High-formability and high-strength aluminum alloy powder, preparation method and application

Abstract

The invention provides high-formability and high-strength aluminum alloy powder as well as a preparation method and application thereof. The aluminum alloy powder material comprises the following components in percentage by mass: 1.0-4.0 wt% of Cr; 1.0 to 4.0 wt% of Mg; mn: 0.5 to 2.5 wt%; 1.0 to 5.0 wt% of Zr; the balance is Al; wherein the ratio of Cr to Mg is 1: 1, and the ratio of Mn to Zr is 1: 2. Compared with a traditional aluminum alloy powder material, the aluminum alloy powder material can break through the solid solution limit of the material during material forming, additive manufacturing is achieved, non-uniform precipitation of a primary phase in the material can serve as a non-uniform nucleating agent of alpha-Al, heterogeneous nucleation of alpha-Al in the laser additive manufacturing process is promoted, and the laser additive manufacturing efficiency is improved. The stacking fault energy of the aluminum alloy is remarkably reduced by adding high Cr and Mg contents, twin crystals and 9R phases are introduced into the aluminum alloy, finally, the prepared material is uniform in structure, free of obvious segregation and isotropic in mechanical property, and the performance goals of high yield ratio, high formability and high strength are achieved.

Description

Technical Field

[0001] The present invention relates to the technical field of additive manufacturing, and in particular to a high-formability and high-strength aluminum alloy powder, a preparation method and an application thereof. Background Art

[0002] With the vigorous development of industries such as aviation and aerospace, especially with the rise of the private aerospace industry today, the cost and recyclability of aircraft are becoming increasingly important. Additive manufacturing, as a stable and reliable rapid prototyping process, has a huge driving force for complex structure molding, multi-component integrated molding and the liberation of design freedom. One generation of technology, one generation of application, one generation of materials, the innovation of technology is bound to bring about the development of materials to cooperate with the better development and application of technology. As the most widely used basic material in the aerospace industry, aluminum alloy has many advantages such as high specific strength and good thermal conductivity. However, the mature aviation forged aluminum currently cannot meet the requirements of additive manufacturing technology. There are thermal cracks and solidification cracks in the molding process, which cannot be used in practice. Therefore, based on the requirements of additive manufacturing technology, it is necessary to develop special alloys to match it.

[0003] Among the aluminum alloy materials for additive manufacturing that can be maturely applied at present, only some Al-Si alloys and very few Al-Mg alloys can be used for laser additive forming. However, Al-Si alloys are subject to the influence of the material system and the inherent solid solubility of elements in aluminum alloys, and the material performance is not excellent enough. Although Al-Mg alloys have good strength, the Mg content added in the process of pursuing high strength is very high, resulting in the formation of a large amount of volatile smoke under the bombardment of the laser. The high porosity of the material affects the density of the material. Although the formed material has high strength, it is very easy to fatigue and become unstable, which seriously affects its practical application and promotion. Furthermore, the Al-Mg alloys currently used are all strengthened by Sc, that is, the Al-Mg-Sc system. The high price of raw materials also limits the application and promotion of materials. Therefore, starting from the material design end, we break through the material solid solubility limit through the process end to provide an aluminum alloy material system with high strength, toughness and even performance, which can not only adapt to the laser additive manufacturing process, but also be promoted for practical application.

[0004] In the existing technology, Al-Si alloys are most suitable for laser additive manufacturing, but the material properties are average and their application is very limited, making it difficult to adapt to the manufacturing of structural load-bearing parts. Summary of the invention

[0005] In view of this, the purpose of the present invention is to provide a high-formability, high-strength aluminum alloy powder, a preparation method and an application, aiming to solve the problems of general performance and limited application of aluminum alloy materials in the prior art.

[0006] The embodiment of the present invention is implemented as follows:

[0007] A high-formability and high-strength aluminum alloy powder, comprising the following components by mass percentage:

[0008] Cr: 1.0~4.0wt%; Mg: 1.0~4.0wt%; Mn: 0.5~2.5wt%; Zr: 1.0~5.0wt%; the balance is Al;

[0009] Among them, the ratio of Cr / Mg is 1:1, and the ratio of Mn / Zr is 1:2.

