Novel FeNi (TiCu) x soft magnetic composite material and preparation method thereof

Abstract

The invention provides a novel FeNi (TiCu) x soft magnetic composite material and a preparation method thereof, and relates to the technical field of metal magnetic materials. The soft magnetic composite material comprises the following chemical components in atomic ratio: 45%-50% of Fe, 45%-50% of Ni, 0-5% of Cu and 0-5% of Ti. By optimizing alloy components, compared with an as-cast Fe-Ni50 material, the mechanical property of the FeNi (TiCu) x soft magnetic composite material manufactured through laser coaxial powder feeding additive manufacturing is improved by 200%-350%, and meanwhile the saturation magnetization intensity and the coercive force are not obviously reduced. The strip produced in a melt-spinning mode is coupled with a heat treatment mode, the magnetic performance and the corrosion resistance of the strip are greatly improved, and meanwhile the strip can be used for a final product only through simple operation such as cutting or laminating. The two forming modes are simple in process, and application of the material in the aspects of magnetic cores, sensors and the like is promoted.

Description

Technical Field

[0001] The present invention relates to the technical field of metal magnetic materials, and in particular to a novel FeNi(TiCu) x Soft magnetic composite material and preparation method thereof. Background Art

[0002] With the rapid development of modern industry, magnetic materials have become essential for a wide range of advanced equipment. Their widespread use, such as in generators, motors, transformers, and various sensors, underscores their importance. As an indispensable component of advanced equipment, magnetic materials have become a critical and irreplaceable strategic resource in today's increasingly scarce world.

[0003] Magnetic materials can be categorized as hard magnetic materials, soft magnetic materials, and magnetostrictive materials. Soft magnetic materials are closely related to our daily lives. They are a class of magnetic materials characterized by low coercivity, high magnetic permeability, and high saturation magnetization. Their core characteristic is their ability to rapidly magnetize and demagnetize in an applied magnetic field while exhibiting extremely low energy loss. Soft magnetic metal alloys are primarily prepared by modifying Fe, Ni, and Co alloys through composition manipulation and element doping. By optimizing the alloy system, the material can possess a combination of high permeability, high resistivity, and low magnetic loss, making it particularly suitable for low- and medium-frequency AC components operating below 100 kHz. Among the many soft magnetic alloys, Permalloy (Fe-Ni alloy) has become the most representative commercial product due to its exceptional comprehensive properties. This alloy system not only exhibits remarkable high permeability but also excellent magnetic response characteristics in weak magnetic fields. With its balanced magnetic-mechanical property profile and outstanding cost-effectiveness, Permalloy maintains a significant market position in the field of electromagnetic functional materials.

[0004] Near-net-shape technology involves directly producing components close to the final product's shape and size through processes such as additive manufacturing, precision casting, powder metallurgy, strip forming, metal injection molding, and isostatic pressing. Its core advantage lies in its "near-net-shape" properties, which significantly reduce material loss (e.g., powder metallurgy raw material utilization exceeds 95%), shorten processing cycles, and possess the ability to form complex structures (such as thin-walled, irregularly shaped, or porous parts) while maintaining microstructural uniformity. It is particularly suitable for materials such as soft magnetic alloys that are sensitive to grain size and phase distribution, effectively avoiding the stress concentration and magnetic property degradation caused by traditional processing.

[0005] Currently, ribbon spinning and additive manufacturing (AM) technologies have become cutting-edge advances in the fabrication of soft magnetic alloys. The latter involves directly forming 20-50 μm amorphous / nanocrystalline ribbons through high-speed cooling of molten alloy, achieving high permeability and low coercivity while suppressing grain boundary formation. AM, on the other hand, constructs complex three-dimensional structures layer by layer through processes such as selective laser melting (SLM), electron beam melting (EBM), and laser coaxial powder deposition (LMD). LMD, with its simultaneous powder feeding and cladding, is particularly well-suited for the precise formation of functionally graded materials or composite soft magnetic components, such as inductor cores with gradient magnetic-thermal properties or heterogeneous integrated electromagnetic components. Both technologies, with machining allowances as low as 0.1 mm, overcome the bottlenecks of traditional multi-step manufacturing. While preserving the material's intrinsic magnetic properties (reducing hysteresis losses by 30%-50%), they also enable high-frequency operating frequencies up to the MHz level. These technologies offer a "design-as-product" integrated manufacturing solution for high-efficiency, energy-efficient electromagnetic devices in applications such as 5G communications and new energy drive motors.

