for preparing the Ti6Al4V alloy component includes the following steps: Ti6Al4V alloy components were obtained by additive manufacturing using Ti6Al4V alloy powder as raw material.

[0013] More preferably, the method for preparing the Ti6Al4V alloy component includes the following steps: Using Ti6Al4V alloy powder as raw material, additive manufacturing of powder materials is achieved through powder material supply methods such as powder spreading and powder feeding, and high-energy beam current is used as heat source to obtain Ti6Al4V alloy components.

[0014] Preferably, the Ti6Al4V alloy powder is prepared by gas atomization or rotating electrode method, and has a spherical morphology with a normal particle size distribution ranging from 15 to 53 μm.

[0015] Preferably, the heat source used in the additive manufacturing includes a high-energy beam.

[0016] Preferably, the high-energy beam is selected from any one of laser, electric arc, electron beam and plasma arc.

[0017] Formation of defect characteristics: Under the action of heat source, alloy powder particles melt to form a molten pool. As the heat source moves away from the location of the molten pool, the molten pool metal solidifies. In this series of processes, due to the residual pores in the powder left in the solidified metal, the gas left in the liquid metal due to the evaporation of the material and cannot escape, the insufficient fluidity of the liquid metal to fill the pores between the solidified metals, and the micro-scale hot cracks and cold cracks formed due to the characteristics of the material itself or the characteristics of the manufacturing process.

[0018] More preferably, during the additive manufacturing process, defects such as pores, process holes, lack of fusion, or even microcracks are confirmed to exist internally through direct or indirect online monitoring, destructive testing of parts in the furnace, and non-destructive scanning technologies (non-destructive testing methods) such as industrial CT.

[0019] More preferably, the additive manufacturing further includes removing the metal additive manufacturing component from the forming chamber of the additive manufacturing equipment and performing powder removal treatment, and treating the floating powder on the inner and outer surfaces by methods such as high-pressure gas, sandblasting, chemical etching or internal grinding flow as needed.

[0020] Powder removal treatment can prevent the powder adhering to the surface of the part from sintering with the surface of the part under the action of temperature and pressure, thus avoiding the deterioration of its surface quality.

[0021] Preferably, the additive manufacturing method is selected from any one of laser powder bed melting (LPBF), laser directed energy deposition (LDED), electron beam additive manufacturing, or arc additive manufacturing.

[0022] LPBF technology is generally used to manufacture large-sized, complex-shaped components for aerospace, transportation, medical and other fields, where these applications have high requirements for mechanical and fatigue performance.

[0023] Preferably, the laser power for melting the laser powder bed is 230-290W, the scanning speed is 1150mm / s, and the scanning interval is 0.12mm.

[0024] When the laser power of laser powder bed melting (LPBF) is 290W, the scanning speed is 1150mm / s, and the scanning spacing is 0.12mm, the density of the metal additive manufacturing component can reach 99.95%. Under this optimal process window, the component exhibits excellent mechanical and fatigue properties. When the power is too high, the scanning speed is increased, or the scanning spacing is too large, defects such as circular keyhole-induced pores, insufficient interlayer bonding, and incomplete fusion occur, respectively. Various defects can also be caused during the component manufacturing process due to local temperature issues or powder bed quality problems.

[0025] More preferably, the laser powder bed melting also includes a laser scanning process achieved through laser motion, machine tool motion, or laser and machine tool motion together, and the specific motion path planning is specified according to the shape of the component and optimized process parameters.

[0026] When the pressure of the low-temperature low-pressure hot isostatic pressing (HIP) treatment is set to 120 MPa, the holding time is 3 h, and the temperature is 550℃, the yield strength of the Ti6Al4V alloy component is relatively high. The externally applied pressure is insufficient to drive the material to undergo sufficiently large elastoplastic strain, so it hardly affects the stress.

[0027] When the pressure of low-temperature low-pressure hot isostatic pressing (HIP) was set to 120 MPa, the holding time was 3 h, and the temperature was 700 °C, the plastic strain of the Ti6Al4V alloy component reached its peak value, and the stress also reached its maximum value. This indicates that the material has a significant plastic deformation capacity at this temperature, and the dislocation slip and grain boundary migration mechanisms effectively promote the closure of internal defects.