[0010] Furthermore, in the above-mentioned high-formability and high-strength aluminum alloy powder, the aluminum alloy powder material also includes Sc, and the content of Sc is ≤3.0wt%.

[0011] Furthermore, in the above-mentioned high-formability and high-strength aluminum alloy powder, the aluminum alloy powder material also includes an additive element, and the additive element includes any one of Fe, Ni, Mo and Ce.

[0012] Furthermore, in the above-mentioned high-formability and high-strength aluminum alloy powder, the content of the added element is ≤3.0wt%.

[0013] Furthermore, the above-mentioned high-formability and high-strength aluminum alloy powder, wherein the raw material of the aluminum alloy powder is a combination of aluminum-chromium alloy, pure magnesium, aluminum-manganese alloy, aluminum-zirconium alloy, pure aluminum and aluminum-scandium alloy.

[0014] Furthermore, in the above-mentioned high-formability and high-strength aluminum alloy powder, the raw material of the added element is any one of aluminum-iron alloy, aluminum-nickel alloy, aluminum-molybdenum alloy, and aluminum-cerium alloy.

[0015] Another object of the present invention is to provide a method for preparing an aluminum alloy powder material, which is used to prepare any of the aluminum alloy powder materials described above, characterized in that the method comprises:

[0016] Weighing a required amount of raw alloy combination and placing it in an atomizing equipment melting device, evacuating the melting device and then filling it with inert gas to standard atmospheric pressure;

[0017] After the raw alloy is melted into alloy liquid, the alloy liquid is kept warm and allowed to stand for a long time to diffuse evenly, thereby obtaining alloy liquid;

[0018] Inert gas is filled into the atomizing disk below the smelting device, accelerated through the annular cavity, and ejected at high speed from the bottom annular gap, so that the prepared alloy melt collides with the bottom of the disk liquid guide tube at high speed to be atomized, broken into small droplets, and then cooled to obtain the aluminum alloy powder.

[0019] Furthermore, in the above-mentioned method for preparing aluminum alloy powder material, the melting temperature is 650°C to 950°C, the insulation temperature is 750°C to 1050°C, and the insulation standing time is 5min to 30min.

[0020] Furthermore, in the above-mentioned method for preparing aluminum alloy powder material, the injection speed of the inert gas is 3-4 Mach, and the gas outlet angle of the annular gap of the atomizing disk is 63°.

[0021] Another object of the present invention is to provide an application method of the aluminum alloy powder material prepared by the above-mentioned preparation method, characterized in that the application method comprises:

[0022] The aluminum alloy powder material is used as a printing material, and a 3D printing process is used to print the printing material based on the three-dimensional graphic file to be printed, and a printed product is obtained by heat treatment, wire cutting, and surface treatment;

[0023] Among them, the 3D printing is red light fiber laser SLM printing, the preheating temperature of the printer plate is 10-120°C, the laser power is 150-370W, the scanning speed is 800-1590mm / s, the scanning spacing is 0.08-0.15mm, the scanning layer thickness is 0.03-0.09mm, the area overlap is set to 0.14mm, the insulation temperature of the heat treatment is 250-450°C, and the insulation time is 1-6h.

[0024] Compared with the existing technology: the aluminum alloy powder material can break through the solid solution limit of the material during material forming and realize additive manufacturing, and the uneven precipitation of primary Al3 (Sc, Zr) particles in the material can serve as a non-uniform nucleating agent for α-Al, promoting the heterogeneous nucleation of α-Al during the printing process. Adding higher Cr and Mg content can significantly reduce the stacking fault energy of the aluminum alloy, and can form twins and 9R phases in the aluminum alloy, ultimately achieving uniform structure of the material, no obvious segregation, isotropic mechanical properties, and achieving the performance goals of high yield ratio, high formability, and high strength. BRIEF DESCRIPTION OF THE DRAWINGS

