Weldable aluminum alloy powder for additive manufacturing and method of making the same

Abstract

The application belongs to the technical field of aluminum alloy powder, and particularly relates to a weldable aluminum alloy powder for additive manufacturing and a preparation method thereof, and comprises the following steps: S1, taking high-purity aluminum ingot, aluminum-manganese intermediate alloy, aluminum-silicon intermediate alloy, pure iron, aluminum-zirconium intermediate alloy and rare earth intermediate alloy as raw materials, melting the high-purity aluminum ingot to form an aluminum melt and keeping the temperature at 750-850 DEG C, respectively adding the aluminum-manganese intermediate alloy, the aluminum-silicon intermediate alloy and the pure iron, fully stirring until uniform, adding preheated aluminum-zirconium intermediate alloy and rare earth intermediate alloy and keeping the temperature at 720-800 DEG C for refining, and obtaining an alloy melt; wherein the rare earth intermediate alloy is an Er-Al intermediate alloy; S2, transferring the alloy melt to an atomization device, atomizing and breaking into small droplets in a high-pressure inert atmosphere, waiting for cooling and solidification, and obtaining fine powder; S3, drying the fine powder, keeping it under an inert atmosphere for standby, and obtaining the aluminum alloy powder.

Description

Technical Field

[0001] This invention belongs to the field of aluminum alloy powder technology, specifically relating to a weldable aluminum alloy powder for additive manufacturing and its preparation method. Background Technology

[0002] Additive manufacturing, also known as 3D printing, involves designing a product model using computer modeling software and then building a solid part by layering materials. This technology not only greatly expands design freedom but also significantly improves manufacturing efficiency and precision. Selective laser melting (SLM), a type of metal additive manufacturing technology, has demonstrated enormous potential in the field of metal parts manufacturing due to its unique technological advantages.

[0003] SLM (Solid Metal Melting) technology achieves metallurgical bonding by precisely controlling the layer-by-layer melting and solidification of metal powder using a high-energy laser beam. This enables the direct fabrication of complex metal parts with high dimensional accuracy and excellent surface quality. This technology not only overcomes the limitations of traditional manufacturing methods in terms of shape complexity, material utilization, and processing costs, but also gains significant attention and recognition due to its high efficiency and environmental friendliness, currently demonstrating enormous potential in aerospace, medical, and automotive fields. As the global industrial sector continues to demand lightweight equipment, low-density, high-performance-to-weight ratio aluminum alloys are gradually becoming the core research material system for metal additive manufacturing. 3003 aluminum alloy, as the most widely used basic rust-resistant aluminum alloy in industry, is also attracting increasing industry attention regarding its SLM forming feasibility and performance control.

[0004] 3003 aluminum alloy is a typical Al-Mn series non-heat-treatable strengthened aluminum alloy. As a highly versatile basic aluminum alloy material, it plays an important role in building decoration, kitchenware containers, and transportation due to its good formability, excellent corrosion resistance, and reliable weldability. However, due to the inherent characteristics of the alloy system, the room temperature strength of 3003 aluminum alloy is relatively low, and the potential for strength improvement under existing traditional processing techniques is very limited. This makes it difficult to adapt to applications with higher requirements for structural load-bearing capacity, which to some extent restricts the expansion of this material into high-end structural components.

[0005] Therefore, overcoming the deficiency of 3003 aluminum alloy in terms of insufficient strength in SLM deposited metal parts is a technical problem that urgently needs to be solved in this field.

[0006] It should be noted that the information disclosed in this background section is only for understanding the background technology of the present application concept, and therefore, the above description is not considered to constitute prior art information. Summary of the Invention

[0007] This disclosure provides at least one weldable aluminum alloy powder for additive manufacturing and a method for preparing the same.

