阅读说明：本技术 一种提高增材制造奥氏体钢力学性能的方法 (Method for improving mechanical property of additive manufactured austenitic steel ) 是由 马宗青 胡章平 杨振文 刘永长 于 2021-09-22 设计创作，主要内容包括：本发明提供了一种提高增材制造奥氏体钢力学性能的方法,将可溶性稀土氧化物盐、316L球形粉末加入无水乙醇或去离子水中,使可溶性稀土氧化物盐于溶液中,316L球形粉末完全润湿,得到固液混合物；将固液混合物进行干燥蒸发,然后煅烧还原,得到初步复合球形粉体；对初步复合球形粉体和稀土单质粉末的混合粉体进行球磨使其充分混合,得到复合球形粉体；以复合球形粉体作为原材料,通过增材制造技术对复合球形粉体层进行逐层打印使其熔化凝固,同时对每一凝固的层进行激光快速重熔以制备出稀土氧化物掺杂316L复合材料。本发明通过添加稀土氧化物来调控复合材料的微观组织从而提升材料的力学性能。(The invention provides a method for improving the mechanical property of additive manufacturing austenitic steel, which comprises the steps of adding soluble rare earth oxide salt and 316L spherical powder into absolute ethyl alcohol or deionized water, so that the soluble rare earth oxide salt is in solution, and the 316L spherical powder is completely wetted to obtain a solid-liquid mixture; drying and evaporating the solid-liquid mixture, and then calcining and reducing to obtain primary composite spherical powder; ball-milling the mixed powder of the preliminary composite spherical powder and the rare earth simple substance powder to fully mix the mixed powder to obtain composite spherical powder; the composite spherical powder is used as a raw material, the composite spherical powder layer is printed layer by layer through an additive manufacturing technology to be melted and solidified, and meanwhile, laser rapid remelting is carried out on each solidified layer to prepare the rare earth oxide doped 316L composite material. According to the invention, the microstructure of the composite material is regulated and controlled by adding the rare earth oxide, so that the mechanical property of the material is improved.)

1. A method for improving the mechanical properties of an additive manufactured austenitic steel, characterized in that the method comprises the following steps:

step S1, adding soluble rare earth oxide salt and 316L spherical powder into absolute ethyl alcohol or deionized water, and enabling the soluble rare earth oxide salt to be in solution and the 316L spherical powder to be completely wetted by ultrasonic oscillation or mechanical stirring to obtain a solid-liquid mixture;

step S2, drying and evaporating the solid-liquid mixture obtained in the step S1 to deposit rare earth oxide salt on 316L spherical particles, and then calcining the particles for 2 to 6 hours in an atmosphere containing hydrogen at the temperature of 450 to 600 ℃ to reduce the particles to obtain primary composite spherical powder in which the rare earth oxide is uniformly dispersed and wrapped on the surfaces of the 316L spherical particles;

step S3, adding rare earth simple substance powder into the primary composite spherical powder obtained in the step S2, and performing ball milling on the mixed powder of the primary composite spherical powder and the rare earth simple substance powder to fully mix the mixed powder to obtain composite spherical powder; the rare earth element of the rare earth simple substance is the same as the rare earth element in the soluble rare earth oxide salt in the step S1;

and step S4, using the composite spherical powder prepared in the step S3 as a raw material, printing the composite spherical powder layer by layer through an additive manufacturing technology to enable the composite spherical powder layer to be melted and solidified, and simultaneously carrying out laser rapid remelting on each solidified layer to prepare the rare earth oxide doped 316L composite material.

2. The method for improving the mechanical property of the austenitic steel for additive manufacturing according to claim 1, wherein the additive manufacturing technology in the step S4 is a selective laser melting technology, and the process parameters are as follows: the energy density range of the laser body is 70-200J/mm³Each layer being of thickness30-50 μm, and the lapping amount between the melting channels in each layer is 10-50%.

3. The method for improving the mechanical property of the additive manufactured austenitic steel according to the claim 1, wherein the process parameters of the laser fast remelting in the step S4 are: the energy density range of the laser body is 70-250J/mm³The scanning speed is 800-1600 mm/s.

4. The method for improving the mechanical property of the additive manufactured austenitic steel according to claim 1, wherein the soluble rare earth oxide salt in step S1 is yttrium nitrate or lanthanum nitrate; if the soluble rare earth oxide salt is yttrium nitrate, the rare earth simple substance added in the step S3 is pure yttrium; if the soluble rare earth oxide salt is lanthanum nitrate, the rare earth simple substance added in the step S3 is pure lanthanum.

