L12-(ni,co,fe)3(al,ti,fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing, printed pieces and methods of making

Abstract

The application provides L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing, a printed part and a preparation method thereof, and belongs to the technical field of additive manufacturing of alloys.The powder provided by the application comprises the following metal raw materials in terms of atomic percentage: Ni: 43% to 47%, Co: 15% to 24%, Fe: 11% to 13%, Al: 9% to 12%, Ti: 5% to 12%, Nb: 0 to 10%, Ta: 0 to 10%, V: 0 to 10%, Cr: 0 to 20%, Mo: 0 to 5%, and W: 0 to 5%.The printed part prepared by using the powder provided by the application has high density, excellent strength and plasticity, and excellent mechanical properties, the yield strength of the printed part can reach 650 to 750 Mpa, the tensile strength can be maintained at 1200 to 1250 Mpa, and the fracture elongation can be maintained at 25% to 35%, so that the printed part can maintain good elongation while maintaining good strength.

Description

TECHNICAL FIELD

[0001] The present application belongs to the technical field of additive manufacturing of alloys, and particularly relates to L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing, a printed part and a preparation method thereof. BACKGROUND

[0002] Electron beam selective melting 3D printing technology (EBM) is a kind of rapid prototyping technology which takes metal powder as raw material, selectively melts through concentrated heat source, and then cools and solidifies to finally form a part. Its characteristics are layer-by-layer manufacturing and layer-by-layer stacking. Compared with traditional subtractive manufacturing technology, additive manufacturing technology is not constrained by shape, can save materials and reduce production cost, and is widely used in the fields of biological medicine and aerospace. In recent years, with the continuous development of China's aerospace industry, especially the increasing demand for thrust-to-weight ratio of aero-engines, the temperature resistance demand of turbine blades is increasing, and the internal cooling structure is also increasingly complex, thus posing a severe challenge to the existing manufacturing technology of turbine blades. The traditional investment casting manufacturing technology has a complex process and high manufacturing cost, and additive manufacturing provides a high-potential manufacturing route for rapid manufacturing of complex structural parts. Nickel-based alloys have become the most commonly used high-temperature alloys in the aerospace industry due to their good high-temperature strength and oxidation resistance. However, in nickel-based high-temperature alloys, some high-density refractory metals need to be added to improve their performance, which makes the cost of nickel-based high-temperature alloys high and the density large, and their application fields are also limited. Intermetallic compounds are widely studied as high-temperature structural materials due to their low density, high specific stiffness, high melting point, high high-temperature strength and good oxidation resistance. However, intermetallic compounds are often hard and brittle due to the insufficient number of slip systems and poor grain boundary bonding, and are prone to brittle fracture during room temperature deformation, thus limiting the large-scale application of this type of alloy. In recent years, the proposal of multi-principal intermetallic compounds provides a new idea for the further development of intermetallic compounds. In the system of multi-principal intermetallic compounds, the strength of the material can be improved by the controllable synergistic effect of elements to improve the anti-phase domain boundary energy; at the same time, the ordered-to-disordered phase transition induced by the co-segregation of elements at the grain boundary can improve the grain boundary bonding and thus improve the plasticity of the material. SUMMARY

[0003] Therefore, the purpose of the present application is to provide L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing and a preparation method thereof, a 3D printed part and a preparation method thereof. The printed part prepared by using the powder provided by the present application has high density, excellent strength and plasticity, and excellent mechanical properties.

[0004] In order to achieve the above-mentioned purpose of the application, the application provides the following technical solutions.

[0005] The application provides L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing, which comprises the following metal raw materials in atomic percentage: Ni: 43% to 47%, Co: 15% to 24%, Fe: 11% to 13%, Al: 9% to 12%, Ti: 5% to 12%, Nb: 0 to 10%, Ta: 0 to 10%, V: 0 to 10%, Cr: 0 to 20%, Mo: 0 to 5%, and W: 0 to 5%.

[0006] The application also provides a preparation method of the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing, which comprises the following steps: weighing the above-mentioned metal raw materials according to atomic percentage, melting, atomizing, powdering and screening, so as to obtain the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder.

[0007] Preferably, the particle size distribution of the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder is 60 mu m <= D50 <= 70 mu m, D97 >= 105 mu m, and D3 <= 45 mu m.

[0008] The application also provides a 3D printed part, which comprises the above-mentioned L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing.

[0009] The application also provides a preparation method of the above-mentioned 3D printed part, which comprises the following steps.