[0008] In a first aspect, the present disclosure provides a method for preparing aluminum alloy powder, comprising the following steps: S1, weighing high-purity aluminum ingots, aluminum-manganese master alloys, aluminum-silicon master alloys, pure iron, aluminum-zirconium master alloys, and rare earth master alloys as raw materials; melting the high-purity aluminum ingots to form an aluminum melt and maintaining the temperature at 750-850°C; adding aluminum-manganese master alloys, aluminum-silicon master alloys, and pure iron respectively; stirring thoroughly until homogeneous; adding preheated aluminum-zirconium master alloys and rare earth master alloys; and refining at 720-800°C to obtain an alloy melt; wherein the rare earth master alloy is an Er-Al master alloy; S2, transferring the alloy melt to an atomizing device; atomizing and breaking it into fine droplets in a high-pressure inert atmosphere; and cooling and solidifying to obtain fine powder; S3, drying the fine powder and storing it in an inert atmosphere to obtain aluminum alloy powder.

[0009] In one optional embodiment, the aluminum alloy powder comprises the following components by weight percentage: Mn 0.5-1.5%, Si ≤0.6%, Fe ≤0.7%, Zr 0.15-0.2%, Cu 0.05-0.2%, Mg and / or Zn <0.03%, Er 0.3-0.4%, with the balance being Al.

[0010] In an optional embodiment, the temperature of the alloy melt in S2 is controlled at 150–300°C above the target alloy liquidus temperature.

[0011] In one optional embodiment, the temperature control range of the alloy melt in S2 is 850–950°C.

[0012] In one optional embodiment, the pressure at the nozzle of the atomizing device in S2 is 3 to 8 MPa; the inert atmosphere includes either nitrogen or argon.

[0013] In one optional embodiment, the drying process in S3 includes: drying the fine powder, then screening it to obtain fine powder within a preset particle size range, and then vacuum drying it again.

[0014] Secondly, this disclosure also provides an aluminum alloy powder, which is prepared by the method described above.

[0015] The beneficial effects of this invention are as follows: The weldable aluminum alloy powder for additive manufacturing and its preparation method introduce the rare earth element Er into the traditional 3003 aluminum alloy composition system. During the solidification process of the molten pool, Er promotes the formation of fine equiaxed α-Al grains and inhibits the continuous growth of coarse columnar α-Al grains, thereby improving the microstructure uniformity and mechanical properties of the formed parts. Secondly, this rare earth element can combine with impurities such as hydrogen and oxygen in the aluminum melt, playing a role in deeply purifying grain boundaries. Furthermore, this rare earth element can form high-temperature stable nanoscale dispersed phases with elements such as Al and Mn. These precipitated phases can effectively inhibit recrystallization and dislocation pinning during thermal cycling, providing a significant precipitation strengthening effect. More importantly, the fine equiaxed α-Al grain structure helps reduce the material's hot cracking sensitivity during welding and interlayer remelting in additive manufacturing, thereby improving the weldability of the formed parts and the process stability during subsequent joining or repair processes.

[0016] Thirdly, this disclosure also provides a method for manufacturing 3003 aluminum alloy additives, which uses laser powder bed melting process to form components, including the following steps: S41, preheating the aluminum alloy substrate and uniformly laying a layer of aluminum alloy powder as described above; S42, selectively scanning and melting the aluminum alloy powder until the powder is completely melted and forms a metallurgical bond with the underlying layer; S43, after completing the scanning of one layer, the forming platform descends by the thickness of the powder layer, lays another layer of aluminum alloy powder, and repeats S42 until the solid part is manufactured; S44, the solid part is taken out along with the substrate and subjected to stress-relief annealing or aging heat treatment to obtain the finished product.

[0017] In one optional embodiment, the preheating temperature in S41 is 100-200°C, and the thickness of the aluminum alloy powder is 20-60 μm; the scanning speed of selective scanning melting in S42 is 800-2000 mm / s, and the line spacing is 50-130 μm; the stress-relief annealing in S44 includes holding at 300-350°C for 1-2 hours; the aging heat treatment includes a first aging stage, in which the first aging stage is held at 300-325°C for 4-10 hours.