5. The method for improving the mechanical property of the additive manufactured austenitic steel according to the claim 1, characterized in that, the content of the rare earth oxide in the composite spherical powder obtained in the step S3 is 0.25 wt.% to 1.0 wt.%.

6. The method for improving the mechanical property of the additive manufactured austenitic steel according to the claim 1, wherein the preliminary composite spherical powder with the nanometer size of the rare earth oxide evenly dispersed and wrapped on the surface of the 316L spherical particles is obtained in the step S2, and the size range of the rare earth oxide is 10-900 nm.

7. The method for improving the mechanical property of the additive manufactured austenitic steel according to the claim 1, wherein the atmosphere containing hydrogen in the step S2 is pure hydrogen or hydrogen argon mixture.

Technical Field

The invention belongs to the technical field of metal composite material additive manufacturing, and particularly relates to a method for improving the mechanical property of material additive manufactured austenitic steel.

Background

At present, the additive manufacturing technology is widely applied to materials such as metal, high polymer, ceramic and the like as an advanced process technology. The technique enables rapid molding of three-dimensional parts with complex shapes directly from powder without the need for time-consuming mold design processes, a "bottom-on-top" near-net-shape fabrication.

316L austenitic steel is widely used as a structural material for nuclear reactors due to its good ductility, corrosion resistance, oxidation resistance and relatively low cost. However, the low mechanical properties of 316L austenitic steels limit their application at high temperatures. Compared with 316L austenitic steel manufactured by the traditional process, 316L austenitic steel manufactured by laser additive manufacturing has higher mechanical property because of high-density microstructure such as network dislocation structure and the like. However, how to further improve the mechanical properties of the alloy on the basis of laser additive manufacturing of 316L austenitic steel still remains to be considered. One solution is to introduce stable nano-objects in the matrix to form a so-called second phase dispersion strengthened steel. For example, the Chinese patent publication No. CN110355367A discloses an additive manufacturing method of Al3Ti/316L steel composite material. The patent regulates the austenite phase region of 316L austenitic steel by adding Al3Ti, thereby forming austenite + ferrite dual phase structure steel and ferrite steel. However, Al3Ti added in this patent has a low melting point (1173 ℃) and poor thermal stability, and cannot provide excellent high-temperature performance to the material. Therefore, the addition of the oxide second-phase nanoparticles with high melting point and good thermal stability can not only improve the room temperature and high temperature performance of the material, but also absorb He bubbles generated in the irradiation process to form a He trap so as to improve the irradiation resistance of the material. For example, in the chinese patent publication No. CN111590079A, a nano-oxide dispersion strengthened steel member and a method for manufacturing the same by rapid additive manufacturing are disclosed. The patent adds Y2O3 as a nano-reinforcing phase to improve the performance of 316L austenitic steel. However, the preparation process of the patent is complicated and tedious, and comprises ball milling and mixing of yttrium oxide and 316L powder, forming and wire drawing, electric arc additive manufacturing and the like. In addition, compared with the laser additive manufacturing technology, the arc additive manufacturing technology has the disadvantages of insufficient precision of a formed part, low reuse rate of raw material powder and the like.

Based on the defects, the high-performance nano rare earth oxide doped 316L forming piece is prepared by adopting the selective laser melting technology with high forming precision. The proposal of the patent provides a feasible method for manufacturing high-performance ODS steel in an additive mode.

Disclosure of Invention

In order to solve the technical problems, the invention provides a method for improving the mechanical property of the additive manufacturing austenitic steel, and the mechanical property of the material is improved by adding the rare earth oxide to regulate and control the microstructure of the composite material under the condition of ensuring that the prepared composite material has no obvious defects by using the additive manufacturing technology.

In order to achieve the purpose, the technical scheme adopted by the invention is as follows:

the invention provides a method for improving the mechanical property of additive manufacturing austenitic steel, which comprises the following steps:

step S1, adding soluble rare earth oxide salt and 316L spherical powder into absolute ethyl alcohol or deionized water, and enabling the soluble rare earth oxide salt to be in solution and the 316L spherical powder to be completely wetted by ultrasonic oscillation or mechanical stirring to obtain a solid-liquid mixture;

step S2, drying and evaporating the solid-liquid mixture obtained in the step S1 to deposit rare earth oxide salt on 316L spherical particles, and then calcining the particles for 2 to 6 hours in an atmosphere containing hydrogen at the temperature of 450 to 600 ℃ to reduce the particles to obtain primary composite spherical powder in which the rare earth oxide is uniformly dispersed and wrapped on the surfaces of the 316L spherical particles;

