Nickel-based alloy cored wire, preparation method and method for additive manufacturing of nickel-based alloy

Abstract

The present invention discloses a nickel-based alloy cored wire, a preparation method thereof, and a method for additive manufacturing of nickel-based alloys, belonging to the technical field of nickel-based superalloys for additive manufacturing. The high-Ti, Al crack-free nickel-based superalloy cored wire includes a wire outer skin and a mixed powder wrapped inside the wire outer skin; the wire outer skin is made of soft or semi-hard pure nickel strip, and the filling rate of the internal mixed powder is 30-35%. The mass percentages of the mixed powder are as follows: chromium powder 15%, aluminum powder 3.5%-6%, titanium powder 3.5%-6%, ceramic phase particle powder 0.5%-1%, and the balance is iron powder; at the same time, a preparation method of the above wire and an additive manufacturing method of nickel-based superalloy are also disclosed. The present invention utilizes an additive manufacturing method to develop a printable nickel-based superalloy with ultra-high temperature strength above 800°C. By introducing a trace amount of ceramic phase, the significantly increased grain boundaries enhance the grain boundary cohesion and make the accumulated thermal stress uniform, effectively suppressing thermal cracks, and having the advantages of high efficiency, low cost, and the ability to print large components.

Description

Technical Field

[0001] The present invention relates to the technical field of nickel-based superalloys for additive manufacturing, and specifically relates to nickel-based alloy cored wires, preparation methods, and methods for additive manufacturing nickel-based alloys. Background Art

[0002] With the rapid development of the aerospace industry, higher requirements are put forward for the thermal efficiency of aeroengines. By increasing the working temperature of the hot-end components of the engine, the thermal efficiency of the engine can be effectively improved. Therefore, improving the service temperature and high-temperature mechanical properties of superalloys has become the current research focus. Some studies have shown that for nickel-based superalloys, within a certain range, the content of γ'-Ni3(Al,Ti) precipitate phases is proportional to the high-temperature strength. When the content of γ' precipitate phases reaches 65%-70%, its high-temperature performance is the best. Since elements such as Al and Ti are the main elements for forming the γ' phase, adding Al elements and Ti elements to nickel-based superalloys can increase the proportion of the γ' phase, thereby improving the high-temperature strength of the alloy.

[0003] The strength of nickel-based alloys at high temperatures is generally determined by factors such as the size, quantity, and distribution characteristics of the γ' phase. However, the quantity of the γ' phase determines the hot working performance, and the more of it, the more difficult it is to forge and form. Therefore, for nickel-based alloys with a high Al+Ti (Al content ≥ 3.5%, Ti content ≥ 3.5%) content, traditional hot working methods are no longer suitable. With the rapid development of additive manufacturing technology, this technology has significant advantages in alloy development and forming, opening up opportunities for the design of new alloys. Therefore, for the additive manufacturing process, developing printable nickel-based alloy compositions with a high Al+Ti content has broad application prospects.

[0004] The existing patent CN111266578B discloses a method for suppressing cracks in the additive manufacturing of difficult-to-weld nickel-based alloys. The steps of the method are as follows: Select difficult-to-weld powder and weldable powder, dry them and use them as additive raw materials. Adopt the laser direct deposition technology and print in a cycle according to the alternate printing method of difficult-to-weld and weldable materials, that is, print 1 layer of weldable powder after printing 2-5 layers of difficult-to-weld powder until the printing of the additive model to be manufactured is completed. The method is simple and feasible, can suppress the formation of cracks in the additive manufacturing process in-situ, effectively solves the problem of rapid nucleation and growth of cracks in the additive manufacturing by conventional methods, saves the high cost required to eliminate cracks in the post-treatment period, and improves the plasticity and toughness while ensuring the strength of the obtained additive parts. At the same time, this method also has certain defects. 1) During the printing process of this method, each time the additive raw materials for printing are switched, it is necessary to stop the laser from emitting light, stop the movement of the laser processing head, and keep it for 5-10 s. After the powder delivery of the switched additive raw materials is stable, continue to perform printing. It can be seen that this method cannot achieve efficient, continuous, and large-scale printing components. 2) This method has a special deposition method of alternating printing of difficult-to-weld and weldable superalloys, resulting in poor control of the usage ratio of difficult-to-weld powder and weldable powder during the alternating printing process, resulting in large composition deviation and unstable performance of the printed parts.