[0018] Fourthly, this disclosure also provides a 3003 aluminum alloy additive manufacturing process, which is prepared using the method described above.

[0019] The beneficial effects of this invention are that the 3003 aluminum alloy additive manufacturing deeply integrates aluminum alloy powder with additive manufacturing technology. Through systematic powder engineering, aluminum alloy powder with high sphericity, narrow particle size distribution, low oxygen content and uniform composition is prepared. The optimized powder material can be directly and rapidly formed into physical samples, expanding the application of 3003 aluminum alloy in SLM metal parts with high structural load-bearing capacity requirements.

[0020] Other features and advantages of the invention will be set forth in the description which follows, and will be apparent in part from the description, or may be learned by practicing the invention. The objects and other advantages of the invention are realized and obtained through the structures particularly pointed out in the description.

[0021] To make the above-mentioned objects, features and advantages of the present invention more apparent and understandable, preferred embodiments are described in detail below. Detailed Implementation

[0022] To make the objectives, technical solutions, and advantages of the embodiments of the present invention clearer, the technical solutions of the present invention will be clearly and completely described below. Obviously, the described embodiments are only some embodiments of the present invention, not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0023] As used herein, the phrases “in one embodiment,” “according to one embodiment,” “in some embodiments,” etc., generally refer to the fact that a particular feature, structure, or characteristic following the phrase can be included in at least one embodiment of this disclosure. Therefore, a particular feature, structure, or characteristic can be included in more than one embodiment of this disclosure, such that these phrases do not necessarily refer to the same embodiment. As used herein, the terms “example,” “exemplary,” etc., are used to “serve as an example, instance, or illustration.” Any implementation, aspect, or design described herein as “example” or “exemplary” is not necessarily to be construed as preferred or superior to other implementations, aspects, or designs. Rather, the use of the terms “example,” “exemplary,” etc., is intended to present concepts in a specific manner.

[0024] The following describes some embodiments of the present invention in detail. Unless otherwise specified, the following embodiments and features can be combined with each other.

[0025] This disclosure provides a method for preparing aluminum alloy powder, comprising the following steps: S1, weighing high-purity aluminum ingots, aluminum-manganese master alloy, aluminum-silicon master alloy, pure iron, aluminum-zirconium master alloy, and rare earth master alloy as raw materials; melting the high-purity aluminum ingots to form an aluminum melt and maintaining the temperature at 750-850°C; adding aluminum-manganese master alloy, aluminum-silicon master alloy, and pure iron respectively; stirring thoroughly until homogeneous; adding preheated aluminum-zirconium master alloy and rare earth master alloy; and refining at 720-800°C to obtain an alloy melt; wherein the rare earth master alloy is an Er-Al master alloy; S2, transferring the alloy melt to an atomizing device; atomizing and breaking it into fine droplets in a high-pressure inert atmosphere; and cooling and solidifying to obtain fine powder; S3, drying the fine powder and storing it under an inert atmosphere to obtain aluminum alloy powder.

[0026] Specifically, in the powder preparation process, this invention controls the superheating temperature of the alloy melt and uses high-pressure inert gas for atomization, causing the alloy melt to rapidly break down into fine droplets and solidify quickly. This improves the uniformity of alloy element distribution in the powder particles and yields aluminum alloy powder with high sphericity and a concentrated particle size distribution. Further, sieving and vacuum drying processes reduce the adverse effects of powder particles that do not meet the target particle size requirements and adsorbed moisture on the subsequent laser powder bed melting process, thereby improving the stability of the powder spreading and melting processes and providing a foundation for obtaining additive manufacturing components with high density and high mechanical properties.