[0025] Figure 1 A microscopic image of a printed sample of an aluminum alloy powder material prepared by a method for preparing a high-formability and high-strength aluminum alloy powder material proposed in one embodiment of the present invention;

[0026] Figure 2 This is a microscopic image of a heat-treated sample of an aluminum alloy powder material prepared by a method for preparing a high-formability and high-strength aluminum alloy powder material proposed in one embodiment of the present invention. DETAILED DESCRIPTION

[0027] Unless otherwise defined, all technical and scientific terms used herein have the same meaning as those commonly understood by those skilled in the art of the present invention. The terms used in the specification of the present invention herein are only for the purpose of describing specific embodiments and are not intended to limit the present invention.

[0028] In addition, the term "and / or" as used herein includes any and all combinations of one or more related listed items. In the detailed description and claims, a list of items connected by the term "one of" may mean any of the listed items. For example, if items A and B are listed, the phrase "one of A and B" means only A or only B. In another example, if items A, B, and C are listed, the phrase "one of A, B, and C" means only A; only B; or only C. Item A may contain a single element or multiple elements. Item B may contain a single element or multiple elements. Item C may contain a single element or multiple elements. In the detailed description and claims, a list of items connected by the terms "at least one of", "at least one of" or other similar terms may mean any combination of the listed items. For example, if items A and B are listed, the phrase "at least one of A and B" or "at least one of A or B" means only A; only B; or A and B. In another example, if items A, B, and C are listed, the phrase "at least one of A, B, and C" or "at least one of A, B, or C" means only A; or only B; only C; A and B (excluding C); A and C (excluding B); B and C (excluding A); or all of A, B, and C. Item A may include a single element or multiple elements. Item B may include a single element or multiple elements. Item C may include a single element or multiple elements.

[0029] In view of the problems that the current aluminum alloy materials have general performance and limited application, the present invention proposes a high-formability and high-strength aluminum alloy powder material, a preparation method and an application, wherein the alloy powder material comprises Cr: 1.0-4.0wt%; Mg: 1.0-4.0wt%; Mn: 0.5-2.5wt%; Zr: 1.0-5.0wt%; the balance is Al; wherein the ratio of Cr / Mg is 1:1, and the ratio of Mn / Zr is 1:2.

[0030] Among them, adding higher Cr and Mg contents can significantly reduce the stacking fault energy of the aluminum alloy, and promote the formation of twins and 9R phases in the aluminum alloy. In some embodiments of the present invention, the aluminum alloy powder material also includes Sc, and the Sc content is ≤3.0wt%. The in-situ formation of primary L12-Al3 (Sc, Zr) precipitates can serve as an effective nuclear core to promote the heterogeneous nucleation of α-Al during the printing process. The aluminum alloy powder material also includes added elements, and the added elements include any one of Fe, Ni, Mo, and Ce. Specifically, the content of the added elements is ≤3.0wt%. Among them, the aluminum alloy powder material containing Sc can achieve high strength at room temperature, the aluminum alloy powder material not containing Sc can achieve medium strength at room temperature, and the aluminum alloy powder material containing Sc and containing one of Fe or Ni or Mo or Ce can achieve high temperature and high strength.

[0031] Specifically, the raw material of the aluminum alloy powder is a combination of aluminum-chromium alloy, pure magnesium, aluminum-manganese alloy, aluminum-zirconium alloy, pure aluminum, aluminum-scandium alloy, aluminum-iron alloy, aluminum-nickel alloy, aluminum-molybdenum alloy, and aluminum-cerium alloy.

[0032] Another aspect of the present invention further provides a method for preparing a high-formability and high-strength aluminum alloy powder material, which is used to prepare the above-mentioned aluminum alloy powder material, and the method comprises:

[0033] Weighing a required amount of raw alloy combination and placing it in an atomizing equipment melting device, evacuating the melting device and then filling it with inert gas to standard atmospheric pressure;

[0034] After the raw alloy is melted into alloy liquid, the alloy liquid is kept warm and allowed to stand for a long time to diffuse evenly, thereby obtaining alloy liquid;

[0035] Inert gas is filled into the atomizing disk below the smelting device, accelerated through the annular cavity, and ejected at high speed from the bottom annular gap, so that the prepared alloy melt collides with the bottom of the disk liquid guide tube at high speed to be atomized, broken into small droplets, and then cooled to obtain the aluminum alloy powder.