[0005] CN114032421B discloses a nickel-based superalloy, a nickel-based superalloy powder material and a product for additive manufacturing, belonging to the technical field of nickel-based superalloys for additive manufacturing. The nickel-based superalloy includes the following elements in the following contents: by weight percentage, Cr: 21-25%, Co: 18-20.5%, Al: 0.8-1.7%, Ti: 1.5-4.3%, W: 1.3-2.2%, Ta: 0.6-1.5%, Nb: 0.6-1.8%, C: 0.25-0.6%, and the balance is Ni and unavoidable impurities. By controlling the types and contents of key alloying elements in the alloy composition, the invention not only enhances the high-temperature strength of the alloy product, but also can inhibit the generation of microcracks in the alloy product. After the nickel-based superalloy powder material of the invention is formed by laser powder bed melting, it can print out uniform and dense complex parts that meet the requirements of high-temperature and high-strength. There are also certain defects. The preparation cost of the alloy powder is high, and the deposition efficiency is low compared with the powder core wire, and the additive manufacturing of large structural parts cannot be realized. At the same time, the Al content of the invention is 0.8-1.7%, and the Ti content is 1.5-4.3%, which does not reach the composition range of high-Ti and Al nickel-based alloys. Summary of the Invention

[0006] The purpose of the present invention is to overcome the problems in the prior art, and develop a printable nickel-based superalloy with ultra-high temperature strength above 800 °C by using the additive manufacturing method, mainly by increasing the Ti and Al ratios and adding trace ceramic particles.

[0007] The metal cored wire of the present invention is made by mixing and adding pure nickel skin and elemental powders of various alloying elements. It has both the advantages of variable composition in the powder spreading and feeding method of additive manufacturing and the advantage of printing large components in the wire feeding method of additive manufacturing. Therefore, the method using the metal cored wire has the advantages of high efficiency, low cost, and the ability to print large components.

[0008] One of the objectives of the present invention is to provide a high-Ti, Al crack-free nickel-based superalloy cored wire, which includes a wire outer skin and mixed powder wrapped inside the wire outer skin; the wire outer skin uses a soft or semi-hard pure nickel strip, and the filling rate of the internal mixed powder is 30-35%. The mass percentages of the mixed powder are as follows: chromium powder 15%, aluminum powder 3.5%-6%, titanium powder 3.5%-6%, ceramic phase particle powder 0.5%-1%, and the balance is iron powder.

[0009] Preferably, the nickel strip has a thickness of 0.3 mm and a width of 8 mm.

[0010] Preferably, the chromium powder, aluminum powder, titanium powder, and iron powder are all elemental pure powders.

[0011] Preferably, the powder particles are preferably spherical powders, and the diameter range of the spherical powder particles is 50-100 μm.

[0012] Preferably, the ceramic phase particles are preferably SiC particles.

[0013] Another objective of the present invention is to provide a preparation method for the above high-Ti, Al crack-free nickel-based superalloy cored wire, and the steps are as follows:

[0014] Weigh and prepare each powder according to the set composition.

[0015] Place the mixed powder in a high-energy ball milling tank and perform ball milling for 10-15 h. The mass ratio of the grinding balls to the mixed powder is 10:1 to achieve full homogenization and alloying of the mixed powder; place the mixed powder in a vacuum drying oven, keep it at 80-120 °C and dry for 10 h; roll the pure nickel strip into a U shape, then add the mixed powder into the U-shaped groove, adjust the set first-pass filling rate to 30-35%, and the filling rate is the ratio of the mass of the mixed powder in the unit length of the wire to the total mass of the unit length of the wire; through the first-pass drawing die hole with a diameter of 2.8 mm, close the U-shaped groove so that the powder is wrapped inside. The closing part adopts a butt joint method, and gradually draw and reduce the diameter through the drawing die hole until its diameter reaches 1.6 mm; between the last pass and the wire take-up reel, perform a decontamination treatment, and finally wind the obtained cored wire into a coil to obtain a high-Ti, Al and SiC ceramic phase composite strengthened nickel-based alloy cored wire for electron beam fused wire additive manufacturing.