[0028] When the low-temperature, low-pressure hot isostatic pressing (HIP) treatment is set at a pressure of 120 MPa, a holding time of 3 hours, and a temperature of 750 °C, the stress reaches its minimum and the strain reaches its maximum, indicating that under these conditions, the defects have achieved full densification. Further heating after densification will trigger changes in other microstructures due to the activity of atoms or molecules within the material.

[0029] The present invention discloses the following technical effects: The method of the present invention (HIP treatment of defective metal additive manufacturing components under low temperature and low pressure conditions) can close defects such as porosity, lack of fusion, and microcracks in metal additive manufacturing components. At the same time, it can avoid the problem of coarse microstructure caused by existing high temperature and high pressure HIP treatment processes, which affects the mechanical and fatigue properties of the components. Furthermore, the method of the present invention can simplify the process flow and shorten the post-processing time.

[0030] This invention provides a densification method for metal additive manufacturing components with internal defects, which improves the mechanical and fatigue properties of the metal additive manufacturing components and provides an important basis for expanding the application range of metal additive manufacturing components. Attached Figure Description

[0031] To more clearly illustrate the technical solutions in the embodiments of the present invention or the prior art, the drawings used in the embodiments will be briefly introduced below. Obviously, the drawings described below are only some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0032] Figure 1Metallographic images of Ti6Al4V alloy components prepared in Example 1, wherein (1), (2), (3), (4), (5), (6), (7), (8), (9), (10), (11), and (12) correspond to 12 types of Ti6Al4V alloy components; Figure 2 The defect morphologies of the Ti6Al4V alloy component prepared in Example 1 are shown, where (a) is a porosity defect, (b) is a keyhole defect, and (c) is a lack of fusion. Figure 3 The porosity and average pore diameter of the Ti6Al4V alloy component prepared in Example 1 are shown, where (a) is the porosity and (b) is the average pore diameter. Figure 4 Metallographic images of the Ti6Al4V alloy components (numbered (1), (2), (3), (4), (5), (6), (7), (8), (9), (10), (11), (12)) prepared in Example 1 after hot isostatic pressing (HIP treatment); Figure 5 The stress / strain relationship diagram is shown for the densified Ti6Al4V alloy component in Example 3; Figure 6 The stress / strain relationship diagram is shown for the densified Ti6Al4V alloy component in Example 4. Detailed Implementation

[0033] Various exemplary embodiments of the present invention will now be described in detail. This detailed description should not be considered as a limitation of the present invention, but rather as a more detailed description of certain aspects, features, and embodiments of the present invention.

[0034] It should be understood that the terminology used in this invention is merely for describing particular embodiments and is not intended to limit the invention. Furthermore, with respect to numerical ranges in this invention, it should be understood that each intermediate value between the upper and lower limits of the range is also specifically disclosed. Every smaller range between any stated value or intermediate value within a stated range, and any other stated value or intermediate value within said range, is also included in this invention. The upper and lower limits of these smaller ranges may be independently included or excluded from the range.

[0035] Unless otherwise stated, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art. While only preferred methods and materials have been described herein, any methods and materials similar or equivalent to those described herein may be used in the implementation or testing of this invention. All references to this specification are incorporated by way of citation to disclose and describe methods and / or materials associated with those references. In the event of any conflict with any incorporated reference, the content of this specification shall prevail.

[0036] Various modifications and variations can be made to the specific embodiments described in this specification without departing from the scope or spirit of the invention, as will be apparent to those skilled in the art. Other embodiments derived from this specification will also be obvious to those skilled in the art. This specification and embodiments are merely exemplary.

[0037] The terms “include,” “including,” “have,” “contain,” etc., used in this article are all open-ended terms, meaning that they include but are not limited to.

[0038] It should be noted that any aspects not described in detail in this invention are conventional practices in the field and are not the focus of this invention.

[0039] Example 1 A method for preparing Ti6Al4V alloy components: (1) Ti6Al4V alloy powder was prepared by gas atomization. The particle morphology was spherical and the particle size was normally distributed in the range of 15 to 53 μm.

[0040] (2) Using Ti6Al4V alloy powder as raw material, the material supply method of powder spreading and powder feeding is adopted, and a high-energy laser beam is used as a heat source. The Ti6Al4V alloy powder is subjected to laser powder bed melting (LPBF, i.e. additive manufacturing) in the additive manufacturing equipment. During the additive manufacturing process, the internal defects are confirmed by online in-situ detection. After the additive manufacturing is completed, the component is taken out from the forming chamber of the additive manufacturing equipment, and the powder is cleaned. Then, the component is cut off by wire cutting to obtain a block sample Ti6Al4V alloy component with a size of 10mm×10mm×10mm.