[0036] Furthermore, in the above-mentioned method for preparing the high-formability and high-strength aluminum alloy powder material, the melting temperature is 650°C to 950°C, the insulation temperature is 750°C to 1050°C, and the insulation standing time is 5min to 30min.

[0037] Furthermore, in the above-mentioned method for preparing high-formability and high-strength aluminum alloy powder material, the injection speed of the inert gas is 3-4 Mach, and the gas outlet angle of the annular seam of the atomizing disk is 63°.

[0038] Another aspect of the present invention further provides an application method of the aluminum alloy powder prepared by the above-mentioned preparation method, the application method comprising:

[0039] The aluminum alloy powder material is used as a printing material, and a 3D printing process is used to print the printing material based on the three-dimensional graphic file to be printed, and a printed product is obtained by heat treatment, wire cutting, and surface treatment;

[0040] Among them, the 3D printing is red light fiber laser SLM printing, the preheating temperature of the printer plate is 10-120°C, the laser power is 150-370W, the scanning speed is 800-1590mm / s, the scanning spacing is 0.08-0.15mm, the scanning layer thickness is 0.03-0.09mm, the area overlap is set to 0.14mm, the insulation temperature of the heat treatment is 250-450°C, and the insulation time is 1-6h. Specifically, vacuum heat treatment is adopted, the insulation temperature is 250-450°C, the insulation time is 1-6h, and then air cooling is adopted.

[0041] In order to facilitate understanding of the present invention, several embodiments of the present invention are provided below. However, the present invention can be implemented in many different forms and is not limited to the embodiments described herein. On the contrary, the purpose of providing these embodiments is to make the disclosure of the present invention more thorough and comprehensive.

[0042] Example 1

[0043] The following are the ingredients according to mass percentage: 2.0wt% Cr, 2.0wt% Mg, 1.5wt% Mn, 3.0wt% Zr, and the balance Al, wherein the ratio of Cr / Mg is 1:1 and the ratio of Mn / Zr is 1:2. The required amount of raw alloy is weighed and placed in a smelting device. The smelting device is evacuated to a vacuum degree of 10Pa, and then filled with inert gas to atmospheric pressure. After being smelted at 750°C into a molten liquid, the molten liquid is kept at 850°C for 20 minutes to obtain an alloy melt. Nitrogen is filled into the smelting device, and the obtained alloy melt is atomized with a high-speed inert gas flow, and the molten alloy is broken into small droplets to obtain an original powder.

[0044] Example 2

[0045] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0046] Sc: 2.0 wt % by mass. The required amount of raw alloy is weighed and placed in a smelting device.

[0047] Example 3

[0048] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0049] In terms of mass percentage, Sc: 2.0wt%; Fe: 1.8wt%. The required amount of raw material alloy is weighed and placed in a smelting device.

[0050] Example 4

[0051] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0052] According to the mass percentage of Cr: 1.0wt%, Mg: 1.0wt%, the required amount of raw material alloy is weighed and placed in a smelting device.

[0053] Example 5

[0054] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0055] According to the mass percentage of Cr: 4.0wt%, Mg: 4.0wt%, the required amount of raw material alloy is weighed and placed in a smelting device.

[0056] Example 6

[0057] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0058] According to the mass percentage of Zr: 1.0wt%, Mn: 0.5wt%, the required amount of raw material alloy is weighed and placed in a smelting device.

[0059] Example 7

[0060] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0061] According to the mass percentage of Zr: 5.0wt%, Mn: 2.5wt%, the required amount of raw material alloy is weighed and placed in a smelting device.

