An ultra-high strength steel powder for additive manufacturing, an additively manufactured component and a method of manufacturing the same

Abstract

This invention provides an ultra-high strength steel powder for additive manufacturing, additive components, and a method for preparing the same, relating to the field of metal additive manufacturing technology. The ultra-high strength steel powder for additive manufacturing provided by this invention uses Fe as a matrix. By precisely controlling the content of elements such as Cr, Ni, C, Si, Mn, S, P, Mg, Cu, Sn, Ce, La, Mo, Ti, Al, V, W, Co, Zn, Pb, and B, the components manufactured using this steel powder possess both high strength and excellent ductility.

Description

Technical Field

[0001] This invention relates to the field of metal additive manufacturing technology, and more specifically, to an ultra-high strength steel powder for additive manufacturing, additive components, and a method for preparing the same. Background Technology

[0002] Additive manufacturing, as a core process of high-end intelligent manufacturing, has been widely applied in aerospace, high-end equipment manufacturing, automotive industry, and mold processing due to its advantages such as high degree of freedom in forming, high material utilization, and the ability to prepare complex structural components. However, as various industries continue to increase their requirements for lightweight, high load-bearing capacity, impact resistance, and brittle fracture prevention in high-end components, stringent standards have been set for the comprehensive mechanical properties of steel powder used in additive manufacturing. The resulting components must possess both ultra-high strength and excellent ductility to meet the demands of extreme working conditions. However, most steel powders currently used in additive manufacturing are powders prepared for conventional processes such as casting. Components manufactured using these steel powders often struggle to achieve both high strength and good ductility. Therefore, obtaining components with both high strength and good ductility using steel powder additive manufacturing has become a pressing issue that needs to be addressed. Summary of the Invention

[0003] The problem solved by this invention is: how to obtain components with both high strength and good ductility when using steel powder additive manufacturing.

[0004] To address the aforementioned problems, this invention provides an ultra-high strength steel powder for additive manufacturing, comprising, by mass percentage: Cr: 17% to 19%, Ni: 5% to 6%, C: 0.01% to 0.1%, Si: 1% to 2%, Mn: 1% to 2%, S: 0.005% to 0.02%, P: 0.01% to 0.03%, Mg: 0.005% to 0.01%, Cu: 0.02% to 0.03%, Sn: 0.001% to 0.01%, Ce: 0.00% to 0.01%. 5% to 0.02%, La: 0.001% to 0.003%, Mo: 0.56% to 0.59%, Ti: 0.001% to 0.01%, Al: 0.001% to 0.01%, V: 0.05% to 0.07%, W: 0.03% to 0.07%, Co: 0.06% to 0.07%, Zn: 0.003% to 0.005%, Pb: 0.001% to 0.003%, B: 0.17% to 0.19%, balance Fe and unavoidable impurities.

[0005] Optionally, the particle size of the ultra-high strength steel powder used for additive manufacturing is from 15 μm to 45 μm.

[0006] The present invention also provides a method for preparing ultra-high strength steel powder for additive manufacturing as described above, comprising: Step S1: Vacuum melt the raw materials to obtain molten steel; Step S2: The molten steel is atomized to produce steel powder.

[0007] Optionally, in step S1, the temperature of the vacuum melting is 1580°C to 1620°C, and the time is 2 hours to 4 hours.

[0008] Optionally, in step S2, the atomizing gas used in the gas atomization powder preparation process is argon.

[0009] Optionally, in step S2, the pressure of the atomizing gas is 3.5 MPa to 5.0 MPa.

[0010] The present invention also provides an additive component, which is made from ultra-high strength steel powder used for additive manufacturing as described above.

[0011] The present invention also provides a method for preparing the additive component as described above, comprising: melting and molding ultra-high strength steel powder for additive manufacturing layer by layer using laser directional energy deposition to obtain the additive component.