[0006] Fe-Ni-based alloys have both high saturation magnetic induction and relatively high magnetic permeability, and are widely used in fields such as computers, printers, and motors. As magnetic components become increasingly smaller and more complex, traditional casting and machining methods have significant limitations. Furthermore, the overall performance optimization of Fe-Ni-based alloys has not yet been significantly improved, and the defects of traditional preparation processes have not been effectively addressed. To address this situation, research needs to seek solutions from two aspects: preparation process optimization and element composition design. On the one hand, innovative processing technologies are needed to break through the bottlenecks of traditional processes. On the other hand, new component combinations should be explored through multi-element alloying strategies to enhance material performance. Summary of the Invention

[0007] In view of this, the present invention proposes a new FeNi(TiCu) x The soft magnetic composite material and its preparation method enable the alloy material to have better comprehensive mechanical properties, soft magnetic properties and corrosion resistance, and at the same time realize the preparation of integrally formed strips and annular magnetic cores.

[0008] To achieve the above objectives, the present invention provides the following technical solutions:

[0009] The present invention provides a new FeNi(TiCu) x The soft magnetic composite material has the following chemical compositions, calculated by atomic ratio: Fe is 45%-50%, Ni is 45%-50%, Cu is 0-5%, and Ti is 0-5%. Preferably, the contents of Cu and Ti are not 0, and more preferably, the contents of Cu and Ti are both 1.5%.

[0010] The present invention also provides a method for preparing the material, which is prepared by adopting a rapid solidification coupled heat treatment or a laser coaxial powder feeding additive manufacturing method.

[0011] Furthermore, the rapid solidification coupled heat treatment comprises the following steps:

[0012] (1) Preparation of alloy raw materials: Weigh 99.99% pure electrolytic Fe, electrolytic Ni, electrolytic Cu, and pure Ti as raw materials;

[0013] Preferably, the raw materials are accurately weighed using a precision balance (the error is kept within ±0.02 g), and then placed in a vacuum drying oven at 105 ° C for 2-5 hours;

[0014] (2) Alloy smelting: placing the raw materials weighed in step (1) into a vacuum arc melting furnace, filling it with high-purity argon gas for protection and smelting to obtain a sample;

[0015] Preferably, the raw materials weighed in step (1) are placed in a copper crucible of a non-consumable vacuum arc melting furnace, and high vacuum is drawn until the vacuum degree is stable below 5 × 10 -3 Pa, stop vacuuming and fill with high-purity argon gas for protection. The argon protection pressure is -0.05 Pa. The melting current is set to 280 A. Repeat the melting until the alloy has good fluidity.

[0016] (3) Spinning and forming: the sample obtained in step (2) is cut and polished and then placed in a special quartz tube, which is then placed in the induction coil of a single-roll vacuum spinning machine. After high vacuum, it is filled with argon gas and the thin strip is obtained by spinning and forming;

[0017] Preferably, high vacuum is applied to 1×10 -3 Pa, stop vacuuming and fill with argon to -0.05 MPa. The preferred parameters of the belt spinning machine are: copper roller speed of 10-25 m / s, belt spraying pressure of 0.01-0.1 MPa, copper roller distance from quartz tube mouth of 1 mm, and belt thickness of 30-50 μm;

[0018] (4) Heat treatment after stripping: The thin strip is washed with anhydrous ethanol and then blown dry. After being cut, it is placed in a tubular furnace for heat treatment to obtain the soft magnetic composite material.

[0019] Preferably, the heat treatment parameters are: annealing at 800 °C for 2 h in an argon atmosphere, and then cooling to room temperature with the furnace.

[0020] Furthermore, the laser coaxial powder feeding additive manufacturing method includes the following steps:

[0021] (1) Mixed powder preparation: high-purity Fe powder, high-purity Ni powder, high-purity Cu powder, and high-purity Ti powder are weighed and prepared in the required proportion to obtain a mixed powder;

[0022] Preferably, the particle size of the high-purity Fe powder, high-purity Ni powder, high-purity Cu powder, and high-purity Ti powder is 45-150 μm;

[0023] (2) Ball milling mixed powder: ball milling the mixed powder prepared in step (1);

[0024] Preferably, the ball mill speed is 180-220 r / min and the ball milling time is 500-600 min. After mixing, the powder is placed in a vacuum drying oven at 150 ° C for 12 hours;

[0025] (3) Near-net shape preparation: The mixed powder from step (2) is placed in a coaxial powder feeder for additive manufacturing.