step S3, adding rare earth simple substance powder into the primary composite spherical powder obtained in the step S2, and performing ball milling on the mixed powder of the primary composite spherical powder and the rare earth simple substance powder to fully mix the mixed powder to obtain composite spherical powder; the rare earth element of the rare earth simple substance is the same as the rare earth element in the soluble rare earth oxide salt in the step S1;

and step S4, using the composite spherical powder prepared in the step S3 as a raw material, printing the composite spherical powder layer by layer through an additive manufacturing technology to enable the composite spherical powder layer to be melted and solidified, and simultaneously carrying out laser rapid remelting on each solidified layer to prepare the rare earth oxide doped 316L composite material.

Preferably, the additive manufacturing technology in step S4 is a selective laser melting technology, and the process parameters thereof are as follows: the energy density range of the laser body is 70-200J/mm³The thickness of each layer is 30-50 μm, and the lapping amount between the melting channels in each layer is 10-50%.

Preferably, the laser rapid remelting process parameters in step S4 are as follows: the energy density range of the laser body is 70-250J/mm³The scanning speed is 800-1600 mm/s.

Preferably, the soluble rare earth oxide salt in step S1 is yttrium nitrate or lanthanum nitrate; if the soluble rare earth oxide salt is yttrium nitrate, the rare earth simple substance added in the step S3 is pure yttrium; if the soluble rare earth oxide salt is lanthanum nitrate, the rare earth simple substance added in the step S3 is pure lanthanum.

Preferably, the content of the rare earth oxide in the composite spherical powder obtained in step S3 is 0.25 wt.% to 1.0 wt.%.

Preferably, the preliminary composite spherical powder in which the nano-sized rare earth oxide is uniformly dispersed and coated on the surface of the 316L spherical particles is obtained in step S2, wherein the size range of the rare earth oxide is 10-900 nm.

Preferably, the atmosphere containing hydrogen in step S2 is pure hydrogen or a mixture of hydrogen and argon.

The invention has the following beneficial effects:

according to the method for improving the mechanical property of the additive manufactured austenitic steel, provided by the invention, the mechanical property of the material is improved by adding the rare earth oxide to regulate and control the microstructure of the composite material under the condition of ensuring that the prepared composite material has no obvious defect by using an additive manufacturing technology.

1. The method utilizes two methods to add rare earth oxide and rare earth simple substance in turn. The first added rare earth oxide is based on physical deposition, reduction and nucleation mechanisms, so that the rare earth oxide can be tightly coated on the austenite steel spherical powder on the basis of keeping the nanometer size, and the sphericity can be kept. And secondly, rare earth simple substances are mixed with the initial composite powder through ball milling, so that not only can oxygen atoms in the process of adding the rare earth oxide be adsorbed, but also oxygen atoms in the printing process can be adsorbed. The added rare earth simple substance forms rare earth oxide in the adsorption process, so that printing defects such as holes, cracks and the like caused by oxidation of the 316L composite material doped with the rare earth oxide are avoided, and the mechanical property of a printed piece is ensured. By the method for adding the rare earth oxide and the rare earth substance in two steps, material defects caused by the existence of oxygen atoms in the method for adding the rare earth oxide can be reduced, and the cost can be saved compared with the method for adding the rare earth simple substance.

2. Compared with the method without adopting a rapid laser remelting technology, the method creatively provides a rapid laser remelting means. The rapid laser remelting can utilize the Marangoni convection effect to crush and redistribute the agglomerated rare earth oxide to eliminate the agglomeration of the rare earth oxide, so that the rare earth oxide can be dispersed and distributed in 316L to play a dispersion strengthening effect to enhance the mechanical property of a printed piece.

3. Compared with 316L without the rare earth oxide, the added rare earth oxide can refine the cellular subgrain size of the composite material through the Zener pinning effect, so that the material has a fine-grain strengthening effect and the mechanical property of the material is improved.

4. The rare earth oxide and 316L composite powder prepared by the invention has low preparation cost and high efficiency under the condition of completely meeting the requirements of additive manufacturing processes, and does not need to add other additives and process control agents. In addition, the invention can design and prepare composite powder with different rare earth oxide contents to perform additive manufacturing on printed parts meeting different service conditions.