[0012] Optionally, the power of the laser used in the layer-by-layer melting and forming process is 1900W to 2100W, and the frequency is 95000Hz to 105000Hz.

[0013] Optionally, the scanning speed of the laser used in the layer-by-layer melting and forming process is 10 mm / s to 20 mm / s.

[0014] Compared with related technologies, the additive manufacturing steel powder provided by this invention uses Fe as the matrix and constructs a synergistic mechanism between Cr and Ni by precisely controlling the content ratio of Cr and Ni. This allows the steel powder to form a dual-phase structure of austenite and ferrite at room temperature after additive manufacturing. The ferrite phase significantly improves the yield strength of the component, providing initial load-bearing capacity, while the austenite phase undergoes martensitic transformation during tensile deformation, thereby improving the tensile strength of the component. Simultaneously, the trace addition of La and Ce not only purifies grain boundaries, improves inclusion morphology, and reduces stress concentration, but also effectively lowers the Md temperature, allowing the martensitic transformation to occur slowly and continuously during tensile deformation. This enhances both the work hardening ability of the material and the ductility of the component. Si has extremely low solubility in carbides, which can inhibit carbon precipitation in the early stages of strain, forcing C atoms to remain in austenite. This ensures sufficient stability of austenite, with phase transformation only occurring at higher strains. This allows the TRIP effect to persist throughout the entire tensile process, continuously strengthening the component's performance. Trace amounts of boron (B) are retained in the metal matrix in large quantities, forming a supersaturated solid solution, due to the rapid solidification characteristics of additive manufacturing. This results in significant solid solution strengthening, which is beneficial for further improving the strength of the component. Elements such as v (V), w (W), and co (Co) achieve dispersion strengthening by forming dispersed second-phase particles. The addition of Mg (Mg) removes sulfur (S) and oxygen (O) to form fine, dispersed complexes, purifying the matrix structure. It also stabilizes the metal vapor pressure during additive manufacturing, reducing spatter and porosity defects. Trace segregation of elements such as copper (Cu) and snake (Sn) at grain boundaries inhibits crack propagation. Elements such as zirconium (Zn) and phosphorus (Pb) further enhance the component's strength through solid solution strengthening. In summary, components manufactured using the steel powder additive manufacturing method provided by this invention possess both high strength and excellent ductility. Attached Figure Description

[0015] Figure 1 This is a comparison of the XRD curves of the additive component obtained in Embodiment 1 of the present invention before and after tensile deformation; Figure 2 The image shows the metallographic structure of the additive component obtained in Embodiment 1 of the present invention before tensile deformation. Figure 3 This is a metallographic image of the additive component obtained in Embodiment 1 of the present invention after tensile deformation. Detailed Implementation

[0016] To make the above-mentioned objects, features, and advantages of the present invention more apparent and understandable, specific embodiments of the present invention will be described in detail below with reference to the accompanying drawings. Although some embodiments of the present invention are shown in the drawings, it should be understood that the present invention can be implemented in various forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided to provide a more thorough and complete understanding of the present invention. It should be understood that the accompanying drawings and embodiments of the present invention are for illustrative purposes only and are not intended to limit the scope of protection of the present invention.

[0017] Unless otherwise defined, all technical and scientific terms used in this invention have the same meaning as commonly understood by one of ordinary skill in the art to which this invention pertains. The terminology used in this specification is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention.

[0018] The term "comprising" and its variations as used herein are open-ended, meaning "including but not limited to"; the term "based on" means "at least partially based on"; the term "one embodiment" means "at least one embodiment"; the term "another embodiment" means "at least one additional embodiment"; the term "some embodiments" means "at least some embodiments"; and the term "optionally" means "optional embodiments". Definitions of other terms will be given in the following description. It should be noted that the concepts of "first," "second," etc., mentioned in this invention are used to distinguish different objects, not to describe a specific order or hierarchy. Furthermore, the terms "first" and "second" are used for descriptive purposes only and should not be construed as indicating or implying relative importance or implicitly specifying the number of indicated technical features. Thus, a feature defined with "first" or "second" may explicitly or implicitly include one or more of that feature. In the description of this invention, unless otherwise stated, "a plurality of" means two or more.