[0016] The aperture diameters of the drawing die holes include 2.8 mm, 2.6 mm, 2.4 mm, 2.2 mm, 2.0 mm, 1.9 mm, 1.8 mm, 1.7 mm, and 1.6 mm, and the diameter is gradually reduced by drawing in successive passes from large to small.

[0017] The third object of the present invention is to provide a method for additive manufacturing of a nickel-based alloy using the above high-Ti, Al crack-free nickel-based superalloy. Using an electron beam as a heat source, the prepared nickel-based alloy cored wire is assembled onto a wire feeder and sent to the lower beam position of the electron beam through a wire feeding nozzle, and the wire feeding angle and the dry extension length are fixed;

[0018] Fix the additive manufacturing substrate on the workbench and close the hatch of the vacuum chamber;

[0019] Turn on the vacuum pump to evacuate. When the vacuum degree reaches 5×10 -2 Pa, hold it, set the electron beam additive manufacturing parameters, and print layer by layer according to the set deposition path to finally obtain the target nickel-based alloy additive component.

[0020] Preferably, the electron beam wire melting additive manufacturing process parameters are: the acceleration voltage is 10 - 30 KV, the electron beam current is 30 - 50 mA, the wire feeding speed is 500 - 900 mm / min, and the movement speed is 120 - 210 mm / min; after each layer of printing in the above solution, use the numerical control panel to move the workbench, raise the electron gun, return to the starting position, and lower it to an appropriate height. Wait until the substrate and the deposited specimen cool to below 50 °C before proceeding with the next deposition.

[0021] Preferably, the angle between the wire and the substrate is 30 - 45°, the distance between the wire and the upper surface of the substrate is 0.5 - 2 mm, and the dry extension length is 5 - 10 mm to ensure a continuous liquid bridge transition during the additive manufacturing process.

[0022] Compared with the prior art, the beneficial effects of the present invention are:

[0023] 1. Develop a printable nickel-based superalloy with ultra-high temperature strength above 800 °C using an additive manufacturing method. The proportion of the precipitated strengthening phase γ' phase reaches 55 - 70%, realizing the composite strengthening of γ' phase and ceramic particles, thereby obtaining a nickel-based superalloy with ultra-high temperature strength.

[0024] 2. Nickel-based superalloys with high (Ti + Al) content have extremely poor weldability and are prone to forming a liquid film at the large-angle grain boundary position during the additive manufacturing process, thus generating hot cracks. The present invention introduces a trace amount of ceramic phase, increasing the low-angle grain boundaries by 30 - 50%. The significantly increased grain boundaries enhance the cohesion of the grain boundaries and make the accumulated thermal stress uniform, effectively suppressing hot cracks.

[0025] 3. The metal cored wire is made by mixing and adding pure nickel skin and elemental powders of various alloying elements. It has the advantages of variable composition in the powder laying and feeding method of additive manufacturing and the ability to print large components in the wire feeding method of additive manufacturing. Therefore, the method using metal cored wire has the advantages of high efficiency, low cost, and the ability to print large components. Brief Description of the Drawings

[0026] Figure 1 Tensile curve of the deposited part in Example 1 of the present invention;

[0027] Figure 2 Microstructure diagram of the deposited part in Example 1 of the present invention. Detailed Description of the Invention

[0028] The following describes in detail the specific implementation manners of the present invention in conjunction with embodiments. However, it should be understood that the protection scope of the present invention is not limited by the specific implementation manners. Based on the embodiments of the present invention, all other embodiments obtained by those of ordinary skill in the art without creative efforts belong to the protection scope of the present invention.