5. The strength of the samples with the rare earth oxide added was improved compared to pure 316L. The nanometer rare earth oxide in the composite material has fine size and is dispersed and distributed. This demonstrates that it is feasible to enhance the performance of rare earth oxide and 316L composites by additive manufacturing techniques. The method makes up the defects of component segregation and difficulty in preparing large and complex components in the traditional powder metallurgy method.

Drawings

In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings used in the description of the embodiments will be briefly introduced below, and it is apparent that the drawings in the following description are only some embodiments of the present invention.

FIG. 1 is a photograph of pure 316L powder;

FIG. 2 is 316L-1.0 wt.% Y₂O₃A picture of the composite powder;

fig. 3 is a scanning electron micrograph of the microstructure of (a) a 316L sample of additive manufacturing and (b) a mechanical property map of comparative example 1;

FIG. 4 is the additive manufacturing 0.25 wt.% Y of example 1 (a)₂O₃-a scanning electron micrograph of the microstructure of the 316L sample and (b) a mechanical property map;

FIG. 5 is the additive manufacturing 1.0 wt.% Y of example 2 (a)₂O₃-a scanning electron micrograph of the microstructure of the 316L sample and (b) a mechanical property map;

FIG. 6 is the additive manufacturing 1.0 wt.% La of example 3(a)₂O₃-a scanning electron micrograph of the microstructure of the 316L sample and (b) a mechanical properties map.

Detailed Description

In order to make the technical solutions of the present invention better understood, the present invention will be described in detail below with reference to the accompanying drawings and specific embodiments.

The invention provides a method for improving the mechanical property of additive manufacturing austenitic steel, which comprises the following steps:

step S1, adding soluble rare earth oxide salt and 316L spherical powder into absolute ethyl alcohol or deionized water, and enabling the soluble rare earth oxide salt to be in solution and the 316L spherical powder to be completely wetted by ultrasonic oscillation or mechanical stirring to obtain a solid-liquid mixture; the particle size range of the 316L spherical powder is 15-150 mu m; the soluble rare earth oxide salt is yttrium nitrate or lanthanum nitrate.

Step S2, drying and evaporating the solid-liquid mixture obtained in the step S1 to deposit rare earth oxide salt on 316L spherical particles, and then calcining the particles for 2 to 6 hours in an atmosphere containing hydrogen at the temperature of 450 to 600 ℃ to reduce the particles to obtain primary composite spherical powder in which nano-sized rare earth oxide is uniformly dispersed and wrapped on the surfaces of the 316L spherical particles; the size range of the rare earth oxide is 10-900 nm.

Step S3, adding rare earth elementary substance powder into the primary composite spherical powder obtained in the step S2, and performing ball milling on the mixed powder of the primary composite spherical powder and the rare earth elementary substance powder to fully mix the mixed powder to obtain composite spherical powder, wherein the content of rare earth oxide in the composite spherical powder is 0.25 wt.% to 1.0 wt.%; the rare earth element of the rare earth simple substance is the same as the rare earth element in the soluble rare earth oxide salt in the step S1; if the soluble rare earth oxide salt is yttrium nitrate, the rare earth simple substance is pure yttrium; if the soluble rare earth oxide salt is lanthanum nitrate, the rare earth simple substance is pure lanthanum.

And S4, taking the composite spherical powder prepared in the step S3 as a raw material, printing the layers of the composite spherical powder layer by layer through an additive manufacturing technology to melt and solidify the layers, and simultaneously carrying out laser rapid remelting on each solidified layer to prepare the rare earth oxide doped 316L composite material, wherein the rare earth oxide doped 316L composite material is crack-free and defect-free, has a density of over 99.5 percent and has a cellular sub-crystalline structure at a nanometer level. The additive manufacturing technology is a selective laser melting technology, and the technological parameters are as follows: the energy density range of the laser body is 70-200J/mm³The thickness of each layer is 30-50 μm, and the lapping amount between the melting channels in each layer is 10-50%. The laser rapid remelting process parameters are as follows: the energy density range of the laser body is 70-250J/mm³The scanning speed is 800-1600 mm/s.

Comparative example 1

Pure 316L material was prepared using Selective Laser Melting (SLM) using a physical energy density of 100J/mm³The thickness of the printing layer is 30 mu m, the lapping amount between the melting channels is 30 percent, the size of the printing sample meets the size requirement of a standard tensile sample, and the density is more than 99.5 percent. FIG. 1 is a pure 316L spherical powder with a particle size in the range of 15-150 μm. When the microstructure of the 316L sample was observed by a Scanning Electron Microscope (SEM), as shown in FIG. 3(a), it was found that the cellular subgrain size was 470 nm. The sample was subjected to a tensile breaking mechanical property test, and the ultimate tensile strength was 707MPa, as shown in FIG. 3 (b).