[0041] The chemical composition of the Ti6Al4V alloy powder is shown in Table 1.

[0042] Table 1 Chemical composition of Ti6Al4V alloy powder The process parameters for laser powder bed melting (the scanning process is achieved by laser transport; when each layer is scanned and melted, the machine tool is vertically lowered to scan the next layer) are shown in Table 2.

[0043] Table 2 Process parameters for laser powder bed melting Metallographic images of the Ti6Al4V alloy components (numbered (1), (2), (3), (4), (5), (6), (7), (8), (9), (10), (11), (12)) prepared in this embodiment are shown below. Figure 1 The defect morphologies of Ti6Al4V alloy components are shown in [reference needed]. Figure 2(a) shows a porosity defect, (b) a keyhole defect, and (c) a lack of fusion. The porosity and average pore diameter of the Ti6Al4V alloy components (numbered (1), (2), (3), (4), (5), (6), (7), (8), (9), (10), (11), and (12)) are shown in [reference needed]. Figure 3 (a) represents porosity, and (b) represents the average pore diameter.

[0044] Figure 1 (1) to (4) are metallographic observation results of Ti6Al4V alloy components obtained by adjusting the laser power under the conditions of a fixed laser scanning speed of 850 mm / s and a fixed scanning interval of 0.10 mm. The defect morphology in the images is mainly regular circular defects, and the magnified morphology is shown in [image missing]. Figure 2 The formation mechanism of this defect is mainly attributed to the porosity induced by the keyhole effect. When the laser energy density is 90 J / mm²... 3 (At a laser power of 230W) up to 114J / mm 3 At high laser power levels (290W), hollow powder and localized areas of the molten pool vaporize, causing keyhole instability and collapse. This traps internal gas or protective gas, forming spherical or near-spherical pore defects. As laser power increases, the energy density received by the powder gradually increases, which not only exacerbates the instability of the molten pool but also leads to an increase in the number and size of keyholes. (See...) Figure 2 Figure (a) shows the defects measured using ImageJ software, with the maximum diameter of the pores reaching 55 μm.

[0045] Figure 1 (5) to (8) are based on the condition that the laser scanning speed is fixed at 1150 mm / s and the scanning interval is fixed at 0.12 mm, and the laser power is adjusted to achieve a laser energy density of 55 J / mm². 3 (At a laser power of 230W) up to 70J / mm 3 Metallographic observation results of Ti6Al4V alloy components obtained within the range of (laser power of 290W). Under these process conditions, the overall porosity of all Ti6Al4V alloy components remained below 0.16%, i.e., the density was higher than 99.84% (for alloy components with laser power of 290W, scanning speed of 1150mm / s, and scanning spacing of 0.12mm). The lowest porosity reached 0.048%. Figure 3 Figure (a) shows a laser power of 290W and an energy density of 70J / mm². 3 Metallographic observation revealed that the defects in these samples were small in size and irregular in shape (see...). Figure 2 (Figure (b)) shows that the average pore diameter is less than 10 μm. Figure 3(Figure (b)) and the energy density decreases continuously as the energy density increases. It is initially speculated that this may be due to the relatively low energy density, which leads to insufficient interlayer bonding. However, this phenomenon is improved as the energy density increases.

[0046] Figure 1 (9) to (12) are the metallographic observation results of Ti6Al4V alloy components obtained by adjusting the scanning spacing (0.10~0.13mm) when the laser scanning speed was fixed at 1450mm / s and the laser power was fixed at 250W. Through metallographic observation, it can be found that when the scanning spacing is small, the higher overlap rate compensates for the limitations on the width and depth of the molten pool caused by insufficient energy density, making the heat distribution on the powder surface more uniform and effectively avoiding poor fusion in local areas due to insufficient energy, thereby reducing incomplete fusion defects. However, as the scanning spacing increases, the average diameter of the pores also increases. Under this condition, the dispersed heat distribution leads to insufficient energy in local areas, resulting in incomplete fusion and exacerbating the poor fusion phenomenon. In addition, due to the influence of powder adhesion and spheroidization effects, circular contour defects appear, as shown in [reference needed]. Figure 2 (c) diagram.