[0010] (1) modeling the component to be printed, slicing by using a slicing software, and importing the sliced file into an EBM device;

[0011] (2) setting a substrate preheating temperature;

[0012] (3) setting a contour scanning parameter;

[0013] (4) setting a part scanning parameter;

[0014] (5) setting a scanning strategy of the part;

[0015] (6) loading the powder into a material bin of the EBM device, leveling the substrate, and vacuumizing to 10 -5 Pa;

[0016] (7) According to the parameters set in steps (2)-(6), the EBM device stacks in a mode of workbench descending one layer thickness, scraper powder laying, powder bed preheating, scanning contour and scanning selected area, that is, forming the required printed part.

[0017] Preferably, the substrate preheating temperature in step (2) is 700-1150℃.

[0018] Preferably, the contour scanning parameters in step (3) are: scanning current 8-15 mA, scanning speed 0.8-1 m / s, focusing current -7 mA-7 mA, and molten pool spacing 0.1-0.3 mm.

[0019] Preferably, the part scanning parameters in step (4) are: scanning current 5-15 mA, scanning speed 0.6-1.8 m / s, scanning spacing 0.1-0.15 mm, and focusing current -7 mA-7 mA.

[0020] Preferably, the powder usage in step (6) is at least 3 Kg.

[0021] The application also provides application of L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing in preparation of 3D printed parts.

[0022] The application has the following beneficial effects:

[0023] (1) The electron beam selective melting process of the application can successfully manufacture 3D printed components with specific shapes. By adjusting different process parameters, the printed components have no crack defects and the density can reach 99.7-99.99%;

[0024] (2) The components printed by the electron beam selective melting process of the Ni-Co-Fe-Al-Ti intermetallic compound in the application have a yield strength of 650-750 Mpa, a tensile strength of 1200-1250 Mpa, and a fracture elongation of 25-35%, which can maintain good elongation while maintaining good strength. BRIEF DESCRIPTION OF DRAWINGS

[0025] Figure 1 NCFAT-1 metal powder for 3D printing;

[0026] Figure 2 NCFAT-2 metal powder for 3D printing;

[0027] Figure 3 Electron beam selective melting 3D printing process;

[0028] Figure 4The electron beam selective melting 3D printing model and sample;

[0029] Figure 5 The stress-strain curve of NCFAT-1;

[0030] Figure 6 The microstructure of NCFAT-1;

[0031] Figure 7 The fracture morphology of NCFAT-1;

[0032] Figure 8 The stress-strain curve of NCFAT-2;

[0033] Figure 9 The microstructure of NCFAT-2;

[0034] Figure 10 The fracture morphology of NCFAT-2. DETAILED DESCRIPTION

[0035] The application provides an L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing, which comprises the following metal raw materials in atomic percentage: Ni: 43-47%, Co: 15-24%, Fe: 11-13%, Al: 9-12%, Ti: 5-12%, Nb: 0-10%, Ta: 0-10%, V: 0-10%, Cr: 0-20%, Mo: 0-5%, and W: 0-5%.

[0036] The application does not have special limitations on the source of the metal raw materials, and conventional commercially available products in the field can be used.

[0037] The application further provides a preparation method of the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing, which comprises the following steps: weighing the metal raw materials according to the atomic percentage, melting, atomizing, and powdering, and screening to obtain the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder.

[0038] In the application, the atomic percentage is preferably converted into the mass percentage.

[0039] In the application, the metal raw materials are preferably melted into alloy liquid in an induction furnace. The application does not have special limitations on the source of the induction furnace equipment, and conventional commercially available equipment in the field can be used.

[0040] In the present application, the alloy liquid is preferably injected into a vacuum gas atomization device to prepare metal powder particles by high-speed spraying through gas atomization. The source of the vacuum gas atomization device is not particularly limited in the present application, and a conventional commercially available device can be used.

[0041] In the present application, a standard vibrating powder sifter is preferably used, and after three times of sieving through a 140-mesh standard sieve, fine powder is taken and sieved three times through a 325-mesh standard sieve to obtain L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder. The source of the standard vibrating powder sifter is not particularly limited in the present application, and a conventional commercially available device can be used.

[0042] In the present application, the particle size distribution of the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder is preferably 60 μm≤D50≤70 μm, D97≥105 μm, and D3≤45 μm.