[0019] This invention provides an ultra-high strength steel powder for additive manufacturing, comprising, by mass percentage: Cr: 17% to 19%, Ni: 5% to 6%, C: 0.01% to 0.1%, Si: 1% to 2%, Mn: 1% to 2%, S: 0.005% to 0.02%, P: 0.01% to 0.03%, Mg: 0.005% to 0.01%. Cu: 0.02% to 0.03%, Sn: 0.001% to 0.01%, Ce: 0.005% to 0.02%, La: 0.001% to 0.003%, Mo: 0.56% to 0.59%, Ti: 0.001% to 0.01%, Al: 0.001% to 0.01%, V: 0.05% to 0.07%, W: 0.03% to 0.07%, Co: 0.06% to 0.07%, Zn: 0.003% to 0.005%, Pb: 0.001% to 0.003%, B: 0.17% to 0.19%, balance Fe and unavoidable impurities.

[0020] The additive manufacturing steel powder provided in this invention uses Fe as the matrix. By precisely controlling the content ratio of Cr and Ni, a synergistic mechanism between the two is constructed, enabling the additively manufactured components to form a dual-phase structure of austenite and ferrite at room temperature. The ferrite phase significantly improves the yield strength of the component, providing initial load-bearing capacity, while the austenite phase undergoes martensitic transformation during tensile deformation, thereby increasing the tensile strength of the component. Simultaneously, the trace addition of La and Ce not only purifies grain boundaries, improves inclusion morphology, and reduces stress concentration, but also effectively lowers the Md temperature, allowing the martensitic transformation to occur slowly and continuously during tensile deformation. This enhances both the work hardening ability of the material and the ductility of the component. Si has extremely low solubility in carbides, inhibiting carbon precipitation in the early stages of strain and forcing C atoms to remain in austenite, ensuring sufficient stability of the austenite. Phase transformation only occurs at higher strains, allowing the TRIP effect to persist throughout the tensile process and continuously strengthen the component's performance. Trace amounts of boron (B) are retained in the metal matrix in large quantities, forming a supersaturated solid solution, due to the rapid solidification characteristics of additive manufacturing. This results in significant solid solution strengthening, which is beneficial for further improving the strength of the component. Elements such as v (V), w (W), and co (Co) achieve dispersion strengthening by forming dispersed second-phase particles. The addition of Mg (Mg) removes sulfur (S) and oxygen (O) to form fine, dispersed complexes, purifying the matrix structure. It also stabilizes the metal vapor pressure during additive manufacturing, reducing spatter and porosity defects. Trace segregation of elements such as copper (Cu) and snake (Sn) at grain boundaries inhibits crack propagation. Elements such as zirconium (Zn) and phosphorus (Pb) further enhance the component's strength through solid solution strengthening. In summary, the components manufactured using steel powder additive manufacturing according to the embodiments of this invention possess both high strength and excellent ductility.

[0021] The steel powder provided in this embodiment of the invention has a chemical composition designed based on the following: As a core alloying element in steel, Cr forms a continuous solid solution with iron, reducing the austenite phase region and enhancing the matrix strength through solid solution strengthening. On the other hand, it combines with carbon to form M... 23 C6-type carbides, through precipitation strengthening, further enhance the material's hardness and wear resistance. Simultaneously, the high Cr content forms a dense passivation film on the component surface, significantly improving corrosion resistance and oxidation resistance. In this embodiment of the invention, the Cr content is set at 17% to 19%, ensuring the integrity of the passivation film and avoiding a decrease in corrosion resistance due to insufficient Cr content, while also avoiding problems such as a sharp decrease in impact toughness caused by excessively high Cr content. This approach suits the balanced requirements of additive manufacturing for material strength and toughness.