[0027] In some embodiments, specifically, the aluminum alloy powder comprises the following components by weight percentage: Mn 0.5-1.5%, Si≤0.6%, Fe≤0.7%, Zr 0.15-0.2%, Cu 0.05-0.2%, Mg and / or Zn<0.03%, Er 0.3-0.4%, with the balance being Al.

[0028] In some embodiments, specifically, the temperature of the alloy melt in S2 is controlled at 150–300°C above the target alloy liquidus temperature.

[0029] In some embodiments, specifically, the temperature control range of the alloy melt in S2 is 850–950°C.

[0030] The target alloy liquidus temperature is determined based on the actual alloy composition of the aluminum alloy powder. In some embodiments, the liquidus temperature of the target alloy can be obtained by differential scanning calorimetry (DSC), differential thermal analysis (DTA), or thermodynamic calculations, and the superheat of the alloy melt before atomization can be controlled based on the determined liquidus temperature.

[0031] By maintaining an appropriate degree of superheat in the alloy melt, the fluidity and atomization stability of the alloy melt during atomization can be improved, allowing the melt to be fully broken into fine droplets under the action of a high-speed inert gas flow, and then forming alloy powder with a relatively uniform composition distribution during the subsequent rapid cooling process.

[0032] In some embodiments, specifically, the pressure at the nozzle of the atomizing device in S2 is 3–8 MPa; the inert atmosphere includes either nitrogen or argon. Atomizing the alloy melt with a high-pressure inert gas allows for thorough fragmentation and rapid cooling and solidification, resulting in alloy powder with small particle size and uniform composition. Furthermore, the inert atmosphere reduces the oxidation of the alloy powder during atomization and cooling, which is beneficial for improving powder quality and the stability of subsequent additive manufacturing.

[0033] In some embodiments, specifically, the drying process in S3 includes: drying the fine powder, then screening it to obtain fine powder within a preset particle size range, and then vacuum drying it again. By controlling the particle size distribution of the powder used for additive manufacturing through sieving, and by reducing the moisture adsorbed on the powder surface through vacuum drying again, it is beneficial to improve the powder spreading stability and the stability of the laser melting process, and reduce forming defects caused by excessive differences in powder particle size or surface adsorbates.

[0034] This disclosure also provides an aluminum alloy powder, which is prepared by the method described above.

[0035] This disclosure also provides a method for manufacturing 3003 aluminum alloy additives, which uses laser powder bed melting process to form components, including the following steps: S41, preheating the aluminum alloy substrate and uniformly laying a layer of aluminum alloy powder as described above; S42, selectively scanning and melting the aluminum alloy powder until the powder is completely melted and forms a metallurgical bond with the underlying layer; S43, after completing the scanning of one layer, the forming platform descends by the thickness of the powder layer, lays another layer of aluminum alloy powder, and repeats S42 until the solid part is manufactured; S44, the solid part is removed along with the substrate and subjected to stress-relief annealing or aging heat treatment to obtain the finished product.

[0036] In some embodiments, specifically, in S41 the preheating temperature is 100-200°C and the thickness of the aluminum alloy powder is 20-60 μm; in S42 the selective scanning melting scanning speed is 800-2000 mm / s and the line spacing is 50-130 μm; in S44 the stress-relief annealing includes holding at 300-350°C for 1-2 hours; the aging heat treatment includes a first aging stage, in which the first aging stage is held at 300-325°C for 4-10 hours.

[0037] In some embodiments, the aging heat treatment further includes a second aging stage performed after the first aging stage.

[0038] This disclosure also provides an additive manufacturing method for 3003 aluminum alloy, which is prepared using the method described above.

[0039] Example 1: S1, Smelting: High-purity aluminum ingots (≥99.9%) are placed in a vacuum induction melting furnace and evacuated to 5×10⁻⁶. -2 After passing through a pressure of 0.05 MPa, high-purity argon gas is introduced to the atmosphere. The aluminum ingot is heated until completely melted, with the melt temperature controlled at 800℃. Al-20Mn master alloy, Al-50Si master alloy, and pure Fe are added, and the mixture is stirred electromagnetically for 20 minutes to ensure homogeneity. Then, preheated Al-5Er and Al-10Zr master alloys are added, and the mixture is stirred and held at that temperature for 15 minutes to refine the alloy melt.