[0062] Example 8

[0063] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0064] According to the mass percentages of Sc: 2.0wt%; Ni: 1.8wt%, the required amount of raw material alloy is weighed and placed in a smelting device.

[0065] Example 9

[0066] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0067] According to the mass percentages of Sc: 2.0wt%; Mo: 1.8wt%, the required amount of raw material alloy is weighed and placed in a smelting device.

[0068] Example 10

[0069] This embodiment also provides a method for preparing a high-formability, high-strength aluminum alloy powder material. The difference between the method for preparing a high-formability, high-strength aluminum alloy powder material provided in this embodiment and the method for preparing a high-formability, high-strength aluminum alloy powder material provided in Example 1 is that:

[0070] According to the mass percentage of Sc: 2.0wt%; Ce: 1.8wt%, the required amount of raw material alloy is weighed and placed in a smelting device.

[0071] Please refer to Table 1 below, which shows the parameters corresponding to the above-mentioned embodiments 1-10 of the present invention, as shown in the following table:

[0072] Table 1

[0073]

[0074] In practical applications, the molded parts prepared in the above-mentioned embodiments 1-7 of the present invention are respectively used for testing. It should be noted that, in order to ensure the accuracy of the experimental data, the preparation of the original powder and the molded parts should be the same except for the above-mentioned parameters. The test data are shown in Table 2 below:

[0075] Table 2

[0076]

[0077] Also, see Figure 1 , is a microscopic image of a printed sample of aluminum alloy powder material prepared in an embodiment of the present invention. It can be seen that the printed sample of the material presents a graded non-uniform microstructure with fine grain distribution, which is attributed to the non-uniform precipitation of primary L12-Al3 (Sc, Zr) particles, which can serve as a non-uniform nucleating agent for α-Al. At the same time, high-density stacking faults, 9R phases and twins are observed in the organization. It should be noted that it is very difficult to introduce twins and 9R phases into aluminum alloys, mainly because aluminum alloys have a 160mJ / mm 2 The stacking fault energy of aluminum alloy is significantly reduced by adding higher content of Cr and Mg elements in the present invention, thereby introducing twins and 9R phases into aluminum alloy. The printed microstructure shows that the primary Al3 (Sc, Zr) precipitates with L12 ordered structure coincide with the α-Al interface atoms, indicating that there is a completely coherent interface between the two. Therefore, the in-situ formation of Al3 (Sc, Zr) precipitates can serve as an effective nucleating agent to promote the heterogeneous nucleation of α-Al during the printing process. Ultrafine particles with a size of about 40nm were also observed in the grains, which can enhance the mechanical properties of the printed alloy. Figure 2 , is a microscopic image of a heat-treated sample of an aluminum alloy powder material prepared in an embodiment of the present invention. After heat treatment, the alloy still contains 9R phase, Al matrix and a large number of high-density stacking faults, and the grain size does not change significantly. The TEM image of the heat-treated alloy shows that there are a considerable number of precipitated phases, which further improves the mechanical properties of the material. At the same time, two main types of ultrafine particles were detected, including precipitates rich in Al-Mn-(Cr, Mg) and precipitates rich in Al-Sc-Zr. The L12 structure of Al3 (Sc, Zr) does not change during the heat treatment process. This is because the presence of Fe (Co, Mo, Ce) and Zr in Al improves the metastability of the precipitated phase, based on which the material has strong high-temperature performance.

[0078] In summary, combined with the data in Table 1 and Table 2 above, it can be clearly seen that the aluminum alloy powder material prepared by the present invention can break through the solid solubility limit of the material during material forming and realize additive manufacturing forming, and the uneven precipitation of the primary phase in the material can be used as a non-uniform nucleating agent for α-Al to promote the heterogeneous nucleation of α-Al during the printing process. The addition of higher Cr and Mg contents can significantly reduce the stacking fault energy of the aluminum alloy, introduce twins and 9R phases into the aluminum alloy, and finally achieve uniform tissue, no obvious segregation, and isotropic mechanical properties of the prepared material, achieving the performance goals of high yield ratio, high formability, and high strength, and high strength at room temperature when containing Sc and medium strength at room temperature when not containing Sc; high strength at high temperature when containing Sc and Fe or Ni or Mo or Ce.