[0026] Preferably, before additive manufacturing, use a 45 steel plate as the substrate. After removing the oxide film on the substrate with sandpaper, use anhydrous ethanol to remove oil and dust from the substrate surface. Then, place the substrate in the protective chamber of the laser coaxial powder feeding additive manufacturing equipment. The protective chamber is sealed and filled with argon gas to ensure that the oxygen content is less than 1000 ppm to prevent the formation of an oxide film before and after additive manufacturing.

[0027] Preferably, the parameters of additive manufacturing are: laser power 700-1000 W, laser movement rate 5-10 mm / s, powder feeding rate 0.2-0.5 r / min, and gas flow rate 3-8 L / min.

[0028] The present invention has the following beneficial effects:

[0029] 1. The present invention optimizes the alloy composition to make FeNi(TiCu) manufactured by laser coaxial powder feeding additive manufacturing x Compared with cast Fe-Ni50 materials, the mechanical properties of the soft magnetic composite material are improved by 200%-350%, while the saturation magnetization and coercive force do not decrease significantly.

[0030] 2. The present invention performs heat treatment by evacuating a tube furnace and introducing argon protection, and annealing at 800 ° C for 2 hours to precipitate a second phase so that the alloy strip has good magnetic properties and corrosion resistance.

[0031] 3. The elements described in the present invention are all common metal elements, which are low in cost and easy to manufacture. The ball milling powder mixing and laser coaxial powder feeding processes have the advantages of energy saving and environmental protection.

[0032] 4. The laser coaxial powder feeding additive manufacturing technology adopted in the present invention is a near-net-shape forming process. The formed parts only need simple heat treatment and surface treatment before they can be used, which significantly broadens the application range of the alloy.

[0033] 5. The present invention significantly improves the magnetic properties and corrosion resistance of the strip produced by the strip-spinning method and coupled heat treatment. Furthermore, the strip can be used in the final product through simple operations such as cutting or lamination. This simple process promotes its application in magnetic cores, sensors, and other fields. BRIEF DESCRIPTION OF THE DRAWINGS

[0034] In order to more clearly illustrate the technical solutions in the embodiments of the present invention, the following briefly introduces the drawings required for use in the description of the embodiments. Obviously, the drawings described below are only some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without creative work.

[0035] Figure 1 (a) is the new FeNi(TiCu) of Example 1 of the present invention x Raw material diagram of soft magnetic composite materials, Figure 1 (b) is the new FeNi(TiCu) of Example 2 of the present invention x Morphology of pre-alloyed powder of soft magnetic composite material.

[0036] Figure 2 (a) is the new FeNi(TiCu) of Example 1 of the present invention x Schematic diagram of the stripping of soft magnetic composite materials. Figure 2 (b) is the new FeNi(TiCu) of Example 2 of the present invention x Schematic diagram of laser coaxial powder feeding additive manufacturing of soft magnetic composite materials.

[0037] Figure 3 (a) FeNi(TiCu) is obtained by casting x Microstructure diagram of soft magnetic composite materials, Figure 3 (b) is FeNi(TiCu) of Example 2 of the present invention x Microstructure diagram of soft magnetic composite material.

[0038] Figure 4 The FeNi(TiCu) manufactured by the embodiment 1 and embodiment 2 of the present invention by using belt throwing and laser coaxial powder feeding is x XRD patterns of soft magnetic composite materials.

[0039] Figure 5 It is the new FeNi(TiCu) of Example 2 of the present invention x Stress-strain curves of soft magnetic composites.

[0040] Figure 6 This is the new FeNi(TiCu) of Example 1 of the present invention x Tafel plot of soft magnetic composite materials.

[0041] Figure 7 It is the new FeNi(TiCu) of Example 1 of the present invention x Tafel plot of the matrix in soft magnetic composite materials.

[0042] Figure 8 It is the new FeNi(TiCu) of Example 2 of the present invention x Tafel plot of soft magnetic composite materials.

[0043] Figure 9 It is the new FeNi(TiCu) of Example 2 of the present invention x Hysteresis loop of soft magnetic composite materials.

[0044] Figure 10 It is the new FeNi(TiCu) of Example 1 of the present invention x Actual photo of the soft magnetic composite material strip.

[0045] Figure 11 It is the new FeNi(TiCu) of Example 2 of the present invention x Picture of the finished product of soft magnetic composite materials in actual application.