Example 1

Adding 23.53g of yttrium nitrate hexahydrate and 5000g of 316L spherical powder into a proper amount of absolute ethyl alcohol, completely dissolving yttrium nitrate hexahydrate in absolute ethyl alcohol through mechanical stirring, completely wetting 316L spherical powder in absolute ethyl alcohol to obtain a solid-liquid mixture, drying the solid-liquid mixture, reducing for 6 hours in a hydrogen atmosphere at 450 ℃ to obtain primary composite spherical powder, adding 5g of pure yttrium powder into the primary composite spherical powder, and performing ball milling on the pure yttrium powder and the primary composite spherical powder to fully mix the pure yttrium powder and the primary composite spherical powder to prepare the composite spherical powder for additive manufacturing. The prepared composite spherical powder is used as printing precursor powder, and a Selective Laser Melting (SLM) technology is adopted to prepare 0.25 wt.% Y₂O₃316L doped composite material, using an energy density of 70J/mm³The thickness of the printing layer is 50 μm, the lapping amount between the melting channels is 50%, and the energy density range of laser rapid remelting is 70J/mm³The scanning speed was 800 mm/s. The size of a printed sample meets the size requirement of a standard tensile sample, and the density is more than 99.5%. Observation of 0.25 wt.% Y by Scanning Electron Microscope (SEM)₂O₃The microstructure of the doped 316L sample, as shown in FIG. 4(a), can be seen to have a cellular subgrain size of 380 nm. The sample was subjected to a tensile breaking mechanical property test, and the ultimate tensile strength was 742MPa, as shown in FIG. 4 (b). By comparing the ultimate tensile strength and shape of the pure 316L sample of comparative example 1, it was found that the ultimate tensile strength and shape of the doped sample was higher than that of the pure 316L sample of comparative example 1Pure 316L sample.

Example 2

170.57g of yttrium nitrate hexahydrate and 6000g of 316L spherical powder are added into a proper amount of absolute ethyl alcohol, the yttrium nitrate hexahydrate is completely dissolved in the absolute ethyl alcohol through ultrasonic oscillation, the 316L spherical powder is completely wetted in the absolute ethyl alcohol to obtain a solid-liquid mixture, the solid-liquid mixture is dried, then the solid-liquid mixture is reduced for 2 hours in a hydrogen atmosphere at 600 ℃ to obtain primary composite spherical powder, 10g of pure yttrium powder is added into the primary composite spherical powder, and the pure yttrium powder and the primary composite spherical powder are subjected to ball milling to be fully mixed, so that the composite spherical powder for additive manufacturing is prepared. The prepared composite spherical powder is used as printing precursor powder, and a Selective Laser Melting (SLM) technology is adopted to prepare 1.0 wt.% of Y₂O₃316L doped composite material, using an energy density of 200J/mm³The thickness of the printing layer is 50 μm, the lapping amount between the melting channels is 10%, and the energy density range of the laser rapid remelting is 250J/mm³The scanning speed was 1600 mm/s. The size of a printed sample meets the size requirement of a standard tensile sample, and the density is more than 99.5%. FIG. 2 is 1.0 wt.% Y₂O₃The particle size of the 316L-coated spherical powder was in the range of 15 to 150 μm, and it was found that yttrium oxide was completely coated on the surface of the 316L-coated spherical powder. Observation of 1.0 wt.% Y by Scanning Electron Microscope (SEM)₂O₃The microstructure of the doped 316L sample, as shown in FIG. 5(a), can be seen to have a cellular subgrain size of 260 nm. The sample was subjected to a tensile breaking mechanical property test, and the ultimate tensile strength was 731MPa, as shown in FIG. 5 (b). By comparing the mechanical properties of the pure 316L sample of comparative example 1, it was found that the ultimate tensile strength of the doped sample was higher than that of the pure 316L sample.