[0029] One of the purposes of the present invention is to provide a high-Ti, Al crack-free nickel-based superalloy cored wire, including a wire outer skin and mixed powder wrapped inside the wire outer skin; the wire outer skin uses a soft or semi-hard pure nickel strip, and the filling rate of the internal mixed powder is 30-35%. The mass percentages of the mixed powder are as follows: chromium powder 15%, aluminum powder 3.5%-6%, titanium powder 3.5%-6%, ceramic phase particle powder 0.5%-1%, and the balance is iron powder.

[0030] Preferably, the nickel strip has a thickness of 0.3 mm and a width of 8 mm.

[0031] Preferably, the chromium powder, aluminum powder, titanium powder, and iron powder are all elemental pure powders.

[0032] Preferably, the powder particles are preferably spherical powders, and the diameter range of the spherical powder particles is 50-100 μm.

[0033] Preferably, the ceramic phase particles are preferably SiC particles.

[0034] The present invention also provides a preparation method for the above high-Ti, Al crack-free nickel-based superalloy cored wire, and the steps are as follows:

[0035] Weigh and mix each powder according to the set composition;

[0036] Place the mixed powder in a high-energy ball milling jar and perform ball milling for 10 - 15 h. The mass ratio of the grinding balls to the mixed powder is 10:1 to achieve sufficient homogenization and alloying of the mixed powder. Place the mixed powder in a vacuum drying oven and dry it at 80 - 120 °C for 10 h. Roll the pure nickel strip into a U shape, then add the mixed powder into the U-shaped groove, and adjust the set filling rate of the first pass to 30 - 35%. The filling rate is the ratio of the mass of the mixed powder in the wire of unit length to the total mass of the wire of unit length. Through the drawing die hole with a diameter of 2.8 mm in the first pass, close the opening of the U-shaped groove to wrap the powder inside. The joint part adopts a butt joint method, and gradually reduce the diameter by drawing through the drawing die hole until its diameter reaches 1.6 mm. Between the last pass and the wire take-up reel, perform a decontamination treatment, and finally wind the obtained powder core wire into a coil to obtain a high-Ti, Al and SiC ceramic phase composite strengthened nickel-based alloy powder core wire for electron beam melting wire additive manufacturing.

[0037] The aperture diameters of the drawing die holes include 2.8 mm, 2.6 mm, 2.4 mm, 2.2 mm, 2.0 mm, 1.9 mm, 1.8 mm, 1.7 mm, 1.6 mm, and gradually reduce the diameter by drawing from large to small in each pass.

[0038] The present invention also provides an additive manufacturing method for a high-Ti, Al crack-free nickel-based superalloy. Using an electron beam as a heat source, assemble the prepared nickel-based alloy powder core wire onto a wire feeder and send it to the lower beam position of the electron beam through a wire feeding nozzle, and fix the wire feeding angle and the dry extension length.

[0039] Fix the additive manufacturing substrate on the workbench and close the vacuum chamber door.

[0040] Turn on the vacuum pump to pump vacuum. When the vacuum degree reaches 5×10 -2 Pa, hold it, set the electron beam additive manufacturing parameters, and print layer by layer according to the set deposition path to finally obtain the target nickel-based alloy additive component.

[0041] Preferably, the electron beam melting wire additive manufacturing process parameters are: the acceleration voltage is 10 - 30 KV, the electron beam current is 30 - 50 mA, the wire feeding speed is 500 - 900 mm / min, and the movement speed is 120 - 210 mm / min. After each layer of printing in the above scheme, use the numerical control panel to move the workbench, raise the electron gun, return to the starting position, and lower it to a suitable height, and wait until the substrate and the deposited specimen cool to below 50 °C before performing the next deposition.

[0042] Finally, inflate and open the door, take out the nickel-based alloy electron beam additive specimen, and select typical positions for microstructure and mechanical property analysis. The tensile strength of the obtained nickel-based alloy is 910 MPa - 1050 MPa, and the microhardness is 465 - 515 HV.