[0046] Figure 12 It is the new FeNi(TiCu) of Example 2 of the present invention x Cross-sectional view of the finished product of soft magnetic composite material. DETAILED DESCRIPTION

[0047] In order to make the technical problems, technical solutions and advantages to be solved by the present invention clearer, a detailed description will be given below with reference to the accompanying drawings and specific embodiments.

[0048] The embodiment of the present invention provides a new FeNi(TiCu) x The soft magnetic composite material contains the following components in atomic percentage: 48.5% Fe, 48.5% Ni, 1.5% Cu, and 1.5% Ti.

[0049] Example 1

[0050] The above new FeNi(TiCu) x The method for preparing a strip of soft magnetic composite material is carried out according to the following steps:

[0051] Step 1: Weigh the metal particles according to the required alloy ratio using a precision balance, and then place them in a vacuum drying oven at 105°C for 3 hours. The purity of the electrolytic Fe used in the present invention is 99.99%, the purity of the electrolytic Ni is 99.99%, the purity of the electrolytic Cu is 99.99%, and the purity of the high-purity Ti is 99.99%. The use of electrolytic metal particles can effectively reduce the impact of impurity elements on the refined alloy. The dried raw materials are placed in a copper crucible of a non-consumable vacuum arc melting furnace and high vacuum is applied. When the vacuum degree is stable below 5×10 -3 Pa, stop vacuuming and fill with high-purity argon for protection. The argon protection pressure is -0.05 Pa. The melting current is set to 280 A. Repeat the melting until the alloy has good fluidity.

[0052] Step 2: To ensure the integrity of the spinning belt, the mass of the sample added each time should not exceed 7.5 g. To adapt to the size of the special quartz tube, the alloy in step 2 needs to be further processed and cut into 10 mm × 10 mm × 7 mm blocks. Before spinning the belt, the surface of the alloy needs to be polished to remove the surface cutting marks. After cleaning with anhydrous ethanol, it is quickly blown dry to avoid the formation of an oxide film on the surface that may affect the experimental results.

[0053] Step 3: Use Figure 2 (a) The strip forming is carried out by the method shown in FIG. The processed alloy pieces are placed in a special quartz tube, and then the special quartz tube is placed in the induction coil of the single roller vacuum strip forming machine, and the vacuum is drawn to 1×10 -3 Pa, the vacuum was stopped and argon was filled to -0.05 MPa. The parameters for strip preparation were: copper roller speed 12 m / s, injection pressure 0.02 MPa, nozzle distance 1 mm from the copper roller, and the material was rapidly solidified by quenching the strip to obtain a strip sample.

[0054] Step 4: Cut the strip sample into segments, clean and dry them with anhydrous ethanol, and place them in a crucible. Place the crucible in a tube furnace and introduce argon to expel air from the furnace. Heat treat at 800°C for 2 hours, then cool the furnace. After cooling, clean, dry, and seal.

[0055] Example 2

[0056] The above new FeNi(TiCu) x The method for preparing alloys by laser coaxial powder feeding additive manufacturing of soft magnetic composite materials is implemented according to the following steps:

[0057] 1. Mix the metal powders according to the appropriate ratio and place them in a ball mill for milling. The milling parameters are as follows: 200 rpm, 550 min. After mixing, dry the powders in a vacuum drying oven at 150°C for 12 h.

[0058] 2. Before laser coaxial powder feeding additive manufacturing, use 60-240 grit sandpaper to remove the oxide film on the surface of the 45 steel plate, and use anhydrous ethanol to remove oil and dust on the surface of the steel plate. After cleaning, place it in a protective cabin in time, seal the protective cabin, fill it with argon, and ensure that the oxygen content is less than 500 ppm to avoid the formation of oxide film before and after additive manufacturing.

[0059] 3. Adoption Figure 2 (b) Laser coaxial powder feeding additive manufacturing is performed as shown, and the corresponding parameters of additive manufacturing are set: laser power 800 W, laser movement speed 6 mm / s, powder feeding rate 0.3 r / min, and gas flow rate 5 L / min.

[0060] Example 3

[0061] In this embodiment, the preparation method and process parameters are the same as those in Example 2, except that the proportions of the raw material formula are different, containing the following atomic percentages: Fe is 45%, Ni is 45%, Cu is 5%, and Ti is 5%.