[0043] In the present application, the particle size distribution is preferably 60 μm≤D50≤70 μm for the powder particle size, the proportion of powder with a particle size less than 45 μm is ≤3%, and the powder with a particle size greater than 105 μm is ≤3%.

[0044] The present application also provides a 3D printed part comprising the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing.

[0045] The present application also provides a preparation method of the 3D printed part, comprising the following steps:

[0046] (1) modeling the component to be printed, slicing using slicing software, and importing the sliced file into the EBM device;

[0047] (2) setting the substrate preheating temperature;

[0048] (3) setting the contour scanning parameters;

[0049] (4) setting the part scanning parameters;

[0050] (5) setting the scanning strategy of the part;

[0051] (6) loading the powder into the EBM device hopper, leveling the substrate, and vacuumizing to 10 -5 Pa;

[0052] (7) according to the parameters set in steps (2) to (6), the EBM device is cycled and stacked in the mode of workbench descending by one layer thickness, scraper powder laying, powder bed preheating, contour scanning, and selected area scanning, i.e. forming the required printed part.

[0053] In the present application, when preparing the 3D printed part, the substrate preheating temperature is preferably 700-1150℃; the contour scanning parameters are preferably: scanning current 8-15mA, scanning speed 0.8-1m / s, focusing current -7mA-7mA, and molten pool spacing 0.1-0.3mm; and the part scanning parameters are preferably: scanning current 5-15mA, scanning speed 0.6-1.8m / s, scanning spacing 0.1-0.15mm, and focusing current -7mA-7mA.

[0054] The source of the EBM device is not particularly limited in the present application, and a conventional commercially available product in the art can be used.

[0055] In the present application, when preparing the 3D printed part, the amount of the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal-element intermetallic compound powder is preferably at least 3Kg.

[0056] In the present application, the printed part is preferably cooled in a vacuum furnace, then helium protection gas is introduced for cooling, the powder bed is sandblasted to take out the printed part, the printed part is line-cut, and surface treatment is performed to obtain a treated printed part. The vacuum furnace in the present application refers to the chamber of the electron beam 3D printing device, and after printing is completed, the printed part is preferably directly vacuum insulated in the 3D printing device for 10min, and then protection gas is introduced for cooling. The purpose of vacuum cooling in the present application is to prevent internal stress caused by too fast cooling.

[0057] In the present application, the sandblasted powder is preferably screened through a 140 mesh standard sieve for 3 times to obtain fine powder for recycling.

[0058] The present application also provides an application of the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal-element intermetallic compound powder based on electron beam melting 3D printing in the preparation of a 3D printed part.

[0059] The technical solutions provided by the present application will be described in detail below in combination with examples, but they should not be understood as limiting the scope of protection of the present application.

[0060] Example 1

[0061] Preparation method of Ni 45 Co 23 Fe 12 Al 10.5 Ti 9.5 Preparation method of L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal-element intermetallic compound powder:

[0062] (1) Use ultrasonic cleaning instrument to clean various metal raw materials, according to the atomic proportion 45:23:12:10.5:9.5, respectively take Ni, Co, Fe, Al, Ti a total of 5Kg, the error of various raw materials is within ±01.g;

[0063] (2) The metal raw materials weighed in step (1) are melted into qualified alloy liquid in an induction furnace;

[0064] (3) The alloy liquid prepared in step (2) is injected into a vacuum gas atomization device to form metal powder particles through high-speed spraying of gas atomization;

[0065] (4) After 3 times of screening with a 140-mesh standard sieve, the fine powder is taken and screened 3 times with a 325-mesh standard sieve to obtain the coarse powder sample;

[0066] (5) Take an appropriate amount of sample, use EDS face scanning to analyze the powder composition, and use a laser particle size instrument to test the particle size, and use X-ray diffraction and SEM to analyze the morphology of the powder sample.

[0067] Experimental results:

[0068] The powder sample prepared above is characterized, the morphology of the powder is analyzed by SEM, as shown in Figure 1 (A), the powder has good sphericity, the powder particle size basically meets the printing requirements of the equipment, and small particles are adsorbed on the large particle size powder, which is mainly due to the fact that during the gas atomization powder production, the metal liquid droplets are broken by high-speed airflow to form numerous small droplets, and the small particle size powder balls are easily adsorbed by the large particle size powder balls to form "satellite balls". The powder ball surface presents a typical dendritic structure, which is caused by the influence of the melting and solidification characteristics of the atomization powder production process. The particle size range of the powder is detected by a laser particle size detector instrument. The composition is analyzed by EDS face scanning, as shown in Figure 1 (B), the powder composition is consistent with the set composition, there is no unfused condition, and the pre-alloying requirement is met. As shown in Figure 1 (C), the powder particle size is 60μm≤D50≤70μm, the proportion of powder with a particle size less than 45μm is ≤3%, and the proportion of powder with a particle size greater than 105μm is ≤3%, which meets the equipment particle size requirement. The crystal structure of the powder is analyzed by XRD, as shown in Figure 1 (D), the FCC\L12 diffraction peak and the B2 phase diffraction peak are observed.