[0040] S2, Gas Atomization: Based on detection / calculation, the liquidus temperature of the target alloy in this embodiment is 654℃. The refined alloy melt is transferred to the insulated crucible of the gas atomization equipment. The melt temperature before the guide tube is controlled at 920℃, i.e., the alloy melt temperature is controlled to be approximately 654℃ higher than the target alloy liquidus temperature. High-pressure nitrogen (purity ≥99.999%) is used as the atomization medium, and the atomization pressure is set to 5.5MPa. The melt flows through a 4mm diameter quartz guide tube and is broken up and solidified by the high-speed gas flow to obtain fine powder.

[0041] S3, Powder Post-processing: Collect the powder from the bottom of the atomization tower and dry it in a vacuum drying oven at 40℃ for 4 hours. Then, use a vibrating sieve to separate the powder in the 15-53μm particle size range. The sieved powder is sealed in an argon-protected glove box and stored in a sealed container for later use, yielding aluminum alloy powder.

[0042] The material proportions of the aluminum alloy powder are as follows (by weight percentage): Mn: 1.2%, Si: 0.2%, Fe: 0.15%, Cu: 0.1%, Zr: 0.15%, Er: 0.3%; Balance: Al and unavoidable impurities, where individual impurities are <0.05% and total impurities are <0.15%.

[0043] S4 uses laser powder bed melting process to form components; Equipment and parameters: Laser powder bed melting equipment (Laiming 260A) was used. The substrate was an AlSi10Mg aluminum alloy plate, preheated to 150℃. Process parameters are as follows: Laser power: 280 W, scanning speed: 1200 mm / s, powder layer thickness: 40 μm, scanning spacing: 80 μm Forming process: Following the above parameters, print layer by layer with a size of 10×10×10 mm. 3 Cube specimens were used for density testing, and standard tensile specimens conforming to GB / T 228.1-2021 were prepared.

[0044] Post-processing: The formed sample is cut and separated from the substrate by wire cutting, and then subjected to two-stage aging heat treatment. In the first aging stage, the sample is held at 325°C for 6 hours and then air-cooled. In the second aging stage, the sample is held at 400°C for 0.5 hours and then air-cooled.

[0045] Performance Testing and Evaluation Powder properties: Morphology and particle size: Scanning electron microscopy (SEM) revealed that the aluminum alloy powder obtained in this embodiment was generally spherical or nearly spherical in shape, with relatively few satellite particles. Laser particle size analyzer measurements showed D10 = 22.5 μm, D50 = 38.2 μm, and D90 = 51.8 μm.

[0046] Flowability: The flow rate measured by the Hall effect flow meter is 135 s / 50g, according to ASTM B213 standard.

[0047] Oxygen content: The oxygen content was measured to be 180 ppm by inert gas melting-infrared absorption method.

[0048] The above results indicate that by controlling the temperature of the alloy melt before atomization, the atomization pressure of the inert gas, and the powder post-treatment process, aluminum alloy powder with a relatively concentrated particle size distribution and low oxygen content can be obtained, providing a good powder foundation for obtaining stable powder spreading and high-density forming during the subsequent laser powder bed melting process.

[0049] Properties of molded parts: Density: The relative density of the cubic specimen was measured using the Archimedes displacement method, and it reached 99.5%.

[0050] Mechanical properties: The tensile specimens after heat treatment were tested, and the results are as follows: Tensile strength (Rm): 185 MPa, yield strength (Rp0.2): 123 MPa, elongation after fracture (A): 17%.