[0079] The above-mentioned embodiments only express several implementation methods of the present invention, and the description thereof is relatively specific and detailed, but it cannot be understood as limiting the scope of the patent of the present invention. It should be pointed out that, for ordinary technicians in this field, several variations and improvements can be made without departing from the concept of the present invention, which all belong to the protection scope of the present invention. Therefore, the protection scope of the patent of the present invention shall be subject to the attached claims.

Claims

1. A high-formability, high-strength aluminum alloy powder, characterized in that: Calculated by mass percentage, it includes the following components: Cr: 1.0-4.0wt%; Mg: 1.0-4.0wt%; Mn: 0.5-2.5wt%; Zr: 1.0-5.0wt%; the balance is Al; Among them, the ratio of Cr / Mg is 1:1, and the ratio of Mn / Zr is 1:

2.

2. The high formability and high strength aluminum alloy powder according to claim 1, characterized in that: The aluminum alloy powder material further comprises Sc, and the content of Sc is ≤3.0wt%.

3. The high formability and high strength aluminum alloy powder according to claim 2, characterized in that: The aluminum alloy powder material further includes an additive element, and the additive element includes any one of Fe, Ni, Mo and Ce.

4. The high formability and high strength aluminum alloy powder according to claim 3, characterized in that: The content of the added element is ≤3.0wt%.

5. The high formability and high strength aluminum alloy powder according to claim 2, characterized in that: The raw material of the aluminum alloy powder is a combination of aluminum-chromium alloy, pure magnesium, aluminum-manganese alloy, aluminum-zirconium alloy, pure aluminum and aluminum-scandium alloy.

6. The high formability and high strength aluminum alloy powder according to claim 4, characterized in that: The raw material of the added element is any one of aluminum-iron alloy, aluminum-nickel alloy, aluminum-molybdenum alloy and aluminum-cerium alloy.

7. A method for preparing an aluminum alloy powder material, for preparing the aluminum alloy powder material according to any one of claims 1 to 6, characterized in that: The method comprises: Weighing a required amount of raw alloy combination and placing it in an atomizing equipment melting device, evacuating the melting device and then filling it with inert gas to standard atmospheric pressure; After the raw alloy is melted into alloy liquid, the alloy liquid is kept warm and allowed to stand for a long time to diffuse evenly, thereby obtaining alloy liquid; Inert gas is filled into the atomizing disk below the smelting device, accelerated through the annular cavity, and ejected at high speed from the bottom annular gap, so that the prepared alloy melt collides with the bottom of the disk liquid guide tube at high speed to be atomized, broken into small droplets, and then cooled to obtain the aluminum alloy powder.

8. The method for preparing aluminum alloy powder material according to claim 7, characterized in that: The smelting temperature is 650°C to 950°C, the insulation temperature is 750°C to 1050°C, and the insulation standing time is 5min to 30min.

9. The method for preparing aluminum alloy powder material according to claim 7, characterized in that: The inert gas has a firing speed of Mach 3-4 and a gas outlet angle of the annular gap of the atomizing disk of 63°.

10. A method for applying the aluminum alloy powder material prepared by the preparation method according to any one of claims 7 to 9, characterized in that: The application method comprises: The aluminum alloy powder material is used as a printing material, and a 3D printing process is used to print the printing material based on the three-dimensional graphic file to be printed, and a printed product is obtained by heat treatment, wire cutting, and surface treatment; Among them, the 3D printing is red light fiber laser SLM printing, the preheating temperature of the printer plate is 10-120°C, the laser power is 150-370W, the scanning speed is 800-1590mm / s, the scanning spacing is 0.08-0.15mm, the scanning layer thickness is 0.03-0.09mm, the area overlap is set to 0.14mm, the insulation temperature of the heat treatment is 250-450°C, and the insulation time is 1-6h.

Images