[0043] Preferably, the included angle between the wire and the substrate is 30-45°, the distance between the wire and the upper surface of the substrate is 0.5-2 mm, and the dry extension length is 5-10 mm, ensuring a continuous liquid bridge transition during the additive process.

[0044] Example 1:

[0045] The specific operation steps of this example are as follows:

[0046] S1. The outer skin of the wire is made of semi-hard pure nickel strip with a thickness of 0.3 mm and a width of 8 mm. The filling rate of the mixed powder is set to 30%. Therefore, the mixed powder is as follows by mass fraction: chromium powder 15%, aluminum powder 3.5%, titanium powder 3.5%, SiC powder 1%, iron powder 8%. The powder particle size is 200 mesh, and each powder is weighed and proportioned separately. The mixed powder is placed in a high-energy ball milling tank for ball milling for 10-15 h, and the mass ratio of the grinding balls to the mixed powder is 10:1. The mixed powder is placed in a vacuum drying oven and dried at 120 °C for 10 h.

[0047] S2. The pure nickel strip is rolled into a U shape, and then the mixed powder is added into the U-shaped groove. The filling rate of the first pass is adjusted to 30%, and through the drawing die hole with a diameter of 2.8 mm in the first pass, the U-shaped groove is closed so that the powder is wrapped therein. The closing part adopts a butt joint method and successively passes through the drawing die holes with diameters of 2.8 mm, 2.6 mm, 2.4 mm, 2.2 mm, 2.0 mm, 1.9 mm, 1.8 mm, 1.7 mm, and 1.6 mm for successive drawing and diameter reduction until the wire diameter finally reaches 1.6 mm. Then, it is decontaminated with degreased cotton and alcohol, and finally the obtained powder core wire is wound into a coil.

[0048] S3. The nickel-based alloy powder core wire prepared in step S2 is assembled onto a wire feeder and sent to the lower position of the electron beam through a wire feeding nozzle. The wire feeding angle is fixed at 45° and the dry extension length is 5 mm. The additive substrate is fixed on the workbench, and the vacuum chamber door is closed. The electron beam wire melting additive process parameters are set as follows: acceleration voltage is 20 KV, electron beam current is 45 mA, wire feeding speed is 500 mm / min, and moving speed is 180 mm / min. Finally, a single-pass 30-layer nickel-based alloy deposition part is obtained, and typical positions are selected for microstructure and mechanical property analysis. The tensile strength of the obtained nickel-based alloy is 910 MPa, and the microhardness is 470 HV.

[0049] Example 2:

[0050] The specific operation steps of this example are as follows:

[0051] S1. The outer skin of the wire is made of semi-hard pure nickel strip with dimensions: thickness 0.3 mm and width 8 mm. The filling rate of the mixed powder is set at 32%, so the mixed powder is as follows by mass fraction: chromium powder 15%, aluminum powder 5%, titanium powder 5%, SiC powder 1%, and iron powder 6%. The powder particle size is 200 mesh, and each powder is weighed proportionally for powder blending. The mixed powder is placed in a high-energy ball milling tank for ball milling for 10 - 15 h, and the mass ratio of the grinding balls to the mixed powder is 10:1. The mixed powder is placed in a vacuum drying oven and dried at 120 °C for 10 h.

[0052] S2. Roll the pure nickel strip into a U shape, then add the above-mentioned mixed powder into the U-shaped groove, adjust and set the filling rate of the first pass to 32%, pass through the drawing die hole with a diameter of 2.8 mm in the first pass, close the mouth of the U-shaped groove to wrap the powder inside, the joint part adopts a butt joint method, and successively pass through the drawing die holes with diameters of 2.8 mm, 2.6 mm, 2.4 mm, 2.2 mm, 2.0 mm, 1.9 mm, 1.8 mm, 1.7 mm, and 1.6 mm for successive drawing and diameter reduction until the wire diameter finally reaches 1.6 mm. Then, use degreasing cotton and alcohol for decontamination treatment, and finally wind the obtained powder core wire into a coil.