[0069] Example 2

[0070] Electron beam selection of Ni 45 Co 22.5 Fe 12 Al 11 Ti9.5 Method for preparing 2-metal powder:

[0071] (1) Use ultrasonic cleaning instrument to clean various metal raw materials, according to the atomic ratio 45:22.5:12:11:9.5, respectively weigh Ni, Co, Fe, Al and Ti a total of 5 kg, the error of various raw materials is within ±0.1 g;

[0072] (2) The weighed metal raw materials in step (1) are melted into qualified alloy liquid in an induction furnace;

[0073] (3) The alloy liquid prepared in step (2) is injected into a vacuum gas atomization device to form metal powder particles by high-speed spraying of gas atomization;

[0074] (4) After 3 times of screening with a 140-mesh standard sieve, take the fine powder and pass it through a 325-mesh standard sieve 3 times to take the coarse powder to obtain the sample;

[0075] (5) Take an appropriate amount of sample, use SEM and EDS to analyze the morphology and composition of the powder, and use a laser particle size instrument to test the particle size.

[0076] Experimental results:

[0077] The prepared powder sample is characterized, the morphology of the powder is analyzed by SEM, as shown in Figure 2 (A), the metal powder maintains good sphericity, which is beneficial to the powder laying flowability in the 3D printing process, and can maintain good powder laying quality in the printing process. The composition is analyzed by EDS area scanning, as shown in Figure 2 (B), the powder composition is consistent with the set composition, there is no unfused condition, which meets the pre-alloying requirement. As shown in Figure 2 (C), the powder particle size is 60 μm≤D50≤70 μm, the proportion of powder with particle size less than 45 μm is ≤3%, and the proportion of powder with particle size greater than 105 μm is ≤3%, which meets the particle size requirement of 3D printing. The crystal structure of the powder is analyzed by XRD, as shown in Figure 2 (D), FCC\L12 diffraction peaks and B2 phase diffraction peaks are observed.

[0078] Example 3

[0079] Preparation method of electron beam selective melting 3D printed Ni 45 Co 23 Fe 12 Al 10.5 Ti 9.5 -1:

[0080] (1) Model the component to be printed, slice the model using slicing software, and import the sliced file into the EBM device;

[0081] (2) Set the substrate preheating temperature: preheating temperature 850℃;

[0082] (3) Set the profile scanning parameters: scanning current 10mA, scanning rate 1m / s, focusing current 0mA, pool spacing 0.2mm;

[0083] (4) Set the part scanning parameters: scanning current 11mA, scanning rate 1.4m / s, scanning spacing 0.15mm, focusing current -1mA;

[0084] (5) Set the scanning strategy of the part, starting angle 45°, rotation angle 90°, rotation layer 1 layer;

[0085] (6) Put 5Kg of the powder of Example 1 into the EBM equipment hopper, level the substrate, and vacuumize to 10 -5 Pa;

[0086] (7) According to the parameters set in steps (1)-(6), the EBM equipment cyclically stacks in the mode of descending one layer thickness of the workbench, scraper powder laying, preheating the powder bed, scanning the profile, and scanning the selected area, to finally form the required printed part;

[0087] (8) After printing is completed, the printed part is cooled for 10min in the vacuum furnace, helium protection gas is introduced for cooling, the printed part is line-cut, and surface treatment is performed, to finally form the required printed part;

[0088] (9) The alloy sample is rough ground by using different types of sandpaper in stages: 240 mesh, 1000 mesh, and 2000 mesh, and then is mechanically polished for rough polishing and fine polishing, until the alloy surface has no obvious scratches and is bright and mirror-like, the sample density is tested by using the drainage method to calculate the density, and the microstructure of the alloy is observed by using X-ray diffraction and scanning electron microscopy;

[0089] (10) The alloy prepared by the above method is prepared into a tensile sample, different types of sandpaper are used to rough grind the sample in stages to remove the oxide skin, and the room temperature tensile properties are tested by using an electronic universal testing machine, and the test results are shown in Table 1;

[0090] (11) The fracture morphology is observed by using a scanning electron microscope, and the fracture mechanism is evaluated.