[0022] Ni, as an austenite stabilizing element, synergistically regulates the phase transformation behavior of steel with Cr, enabling the formation of an austenite-ferrite dual-phase microstructure in the component at room temperature. Ferrite provides the initial yield strength of the component, while austenite triggers the TRIP effect during tensile deformation, continuously strengthening the tensile strength through deformation-induced martensitic transformation. In this embodiment of the invention, the Ni content is determined to be 5% to 6%, which stabilizes the austenite microstructure, inhibits the precipitation of brittle phases, and controls the alloy cost. Unlike traditional high-Ni austenitic stainless steels, this invention achieves a balance between cost-effectiveness and performance.

[0023] Carbon (C) is a key element for strengthening steel, achieving precipitation strengthening through carbide formation and simultaneously improving austenite stability. This invention employs a low-carbon design of 0.01% to 0.1%, ensuring sufficient strengthening while avoiding problems such as excessive carbide coarsening and grain boundary embrittlement caused by high carbon content.

[0024] Si strengthens the ferrite matrix, improving the overall strength and oxidation resistance of the material. Because Si has extremely low solubility in carbides, it inhibits carbon precipitation in the early stages of strain, forcing C atoms to remain in austenite. This ensures sufficient stability of the austenite, with phase transformation occurring only at higher strains. This allows the TRIP effect to continue throughout the tensile process, continuously strengthening the material's properties. In this embodiment of the invention, the Si content is set at 1% to 2%, ensuring both the strengthening effect and avoiding the decrease in plasticity caused by excessively high Si content.

[0025] Mn can assist Ni in stabilizing the austenite structure and expanding the austenite phase region, while also combining with S to form spherical manganese sulfide. In this embodiment of the invention, the Mn content is determined to be 1% to 2%, which improves the material's machinability and reduces the tendency to crack during additive manufacturing without significantly reducing toughness.

[0026] Boron (B) utilizes the rapid solidification characteristics of additive manufacturing to remain in the metal matrix in large quantities, forming a supersaturated solid solution and producing a significant solid solution strengthening effect. Simultaneously, it refines grain size, improves hardenability, and reduces hot cracking defects during additive manufacturing. In this embodiment of the invention, the B content is determined to be between 0.17% and 0.19%, precisely controlling the degree of solid solution strengthening and avoiding increased brittleness caused by excessive B.

[0027] As a strong carbide-forming element, vanadium (V) combines with carbon atoms in steel to form fine, dispersed VC-type carbides. These nanoscale particles effectively hinder dislocation movement, significantly improving the strength and hardness of the material through precipitation strengthening. In this embodiment of the invention, the V content is set to 0.05% to 0.07%, ensuring the formation of a sufficient number of VC particles while avoiding carbide coarsening due to excessive V content, thereby achieving a balance between strength and toughness in additively manufactured components.

[0028] W combines with C to form WC or M6C type carbides. These carbides have high hardness and good stability, which can significantly improve the wear resistance and high-temperature strength of the material. In the embodiments of the present invention, the W content is determined to be 0.03% to 0.07%, which ensures the formation of sufficient reinforcing phase without increasing the brittleness of the material due to excessive W content.

[0029] Co, as a transition metal, can be dissolved in a ferrite matrix, thereby enhancing the high-temperature strength and wear resistance of the material through solid solution strengthening. In this embodiment of the invention, the Co content is determined to be 0.06% to 0.07%, which strengthens the matrix without inducing the precipitation of brittle phases.

[0030] Ti is a key element for grain refinement and toughness improvement. It can form fine TiC particles with C. These particles can act as heterogeneous nucleation sites during the rapid solidification process of additive manufacturing, inhibiting excessive austenite grain growth, thereby refining the grains and improving toughness. In this embodiment of the invention, the Ti content is set to 0.001% to 0.01%, which ensures the formation of sufficient TiC particles while avoiding carbide coarsening or the formation of brittle phases due to excessive Ti content.