[0053] S3. Assemble the nickel-based alloy powder core wire prepared in step S2 onto a wire feeder, and send it to the lower position of the electron beam through the wire feeding nozzle. Fix the wire feeding angle at 45° and the dry extension length at 5 mm. Fix the additive manufacturing substrate on the workbench and close the vacuum chamber door. Set the electron beam wire melting additive manufacturing process parameters as follows: acceleration voltage 20 KV, electron beam current 45 mA, wire feeding speed 500 mm / min, and movement speed 180 mm / min. Finally, obtain a single-pass 30-layer nickel-based alloy deposition part, and select typical positions for microstructure and mechanical property analysis. The tensile strength of the obtained nickel-based alloy is 1050 MPa, and the microhardness is 485 HV.

[0054] Example 3:

[0055] The specific operation steps of this example are as follows:

[0056] S1. The outer skin of the wire is made of semi-hard pure nickel strip with dimensions: thickness 0.3 mm and width 8 mm. The filling rate of the mixed powder is set at 33%, so the mixed powder is as follows by mass fraction: chromium powder 15%, aluminum powder 6%, titanium powder 6%, SiC powder 1%, and iron powder 5%. The powder particle size is 200 mesh, and each powder is weighed proportionally for powder blending. The mixed powder is placed in a high-energy ball milling tank for ball milling for 10 - 15 h, and the mass ratio of the grinding balls to the mixed powder is 10:1. The mixed powder is placed in a vacuum drying oven and dried at 120 °C for 10 h.

[0057] S2. Roll the pure nickel strip into a U shape, then add the mixed powder into the U-shaped groove, adjust the set filling rate of the first pass to 33%, pass through the drawing die hole with a diameter of 2.8 mm in the first pass, close the mouth of the U-shaped groove to wrap the powder inside. The joint part adopts a butt joint method and passes through the drawing die holes with diameters of 2.8 mm, 2.6 mm, 2.4 mm, 2.2 mm, 2.0 mm, 1.9 mm, 1.8 mm, 1.7 mm, and 1.6 mm in sequence to reduce the diameter by drawing in each pass. Finally, the diameter of the wire is reduced to 1.6 mm. Then, use degreased cotton and alcohol for decontamination treatment, and finally wind the obtained powder core wire into a coil.

[0058] S3. Assemble the nickel-based alloy powder core wire prepared in step 2 onto the wire feeder, and send it to the lower position of the electron beam through the wire feeding nozzle. Fix the wire feeding angle at 45° and the dry extension length at 5 mm. Fix the additive manufacturing substrate on the workbench and close the hatch of the vacuum chamber. Set the electron beam fused deposition additive manufacturing process parameters as follows: acceleration voltage is 20 KV, electron beam current is 45 mA, wire feeding speed is 500 mm / min, and movement speed is 180 mm / min. Finally, obtain a single-pass 30-layer nickel-based alloy deposition part, and select typical positions for microstructure and mechanical property analysis. The tensile strength of the obtained nickel-based alloy is 1150 MPa, and the microhardness is 503 HV.

[0059] Although the embodiments of the present invention have been shown and described, those of ordinary skill in the art can understand that various changes, modifications, substitutions, and variations can be made to these embodiments without departing from the principles and spirit of the present invention. The scope of the present invention is defined by the appended claims and their equivalents.

Claims

1. A high-Ti, Al crack-free nickel-based superalloy cored wire, characterized in that, It includes a wire outer skin and a mixed powder wrapped inside the wire outer skin; the wire outer skin is made of soft or semi-hard pure nickel strip, and the filling rate of the internal mixed powder is 30 - 35%, where the filling rate is the ratio of the mass of the mixed powder in the wire per unit length to the total mass of the wire per unit length; the mass percentages of the mixed powder are as follows: 15% chromium powder, 3.5% - 6% aluminum powder, 3.5% - 6% titanium powder, 0.5% - 1% ceramic phase particle powder, and the balance is iron powder. By introducing a trace amount of ceramic phase, the low-angle grain boundaries are increased.