[0051] Weldability evaluation: After polishing and etching, the sample was observed using a metallographic microscope and SEM. The microstructure of the formed part was mainly composed of fine equiaxed α-Al grains, and no obvious coarse columnar α-Al grains or cracks were observed. Electron backscatter diffraction (EBSD) analysis showed that the average grain size was 3.8 μm, and fine precipitates were observed to be dispersed.

[0052] Weldability evaluation: After undergoing the same heat treatment, the two additively manufactured test plates were laser butt welded without filler wire treatment.

[0053] X-ray inspection of the welded joint revealed no macroscopic cracks or porosity. Microhardness testing of the welded joint cross-section showed that the hardness of the heat-affected zone did not decrease significantly, and the width of the softened zone was significantly smaller than that of conventional 3003 aluminum alloy.

[0054] The tensile strength of the welded joint reaches 92% of the strength of the base material (additive manufacturing state).

[0055] Example 2: The preparation process is the same as in Example 1, except that the raw material ratio in S1 is adjusted, the melt temperature before the guide tube in S2 is controlled at 920℃, and the atomization pressure is adjusted to 4.0MPa to obtain powder with D50=42.5μm.

[0056] The material proportions of the aluminum alloy powder are as follows (by weight percentage): Mn: 1.3%, Si: 0.4%, Fe: 0.45%, Cu: 0.15%, Zr: 0.2%, Er: 0.4%; Balance: Al and unavoidable impurities, where individual impurities are <0.05% and total impurities are <0.15%.

[0057] The additive manufacturing parameters in S4 were adjusted to: laser power 320W, scanning speed 1500mm / s, layer thickness 30μm, and scanning spacing 0.08mm. After forming, stress-relief annealing was performed directly at 300℃ for 2 hours.

[0058] Performance testing Density: The relative density of the cubic sample was 99.2% when measured using the Archimedes displacement method.

[0059] Mechanical properties: The tensile specimens after annealing were tested, and the results are as follows: Tensile strength (Rm): 176 MPa, yield strength (Rp0.2): 118 MPa, elongation after fracture (A): = 22.5%.

[0060] Metallographic observation showed that relatively fine equiaxed α-Al grains were formed in the molded part, with an average grain size of 5.2 μm, and no obvious hot cracks were observed.

[0061] Comparative Example Traditional 3003 aluminum alloy powder (composition: Mn 0.8%, Si 0.7%, Fe 0.5%, balance Al) without the addition of any rare earth elements was prepared, and powder preparation and sample printing were performed using the same atomization and additive manufacturing process parameters as in Example 1.

[0062] Observation of the forming process: During the printing process, obvious warping is likely to occur between layers.

[0063] Performance testing Density: The relative density of the cubic specimen was 97.8% when measured using the Archimedes displacement method.

[0064] Mechanical properties: The tensile specimens after heat treatment were tested, and the results are as follows: Tensile strength (Rm): 136 MPa, yield strength (Rp0.2): 89 MPa, elongation after fracture (A): 12%.

[0065] Laser welding test: The welded joint showed obvious hot cracks, and the joint strength was only 65% ​​of the base material.

[0066] In summary, this additive manufacturing weldable aluminum alloy powder and its preparation method introduce the rare earth element Er into the traditional 3003 aluminum alloy composition system. During the solidification process of the molten pool, Er promotes the formation of fine equiaxed α-Al grains and inhibits the continuous growth of coarse columnar α-Al grains, thereby improving the microstructure uniformity and mechanical properties of the formed parts. Secondly, this rare earth element can combine with impurities such as hydrogen and oxygen in the aluminum melt, playing a role in deeply purifying grain boundaries. In addition, this rare earth element can form high-temperature stable nanoscale dispersed phases with elements such as Al and Mn. These precipitated phases can effectively inhibit recrystallization and dislocation pinning during thermal cycling, providing a significant precipitation strengthening effect. More importantly, the fine equiaxed α-Al grain structure helps reduce the hot cracking sensitivity of the material during welding and interlayer remelting in additive manufacturing, thereby improving the weldability of the formed parts and the process stability in subsequent joining or repair processes.