[0091] Table 1 Room temperature tensile mechanical properties of NCFAT-1 alloy

[0092]

[0093] Experimental results:

[0094] The process steps of the above electron beam selective melting 3D printing are recorded as follows:Figure 3 (A)(B)(C)(D) shows that the whole process is stable, the powder bed surface uniformity is good, the powder bed sintering degree is moderate, and the powder bed recycling rate is high. The printed modeling and the printed sample are shown in Figure 4 (A)(B) shows that the printed part has high reduction degree to the model, small surface roughness, and the whole presents a dense state.

[0095] The NCFAT-1 alloy prepared above was tested and characterized. The alloy sample was processed into a dumbbell shape by wire cutting, and the room temperature tensile property test of the alloy sample material was carried out by using a universal tensile testing machine, and the test results are shown in Figure 5 The experimental results show that the yield strength of NCFAT-1 alloy is 702 MPa, the fracture strength is 1247 MPa, and the fracture elongation is 28.5% when deformed at room temperature. NCFAT-1 alloy has excellent comprehensive mechanical properties at room temperature, and has both strength and elongation. At the same time, the density obtained by the drainage method reaches 99.95%.

[0096] The crystal structure of NCFAT-1 alloy was analyzed by XRD, as shown in Figure 6 (A) shows that FCC / L12 phase and B2 phase are observed. Figure 6 (B) shows that the printed component presents equiaxed crystal morphology in the horizontal direction; Figure 6 (C) shows that the printed component presents columnar crystal morphology in the vertical direction. Figure 6 (D)(E)(F) shows that the main morphology of the printed component is dispersedly distributed B2 phase and reticulatedly distributed FCC channel in L12 phase. By Figure 7 (A)(B) analyzes the fracture morphology, and the dimples and cleavage planes can be observed, B2 phase plays a role of dispersion strengthening in the component matrix, and FCC phase increases the interface, which also plays a role of strengthening.

[0097] Example 4

[0098] Electron beam selective melting 3D printing Ni 45 Co 22.5 Fe 12 Al 11 Ti 9.5 Preparation method of EBM printed part:

[0099] (1) Model the component to be printed, slice the component by using slicing software, and import the sliced file into the EBM equipment;

[0100] (2) Set the substrate preheating temperature: preheating temperature 950℃;

[0101] (3) Set the contour scanning parameters: scanning current 10 mA, scanning rate 1 m / s, focus 0 mA, pool spacing 0.1 mm;

[0102] (4) Set the part scanning parameters: scanning current 8.5 mA, scanning rate 1.8 m / s, scanning spacing 0.15 mm, focus current -3 mA;

[0103] (5) Set the scanning strategy of the part: starting angle 0°, rotation angle 180°, rotation layer 1 layer;

[0104] (6) Load 5Kg of the powder of Example 2 into the EBM device hopper, level the substrate, and vacuum to 10-5Pa;

[0105] (7) According to the parameters set in steps (1)-(6), the EBM device circulates stacking in the mode of workbench descending one layer thickness, scraper powder laying, preheating powder bed, scanning contour, and scanning selected area, to finally form the required printed part;

[0106] (8) After printing is completed, the printed part is cooled in the vacuum furnace for 10 min, helium gas protection gas is introduced for cooling, the printed part is line-cut, surface treated, and finally the required printed part is formed.

[0107] (9) Coarsely grind the alloy sample with different types of sandpaper in stages: 240 mesh, 1000 mesh, and 2000 mesh, and then perform mechanical polishing for coarse polishing and fine polishing until the alloy surface has no obvious scratches and appears bright and mirror-like. The density of the sample is tested by the drainage method to calculate the density, and the microstructure of the sample is observed by X-ray diffraction and scanning electron microscopy.

[0108] (10) Prepare the alloy prepared by the above method into a tensile specimen, coarsely grind the alloy with different types of sandpaper in stages to remove the oxide skin, and test the room temperature tensile properties by means of an electronic universal testing machine. The test results are shown in Table 2.

[0109] (11) Observe the fracture morphology by means of a scanning electron microscope to evaluate the fracture mechanism.