2. The high-Ti, Al crack-free nickel-based superalloy cored wire according to claim 1, characterized in that, The size of the pure nickel strip is 0.3 mm in thickness and 8 mm in width.

3. The high-Ti, Al crack-free nickel-based superalloy cored wire according to claim 1, characterized in that, The chromium powder, aluminum powder, titanium powder, and iron powder are all elemental pure powders.

4. The high-Ti, Al crack-free nickel-based superalloy cored wire according to claim 1, characterized in that, The mixed powder is spherical powder, and the particle diameter range of the spherical powder is 50 - 100 μm.

5. The high-Ti, Al crack-free nickel-based superalloy cored wire according to claim 1, characterized in that, The ceramic phase particle powder is SiC particles.

6. The preparation method of the high-Ti and Al crack-free nickel-based superalloy cored wire according to claim 1, characterized in that, The steps are as follows: Weigh and prepare each powder according to the set composition; Place the mixed powder in a high-energy ball milling tank for ball milling for 10 - 15 h, and the mass ratio of the grinding balls to the mixed powder is 10:1 to achieve full homogenization and alloying of the mixed powder; place the mixed powder in a vacuum drying oven and keep it at 80 - 120 °C for drying for 10 h; roll the pure nickel strip into a U shape, then add the mixed powder into the U-shaped groove, and adjust the set filling rate of the first pass to 30 - 35%; through the drawing die hole with a diameter of 2.8 mm in the first pass, close the mouth of the U-shaped groove to wrap the powder in it. The closing part adopts a butt joint method, and through the drawing die hole, gradually reduce the diameter by drawing in each pass until its diameter reaches 1.6 mm; between the last pass and the wire take-up reel, perform a decontamination treatment, and finally wind the obtained powder core wire into a reel to obtain a high-Ti, Al, and SiC ceramic phase composite strengthened nickel-based alloy powder core wire for electron beam melting wire additive manufacturing.

7. The preparation method of the high-Ti and Al crack-free nickel-based superalloy cored wire according to claim 6, characterized in that, The diameters of the drawing die holes include 2.8 mm, 2.6 mm, 2.4 mm, 2.2 mm, 2.0 mm, 1.9 mm, 1.8 mm, 1.7 mm, and 1.6 mm, and gradually reduce the diameter by drawing from large to small in each pass.

8. The method for additive manufacturing of nickel-based alloys with high-Ti and Al crack-free nickel-based superalloy cored wires according to any one of claims 1-5, characterized in that, Using the electron beam as the heat source, assemble the prepared nickel-based alloy powder core wire onto the wire feeder and send it to the lower beam position of the electron beam through the wire feeding nozzle, and fix the wire feeding angle and the dry extension length; Fix the additive manufacturing substrate on the workbench and close the vacuum chamber hatch; Turn on the vacuum pump to evacuate, and maintain when the vacuum degree reaches 5×10 -2 Pa. Set the electron beam additive manufacturing parameters, and print layer by layer according to the set deposition path to finally obtain the target nickel-based alloy additive component.

9. The method for additive manufacturing of nickel-based alloys according to claim 8, characterized in that, The process parameters of the electron beam melting wire additive manufacturing are: the acceleration voltage is 10 - 30 KV, the electron beam current is 30 - 50 mA, the wire feeding speed is 500 - 900 mm / min, and the movement speed is 120 - 210 mm / min; after each layer of printing is completed, use the numerical control panel to move the workbench, raise the electron gun, return to the starting position, and lower it to an appropriate height, and wait until the substrate and the deposited specimen cool to below 50 °C before proceeding with the next deposition.

10. The method for additive manufacturing of nickel-based alloys according to claim 8, wherein, The angle between the wire and the substrate is 30 - 45°, the distance between the wire and the upper surface of the substrate is 0.5 - 2 mm, and the dry extension length is 5 - 10 mm to ensure a continuous liquid bridge transition during the additive manufacturing process.

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