[0031] Ce, as a rare earth element, possesses extremely strong surface activity. It preferentially segregates at grain boundaries and phase interfaces, purifying harmful impurities at grain boundaries, improving inclusion morphology, reducing stress concentration, and enhancing the toughness and crack propagation resistance of materials. In this embodiment of the invention, the Ce content is determined to be 0.005% to 0.02%, which can effectively reduce the Md temperature, allowing deformation-induced martensitic transformation to occur slowly and continuously during tensile deformation, enhancing work hardening ability, and simultaneously improving the ductility of the component.

[0032] As a rare earth element, La works synergistically with Ce to further purify grain boundaries, improve inclusion morphology, and enhance the toughness and corrosion resistance of materials. In this embodiment of the invention, the La content is set at 0.001% to 0.003%, which can assist Ce in its function without causing brittleness problems due to excessively high La content.

[0033] Sulfur (S) is a common impurity element in steel. Excessive sulfur can easily lead to grain boundary embrittlement and increase the tendency of components to crack. Therefore, its content must be strictly controlled within a low range. In this embodiment of the invention, the sulfur content is determined to be 0.005% to 0.02%.

[0034] Phosphorus (P) is a typical harmful impurity element in steel, which easily segregates at grain boundaries, causing grain boundary embrittlement and significantly reducing the impact toughness and plasticity of the material. In this invention, the P content is strictly controlled within a low range of 0.01% to 0.03%, effectively avoiding excessive enrichment of P at grain boundaries and reducing the possibility of stress concentration and crack propagation.

[0035] In steel, Cu can accumulate at grain boundaries through trace segregation, forming a "grain boundary strengthening layer" that inhibits crack propagation at grain boundaries, thereby improving the material's toughness. In this embodiment of the invention, the Cu content is set to 0.02% to 0.03%, which effectively strengthens the grain boundaries without causing hot brittleness due to excessive Cu content.

[0036] Sn, as a trace element, can undergo slight segregation at grain boundaries, filling defects at the grain boundaries and hindering crack initiation and propagation, thereby improving the toughness of the material. In this embodiment of the invention, the Sn content is determined to be 0.001% to 0.01%, which can both assist Cu in strengthening grain boundaries and prevent grain boundary embrittlement caused by excessive Sn.

[0037] Zn can strengthen the material by distorting the matrix lattice and hindering dislocation movement through solid solution. In this embodiment of the invention, the Zn content is controlled between 0.003% and 0.005%, which effectively utilizes the auxiliary effect of solid solution strengthening while strictly avoiding the brittleness problem caused by excessive Zn.

[0038] When phosphorus (Pb) dissolves in the steel matrix, it produces a solid solution strengthening effect, which helps to improve the strength of the material. In this embodiment of the invention, the Pb content is set to 0.001% to 0.003%, which avoids the brittleness and environmental risks caused by excessive Pb, and can further improve the strength of the component through solid solution strengthening and other strengthening mechanisms.

[0039] In some embodiments of the present invention, preferably, the particle size of the ultra-high strength steel powder used for additive manufacturing is 15 μm to 45 μm.

[0040] This invention also provides a method for preparing ultra-high strength steel powder for additive manufacturing as described above, comprising: Step S1: Vacuum melt the raw materials to obtain molten steel; Step S2: The molten steel is atomized to produce steel powder.

[0041] In some embodiments of the present invention, in step S1, the temperature of the vacuum melting is 1580°C to 1620°C, and the time is 2 hours to 4 hours.

[0042] In some embodiments of the present invention, in step S2, the atomizing gas used in the gas atomization powder preparation process is argon.

[0043] In some embodiments of the present invention, in step S2, the pressure of the atomizing gas is 3.5 MPa to 5.0 MPa.

[0044] This invention also provides an additive component, which is made from ultra-high strength steel powder used for additive manufacturing as described above.