Example 3

785.84g of lanthanum nitrate hexahydrate and 6000g of 316L spherical powder are added into a proper amount of deionized water, the lanthanum nitrate hexahydrate is completely dissolved in the deionized water through mechanical stirring, the 316L spherical powder is completely wetted in the deionized water to obtain a solid-liquid mixture, the solid-liquid mixture is dried, and then the solid-liquid mixture is reduced for 4 hours in a hydrogen atmosphere at 500 ℃ to obtain primary composite spherical powderAdding 20g of pure lanthanum powder into the primary composite spherical powder, and performing ball milling on the pure lanthanum powder and the primary composite spherical powder to fully mix the pure lanthanum powder and the primary composite spherical powder so as to prepare the composite spherical powder for additive manufacturing. The prepared composite spherical powder is used as printing precursor powder, and a Selective Laser Melting (SLM) technology is adopted to prepare 1.0 wt.% of La₂O₃316L doped composite material, using an energy density of 150J/mm³The thickness of the printing layer is 40 μm, the lapping amount between the melting channels is 20%, and the energy density range of laser rapid remelting is 200J/mm³The scanning speed was 1200 mm/s. The size of a printed sample meets the size requirement of a standard tensile sample, and the density is more than 99.5%. Observation of 1.0 wt.% La by Scanning Electron Microscope (SEM)₂O₃The microstructure of the doped 316L, as shown in FIG. 6(a), can be seen to have a cellular subgrain size of 280 nm. The sample was subjected to a tensile breaking mechanical property test, and the ultimate tensile strength was 765MPa, as shown in FIG. 6 (b). The ultimate tensile strength of the doped sample was found to be higher than that of the pure 316L sample by comparison with that of the pure 316L sample of comparative example 1.

According to the technical scheme, the method for improving the mechanical property of the additive manufactured austenitic steel is provided, and the mechanical property of the material is improved by adding the rare earth oxide to regulate and control the microstructure of the composite material under the condition that the additive manufacturing technology ensures that the prepared composite material has no obvious defects.

1. The rare earth oxide and the rare earth simple substance are added in sequence by two methods proposed in the embodiment. The first added rare earth oxide is based on physical deposition, reduction and nucleation mechanisms, so that the rare earth oxide can be tightly coated on the austenite steel spherical powder on the basis of keeping the nanometer size, and the sphericity can be kept. And secondly, rare earth simple substances are mixed with the initial composite powder through ball milling, so that not only can oxygen atoms in the process of adding the rare earth oxide be adsorbed, but also oxygen atoms in the printing process can be adsorbed. The added rare earth simple substance forms rare earth oxide in the adsorption process, so that printing defects such as holes, cracks and the like caused by oxidation of the 316L composite material doped with the rare earth oxide are avoided, and the mechanical property of a printed piece is ensured. By the method for adding the rare earth oxide and the rare earth substance in two steps, material defects caused by the existence of oxygen atoms in the method for adding the rare earth oxide can be reduced, and the cost can be saved compared with the method for adding the rare earth simple substance.

2. Compared with the method without adopting a rapid laser remelting technology, the method creatively provides a rapid laser remelting means. The rapid laser remelting can utilize the Marangoni convection effect to crush and redistribute the agglomerated rare earth oxide to eliminate the agglomeration of the rare earth oxide, so that the rare earth oxide can be dispersed and distributed in 316L to play a dispersion strengthening effect to enhance the mechanical property of a printed piece.

3. Compared with 316L without the rare earth oxide, the added rare earth oxide can refine the cellular subgrain size of the composite material through the Zener pinning effect, so that the material has a fine-grain strengthening effect and the mechanical property of the material is improved.

4. The composite powder of rare earth oxide and 316L prepared by the embodiment has low preparation cost and high efficiency under the condition of completely meeting the requirements of additive manufacturing processes, and does not need to add other additives and process control agents. In addition, the embodiment can design and prepare composite powders with different rare earth oxide contents to additively manufacture printed products meeting different service conditions.

5. The strength of the samples with the rare earth oxide added was improved compared to pure 316L. The nanometer rare earth oxide in the composite material has fine size and is dispersed and distributed. This demonstrates that it is feasible to enhance the performance of rare earth oxide and 316L composites by additive manufacturing techniques. The method makes up the defects of component segregation and difficulty in preparing large and complex components in the traditional powder metallurgy method.

The embodiments of the present invention have been described in detail through the embodiments, but the description is only exemplary of the embodiments of the present invention and should not be construed as limiting the scope of the embodiments of the present invention. The scope of protection of the embodiments of the invention is defined by the claims. In the present invention, the technical solutions described in the embodiments of the present invention or those skilled in the art, based on the teachings of the embodiments of the present invention, design similar technical solutions to achieve the above technical effects within the spirit and the protection scope of the embodiments of the present invention, or equivalent changes and modifications made to the application scope, etc., should still fall within the protection scope covered by the patent of the embodiments of the present invention.