[0047] Example 2 A method for densification of metal additive manufacturing components: The Ti6Al4V alloy components (numbered (1), (2), (3), (4), (5), (6), (7), (8), (9), (10), (11), (12)) prepared in Example 1 were subjected to hot isostatic pressing and then cooled to room temperature in the furnace to obtain densified Ti6Al4V alloy components.

[0048] The parameters for hot isostatic pressing (HIP) are: temperature 920℃, pressure 130MPa, and holding time 2.5h.

[0049] Metallographic images of the densified Ti6Al4V alloy components (numbered (1), (2), (3), (4), (5), (6), (7), (8), (9), (10), (11), (12)) prepared in Example 1 after hot isostatic pressing (HIP) treatment are shown below. Figure 4 .

[0050] from Figure 4 As can be seen, the circular or near-circular defects and unfused defects that were originally present in the alloy almost disappeared after HIP treatment, indicating that HIP treatment effectively promoted the densification of the material and significantly improved the microstructure quality of the alloy.

[0051] The mechanical properties (transverse specimens) of the Ti6Al4V alloy component (numbered (8)) prepared in Example 1 after hot isostatic pressing (HIP treatment) are shown in Table 3.

[0052] The specimens used for tensile property testing are 15mm×15mm×75mm in size. They are prepared into standard tensile specimens by lathe machining in accordance with the national standard GB / T228.1-2015 "Metallic materials - Tensile testing - Part 1". The tensile properties are tested at room temperature using a Zwick / Roell-Z100 electronic universal testing machine.

[0053] The specimens used for hardness testing were 10mm × 10mm × 10mm in size. The Vickers hardness (HV) of the XOZ and XOY surfaces was tested using an HXD-1000TMC / LCD automatic turret micro Vickers hardness tester. The experimental parameters were set with a test load of 300g and a loading time of 15s. The surface hardness value of the specimen was obtained by measuring the average length of the diagonal of the rhomboid indentation.

[0054] Table 3 Mechanical properties of densified Ti6Al4V alloy components Example 3 A method for densification of metal additive manufacturing components: The Ti6Al4V alloy component (numbered (8)) prepared in Example 1 was subjected to low-temperature and low-pressure hot isostatic pressing treatment and cooled to room temperature in the furnace to obtain a densified Ti6Al4V alloy component.

[0055] The low-temperature, low-pressure hot isostatic pressing (HIP) treatment was performed using a Swedish Quintus RD1200 hot isostatic pressing system. The parameters for the low-temperature, low-pressure hot isostatic pressing treatment are shown in Table 4.

[0056] Table 4 Parameters for Low-Temperature Low-Pressure Hot Isostatic Pressing Treatment The stress / strain relationship diagram of the densified Ti6Al4V alloy component prepared in this embodiment is shown in the figure. Figure 5 .

[0057] from Figure 5 As can be seen, at a low temperature of 550℃, the yield strength of the Ti6Al4V alloy component (material) is relatively high, and the externally applied pressure is insufficient to drive the material to undergo sufficiently large elastoplastic strain; the stress effect is almost negligible. However, as the temperature increases, the yield strength of the material gradually decreases, and the external stress field can more effectively drive the healing of defects, and the strain also increases accordingly.

[0058] When the temperature reaches 700℃, the material's plastic strain reaches its peak, and the stress also reaches its maximum. At this temperature, the material's plastic deformation capacity is significant, and dislocation slip and grain boundary migration mechanisms effectively promote the closure of internal defects. As the temperature continues to rise to higher levels, the stress near the defects begins to decrease due to the influence of diffusion creep. At 770℃, the stress reaches its minimum, while the strain tends to be consistent with the previous values. This indicates that under these conditions, the defects have achieved full densification. After densification is completed, further heating may further activate the atoms or molecules inside the material, but since the defects have already been closed, this activity is unlikely to further enhance densification. Instead, it may trigger other microstructural changes, such as grain growth and phase transformation, and may generate additional thermal stress, as seen in the results of HIP treatment in samples 8, 9, and 10.

[0059] Example 4 A method for densification of metal additive manufacturing components: The Ti6Al4V alloy component (numbered (8)) prepared in Example 1 was subjected to low-temperature and low-pressure hot isostatic pressing treatment and cooled to room temperature in the furnace to obtain a densified Ti6Al4V alloy component.

[0060] The low-temperature, low-pressure hot isostatic pressing (HIP) treatment was performed using a Swedish Quintus RD1200 hot isostatic pressing system. The parameters for the low-temperature, low-pressure hot isostatic pressing treatment are shown in Table 5.