[0045] The present invention also provides a method for preparing the additive component as described above, comprising: melting and forming ultra-high strength steel powder for additive manufacturing layer by layer using laser directional energy deposition to obtain the additive component.

[0046] In some embodiments of the present invention, the power of the laser used in the layer-by-layer melting and forming process is 1900W to 2100W, and the frequency is 95000Hz to 105000Hz.

[0047] In some embodiments of the present invention, the scanning speed of the laser used in the layer-by-layer melting and forming process is 10 mm / s to 20 mm / s.

[0048] The present invention will be further described below with reference to specific embodiments.

[0049] Example 1 Additive components are obtained by melting steel powder layer by layer using laser-directed energy deposition (LDED). The steel powder, by mass percentage, comprises: Cr: 18%, Ni: 5.5%, C: 0.05%, Si: 1.5%, Mn: 1.5%, S: 0.012%, P: 0.02%, Mg: 0.008%, Cu: 0.025%, Sn: 0.005%, Ce: 0.012%, La: 0.002%, Mo: 0.57%, Ti: 0.005%, Al: 0.005%, V: 0.06%, W: 0.05%, Co: 0.065%, Zn: 0.004%, Pb: 0.002%, B: 0.18%, with the balance being Fe and unavoidable impurities. The laser used in the layer-by-layer melting process has a power of 2000W, a frequency of 10000Hz, and a scanning speed of 15mm / s.

[0050] Example 2 The difference from Example 1 is that, by mass percentage, the elemental composition of the steel powder includes: Cr: 17%, Ni: 5.5%, C: 0.05%, Si: 1.5%, Mn: 1.5%, S: 0.012%, P: 0.02%, Mg: 0.008%, Cu: 0.025%, Sn: 0.005%, Ce: 0.005%, La: 0.003%, Mo: 0.57%, Ti: 0.005%, Al: 0.005%, V: 0.06%, W: 0.05%, Co: 0.065%, Zn: 0.004%, Pb: 0.002%, B: 0.17%, with the balance being Fe and unavoidable impurities.

[0051] Example 3 The difference from Example 1 is that, by mass percentage, the elemental composition of the steel powder includes: Cr: 19%, Ni: 5.5%, C: 0.05%, Si: 1.5%, Mn: 1.5%, S: 0.012%, P: 0.02%, Mg: 0.008%, Cu: 0.025%, Sn: 0.005%, Ce: 0.02%, La: 0.001%, Mo: 0.57%, Ti: 0.005%, Al: 0.005%, V: 0.06%, W: 0.05%, Co: 0.065%, Zn: 0.004%, Pb: 0.002%, B: 0.19%, with the balance being Fe and unavoidable impurities.

[0052] Comparative Example 1 The difference from Example 1 is that the Cr content is 10%, while the contents of other elements remain unchanged.

[0053] Comparative Example 2 The difference from Example 1 is that Ce was not added, while the contents of other elements remained unchanged.

[0054] Comparative Example 3 The difference from Example 1 is that La was not added, while the contents of other elements remained unchanged.

[0055] Comparative Example 4 The difference from Example 1 is that B was not added, while the contents of other elements remained unchanged.

[0056] Effect Example The tensile strength and elongation after fracture of the additive components prepared in Examples 1 to 3 and Comparative Examples 1 to 4 were tested. The results are shown in Table 1. As can be seen from Table 1, compared with Comparative Examples 1 to 4, the additive components prepared in Examples 1 to 3 have higher tensile strength and elongation after fracture, indicating that the additive components prepared in Examples 1 to 3 have higher strength and ductility.

[0057] Table 1

[0058] The XRD patterns of the additive component prepared in Example 1 before and after tensile deformation were examined, and the results are shown in the figure. Figure 1 ,from Figure 1 As can be seen from the figure, the microstructure of the additive component prepared in Example 1 before tensile deformation is austenite and ferrite, and after tensile deformation, some of the austenite is transformed into martensite. Figure 1 The curve below “Before Deformation” is the XRD curve of the additive component obtained in Example 1 before tensile deformation. Figure 1 The curve below "After Deformation" is the XRD curve of the additive component after tensile deformation obtained in Example 1.