[0110] Table 2 Room temperature tensile mechanical properties of NCFAT-2 alloy

[0111]

[0112] The NCFAT-2 alloy prepared by the above method is tested and characterized, the alloy sample is processed into a dumbbell shape by line cutting, and the room temperature tensile property of the alloy sample material is tested by means of a universal tensile testing machine. The test results are as follows Figure 8The experimental results show that the yield strength of the NCFAT-2 alloy is 702 MPa, the fracture strength is 1247 MPa, and the fracture elongation is 28.5% when deformed at room temperature. By improving the preheating temperature and scanning parameters, the NCFAT-2 alloy realizes higher elongation, has excellent comprehensive mechanical properties at room temperature, and balances the strength and ductility. At the same time, the density obtained by the drainage method reaches 99.9%.

[0113] The crystal structure of the NCFAT-2 alloy is analyzed by XRD, as shown in Figure 9 (A), and the FCC / L12 phase and B2 phase are observed. Figure 9 (B) shows that the printed component presents an equiaxed crystal morphology in the horizontal direction; Figure 9 (C) shows that the printed component presents a columnar crystal morphology in the vertical direction, and the whole printed part has no crack defects and high density. Figure 9 (D)(E)(F) show that the main morphology of the printed component is dispersedly distributed B2 phase and reticulatedly distributed FCC channel in the L12 phase. By Figure 10 (C)(D) analyzing the fracture morphology, it can be observed that the dimples and cleavage planes exist at the same time, the B2 phase plays a role in dispersion strengthening in the component matrix, and the FCC phase strengthens the matrix, so that this part presents the characteristics of ductile fracture.

[0114] The above only describes the preferred embodiments of the present application, and it should be noted that for those skilled in the art, without departing from the principles of the present application, a number of improvements and refinements can be made, and these improvements and refinements should also be considered as the protection scope of the present application.

Claims

1. A 3D printed piece, characterized in that, The L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder based on electron beam melting 3D printing comprises the following metal raw materials in atomic percentage: Ni: 43% to 47%, Co: 15% to 24%, Fe: 11% to 13%, Al: 9% to 12%, Ti: 5% to 12%, Nb: 0 to 10%, Ta: 0 to 10%, V: 0 to 10%, Cr: 0 to 20%, Mo: 0 to 5%, and W: 0 to 5%. The particle size distribution of the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder is 60 μm≤D50≤70 μm, D97≥105 μm, and D3≤45 μm. The 3D printed part has a main morphology of B2 phase dispersedly distributed in L12 phase and FCC channels in a network distribution.

2. The 3D printed piece of claim 1, characterized in that, The method comprises the following steps: The metal raw materials in atomic percentage according to claim 1 are weighed, melted, atomized, powdered, and sieved to obtain the L12-(Ni, Co, Fe)3(Al, Ti, Fe) type multi-principal intermetallic compound powder.

3. The method of producing a 3D printed piece according to claim 1, characterized in that, The method comprises the following steps: (1) modeling the component to be printed, slicing the component by using a slicing software, and importing the sliced file into an EBM device; (2) setting a substrate preheating temperature; (3) setting a contour scanning parameter; (4) setting a part scanning parameter; (5) setting a scanning strategy of the part; (6) The powder of claim 1 is loaded into the EBM machine hopper, the substrate is leveled, vacuum is pulled to 10 -5 Pa; (7) according to the parameters set in steps (2) to (6), the EBM device is cycled and stacked in a way of workbench descending by one layer thickness, scraper powder laying, powder bed preheating, contour scanning, and selected area scanning, to form the required printed part.

4. The method of claim 3, wherein the 3D printed part is a 3D printed part of a medical device. The substrate preheating temperature in step (2) is 700 to 1150 ℃.

5. The method of claim 3, wherein the 3D printed part is prepared by a method comprising: The contour scanning parameter in step (3) is: a scanning current of 8 to 15 mA, a scanning speed of 0.8 to 1 m / s, a focusing current of -7 mA to 7 mA, and a melt pool spacing of 0.1 to 0.3 mm.

6. The method of claim 3, wherein the 3D printed part is a 3D printed part of a medical device. The part scanning parameter in step (4) is: a scanning current of 5 to 15 mA, a scanning speed of 0.6 to 1.8 m / s, a scanning spacing of 0.1 to 0.15 mm, and a focusing current of -7 mA to 7 mA.

7. The method of claim 3, wherein the 3D printed part is a 3D printed part of a vehicle. The powder usage in step (6) is at least 3 Kg.

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