[0061] Table 5 Parameters for Low-Temperature Low-Pressure Hot Isostatic Pressing Treatment The stress / strain relationship diagram of the densified Ti6Al4V alloy component prepared in this embodiment is shown in the figure. Figure 6 .

[0062] Table 6 Mechanical properties of densified Ti6Al4V alloy components Traditional high-intensity interphase (HIP) treatment of Ti6Al4V alloys typically involves temperatures ranging from 895 to 955°C and pressures from 100 to 200 MPa. Under these high-temperature and high-pressure conditions, internal defects in the material can be effectively closed, improving the anisotropy of SLM (additive manufacturing) alloys. However, this process is often accompanied by excessive growth of the β phase and grain coarsening, leading to a significant reduction in tensile and yield strength. Selecting a suitable HIP regime within this range requires precise matching of temperature, pressure, and holding time to the microstructure characteristics of the Ti6Al4V alloy, which not only increases the complexity of process control but also limits overall production efficiency.

[0063] In this embodiment, HIP treatment was performed at a temperature below the phase transition temperature (750°C). Within the same holding time, the stress near the defect increased significantly with increasing environmental pressure. However, under constant environmental pressure, extending the holding time led to a decrease in stress. This indicates that appropriately extending the HIP treatment time can effectively alleviate stress concentration caused by differences in environmental pressure.

[0064] from Figure 6 It can be seen that even under HIP treatment conditions of 750℃×60MPa and 3h of heat and pressure holding, defects can still achieve efficient closure. The increase in HIP treatment pressure leads to a linear increase in strain. Under HIP treatment pressure, at higher pressures, defect deformation rapidly transitions from the plastic deformation stage in the initial stage of HIP treatment to the creep stage. With prolonged creep time, the defect healing effect is significant.

[0065] The above results demonstrate that low-temperature treatment (750℃) combined with prolonged heat and pressure holding can effectively close internal defects in Ti6Al4V alloy components, and the final residual stress is far lower than that generated under high temperature and high pressure conditions. The use of a low-temperature, low-pressure (HIP) treatment system not only reduces the complexity of post-processing for additive manufacturing products but also improves overall production efficiency, making densification of defective alloys feasible.

[0066] The embodiments described above are merely preferred embodiments of the present invention and are not intended to limit the scope of the present invention. Various modifications and improvements made by those skilled in the art to the technical solutions of the present invention without departing from the spirit of the present invention should fall within the protection scope defined by the claims of the present invention.

Claims

1. A method for densifying metal additive manufacturing components, characterized in that, Includes the following steps: Metal additive manufacturing components are prepared using additive manufacturing techniques. The metal additive manufacturing component is subjected to low-temperature, low-pressure hot isostatic pressing to obtain a densified alloy component.

2. The method according to claim 1, characterized in that, The temperature of the low-temperature, low-pressure hot isostatic pressing treatment is 700–750℃, the pressure is 60–120 MPa, and the heat and pressure holding time is 3–6 hours.

3. The method according to claim 2, characterized in that, The heating rate of the low-temperature, low-pressure hot isostatic pressing treatment is 5–6 °C / min.

4. The method according to claim 1, characterized in that, The metal additive manufacturing component includes a Ti6Al4V alloy component.

5. The method according to claim 4, characterized in that, The method for preparing the Ti6Al4V alloy component includes the following steps: Ti6Al4V alloy components were obtained by additive manufacturing using Ti6Al4V alloy powder as raw material.

6. The method according to claim 5, characterized in that, The Ti6Al4V alloy powder was prepared by gas atomization or rotating electrode method, and its morphology was spherical with a normal particle size distribution ranging from 15 to 53 μm.

7. The method according to claim 5, characterized in that, The heat source used in the additive manufacturing includes a high-energy beam.

8. The method according to claim 7, characterized in that, The high-energy beam is selected from any one of laser, electric arc, electron beam and plasma arc.

9. The method according to claim 5, characterized in that, The additive manufacturing method is selected from any one of laser powder bed melting, laser directed energy deposition, electron beam additive manufacturing, or electric arc additive manufacturing.

10. The method according to claim 9, characterized in that, The laser power for melting the laser powder bed is 230-290W, the scanning speed is 1150mm / s, and the scanning interval is 0.12mm.

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