[0059] Scanning electron microscopy analysis was performed on the metallographic structure of the additive component prepared in Example 1 before and after tensile deformation. The results are shown in the figure. Figure 2 and Figure 3 ,from Figure 2 It can be seen that the metallographic structure of the additive component prepared in Example 1 before tensile deformation contains a σ phase. Figure 3 It can be seen that after the additive component prepared in Example 1 is stretched and deformed, the microcracks appearing in the σ phase stop propagating at the matrix phase interface. The matrix phase acts as a crack buffer layer, which acts on the microcrack tip to passivate it and shield the related local high stress. When the microcrack penetrates the entire σ phase, the surrounding martensitic matrix will passivate the crack tip, indicating that the σ phase can play a buffering role in the fracture of the component.

[0060] While the present invention has been disclosed above, its scope of protection is not limited thereto. Those skilled in the art can make various changes and modifications without departing from the spirit and scope of the present invention, and all such changes and modifications will fall within the scope of protection of the present invention.

Claims

1. An ultra-high strength steel powder for additive manufacturing, characterized in that, The elemental composition, by mass percentage, includes: Cr: 17% to 19%, Ni: 5% to 6%, C: 0.01% to 0.1%, Si: 1% to 2%, Mn: 1% to 2%, S: 0.005% to 0.02%, P: 0.01% to 0.03%, Mg: 0.005% to 0.01%. Cu: 0.02% to 0.03%, Sn: 0.001% to 0.01%, Ce: 0.005% to 0.02%, La: 0.001% to 0.003%, Mo: 0.56% to 0.59%, Ti: 0.001% to 0.01%, Al: 0.001% to 0.01%, V: 0.05% to 0.07%, W: 0.03% to 0.07%, Co: 0.06% to 0.07%, Zn: 0.003% to 0.005%, Pb: 0.001% to 0.003%, B: 0.17% to 0.19%, balance Fe and unavoidable impurities.

2. The ultra-high strength steel powder for additive manufacturing according to claim 1, characterized in that, The ultra-high strength steel powder used for additive manufacturing has a particle size of 15 μm to 45 μm.

3. A method for preparing ultra-high strength steel powder for additive manufacturing as described in claim 1 or 2, characterized in that, include: Step S1: Vacuum melt the raw materials to obtain molten steel; Step S2: The molten steel is atomized to produce steel powder.

4. The method for preparing ultra-high strength steel powder for additive manufacturing according to claim 3, characterized in that, In step S1, the temperature of the vacuum melting is 1580°C to 1620°C, and the time is 2 hours to 4 hours.

5. The method for preparing ultra-high strength steel powder for additive manufacturing according to claim 3, characterized in that, In step S2, the atomizing gas used in the gas atomization powder preparation process is argon.

6. The method for preparing ultra-high strength steel powder for additive manufacturing according to claim 3, characterized in that, In step S2, the pressure of the atomizing gas is 3.5 MPa to 5.0 MPa.

7. An additive component, characterized in that, It is prepared using ultra-high strength steel powder for additive manufacturing as described in claim 1 or 2 as raw material.

8. A method for preparing an additive component as described in claim 7, characterized in that, include: Laser-directed energy deposition is used to melt and shape ultra-high strength steel powder for additive manufacturing layer by layer to obtain additive components.

9. The method for preparing an additive manufacturing component according to claim 8, characterized in that, The laser used in the layer-by-layer melting and forming process has a power of 1900W to 2100W and a frequency of 95000Hz to 105000Hz.

10. The method for preparing the additive component according to claim 8, characterized in that, The scanning speed of the laser used in the layer-by-layer melting and forming process is 10 mm / s to 20 mm / s.

Images