[0067] Based on the above-described preferred embodiments of the present invention, and through the foregoing description, those skilled in the art can make various changes and modifications without departing from the inventive concept. The technical scope of this invention is not limited to the contents of the specification, but must be determined according to the scope of the claims.

Claims

1. A method for preparing aluminum alloy powder, characterized in that, Includes the following steps: S1. Weigh high-purity aluminum ingots, aluminum-manganese master alloy, aluminum-silicon master alloy, pure iron, aluminum-zirconium master alloy, and rare earth master alloy as raw materials. Melt the high-purity aluminum ingots to form an aluminum melt and keep the temperature constant at 750-850℃. Add aluminum-manganese master alloy, aluminum-silicon master alloy, and pure iron respectively, and stir thoroughly until uniform. Add preheated aluminum-zirconium master alloy and rare earth master alloy and keep at 720-800℃ for refining to obtain an alloy melt. The rare earth master alloy is an Er-Al master alloy. S2, the alloy melt is transferred to an atomizing device and atomized and broken into fine droplets in a high-pressure inert atmosphere. After cooling and solidification, fine powder is obtained. S3. The fine powder is dried and stored under an inert atmosphere to obtain aluminum alloy powder.

2. The method for preparing aluminum alloy powder as described in claim 1, characterized in that, The aluminum alloy powder comprises the following components by weight percentage: Mn 0.5–1.5%, Si ≤0.6%, Fe ≤0.7%, Zr 0.15–0.2%, Cu 0.05–0.2%, Mg and / or Zn <0.03%, Er 0.3–0.4%, balance Al.

3. The method for preparing aluminum alloy powder as described in claim 1, characterized in that, The temperature of the alloy melt described in S2 is controlled at 150–300°C above the target alloy liquidus temperature.

4. The method for preparing aluminum alloy powder as described in claim 3, characterized in that, The temperature control range of the alloy melt described in S2 is 850–950°C.

5. The method for preparing aluminum alloy powder as described in claim 1, characterized in that, The pressure at the nozzle of the atomizing device in S2 is 3-8 MPa; The inert atmosphere includes either nitrogen or argon.

6. The method for preparing aluminum alloy powder as described in claim 1, characterized in that, The drying process in S3 includes: drying the fine powder, then screening it to obtain fine powder within a preset particle size range, and then vacuum drying it again.

7. An aluminum alloy powder, characterized in that, It is prepared by the method described in any one of claims 1-6.

8. A method for manufacturing 3003 aluminum alloy additives, characterized in that, The component forming process using laser powder bed melting includes the following steps: S41, preheat the aluminum alloy substrate and uniformly lay a layer of aluminum alloy powder as described in claim 7; S42, selectively scans and melts aluminum alloy powder until the powder is completely melted and forms a metallurgical bond with the underlying layer; S43. After scanning one layer, the forming platform descends by the thickness of powder, lays another layer of aluminum alloy powder, and repeats S42 until the solid part is manufactured. S44. The solid part is removed along with the substrate and subjected to stress-relieving annealing or aging heat treatment to obtain the finished product.

9. The method for manufacturing 3003 aluminum alloy additive manufacturing as described in claim 8, characterized in that, The preheating temperature in S41 is 100-200℃, and the thickness of the aluminum alloy powder is 20-60μm. The scanning speed for selective scanning melting in S42 is 800–2000 mm / s, and the line spacing is 50–130 μm. In S44, stress-relief annealing includes holding at 300–350°C for 1–2 hours, and aging heat treatment includes a first aging stage, which is held at 300–325°C for 4–10 hours.

10. A 3003 aluminum alloy additive manufacturing process, characterized in that, It is prepared by the method described in any one of claims 8 or 9.