[0062] Comparative Example 1

[0063] In this comparative example, the preparation method and process parameters are the same as those in Example 2, except that the types of raw materials are different, and the components contain the following atomic percentages: Fe is 40%, Ni is 40%, Si is 5%, and B is 15%.

[0064] Comparative Example 2

[0065] In this comparative example, the preparation method and the types of elements are the same as those in Example 1, except that the process parameters are different and the copper roller rotation speed is 15 m / s.

[0066] Table 1 Test results of examples and comparative examples

[0067]

[0068] The test results of the above embodiments and comparative examples are shown in Table 1, which illustrate the new FeNi(TiCu) x Soft magnetic composite materials have good magnetic properties and corrosion resistance. If the element types or preparation process parameters are changed, the product performance will be reduced to varying degrees.

[0069] The new FeNi(TiCu) prepared by the above two methods x Soft magnetic composites were tested using equipment including an X-ray diffractometer, metallographic microscope, scanning electron microscope, electrochemical corrosion workstation, and vibrating sample magnetometer. Tensile specimens, magnetic property specimens, and electrochemical corrosion specimens were cut in the longitudinal direction.

[0070] Figure 1 (a) is a raw material diagram for the strip forming process in Example 1. Figure 1 (b) is the SEM morphology of the pre-alloyed powder after ball milling and mixing in Example 2. It can be seen that the mixed powder particles are spherical, which helps to improve the density of the additive alloy.

[0071] Figure 2 (a) is the new FeNi(TiCu) of Example 1 of the present invention x Schematic diagram of the stripping of soft magnetic composite materials. Figure 2 (b) is the new FeNi(TiCu) of Example 2 of the present invention x Schematic diagram of laser coaxial powder feeding additive manufacturing of soft magnetic composite materials.

[0072] Figure 3 (a) is the alloy Fe obtained by casting method 48.5 Ni 48.5 Cu 1.5 Ti 1.5 The microstructure diagram of the preparation process is the same as that of Example 1, with the difference that suction casting is used instead of belt casting. Specifically, the smelted ingot is fixed to the suction casting mold, the melting current is set to 300A, and the suction casting button is clicked after the ingot is completely fluidized. Figure 3 (b) is the new alloy Fe of Example 2 of the present invention 48.5 Ni 48.5 Cu 1.5 Ti 1.5 Microstructure diagram of . Figure 3 (a) and Figure 3 (b) It can be seen that the alloy grain size after laser additive manufacturing is evenly distributed, with no obvious defects such as pores or cracks in the deposition direction, and the grain size is smaller than that of the cast alloy.

[0073] Figure 4 For the new Fe in Example 1 and Example 2 48.5 Ni 48.5 Cu 1.5 Ti 1.5 Alloy, and the XRD diffraction patterns of the matrix Fe-50Ni prepared by two methods. 48.5 Ni 48.5 Cu 1.5 Ti 1.5 The increased intensity of the diffraction peak of the (111) crystal plane in the FCC phase of the material indicates that the crystal structure is more directional and ordered, and the crystal structure is more complete. The introduction of Cu and Ti elements improves the temperature gradient and solidification rate during the alloy solidification process. The fluidity of the molten pool during alloy solidification is improved, which promotes element diffusion, improves wettability, and reduces surface tension.

[0074] Figure 5 The tensile stress-strain curve of Example 2 shows that the new alloy (Fe 48.5 Ni 48.5 Cu 1.5 Ti 1.5 ) has a room temperature tensile strength of 434 MPa, which is 203% higher than that of cast Fe-50Ni (143 MPa) and 11.9% higher than that of additively manufactured Fe-50Ni (388 MPa). The elongation after fracture reaches 52.3%.

[0075] Figure 6 The Tafel curve of Fe-50Ni in Example 1 shows that the corrosion current density (3.241×10 -6 A / cm 2 ) is higher than the corrosion current density of cast Fe-50Ni (8.114×10 -6 A / cm 2 ) was reduced by 60%, showing good corrosion resistance.

[0076] Figure 7 The Tafel curve of Example 1 shows that the corrosion current density (6.977×10 -7 A / cm 2 ) is compared with the corrosion current density of the substrate Fe-50Ni (3.241×10 -6 A / cm 2 ) is reduced by an order of magnitude, showing good corrosion resistance.

[0077] Figure 8 The Tafel curve of Example 2 shows that the corrosion current density of the sample after laser additive manufacturing (3.382×10 -6 A / cm 2 ) is compared with the corrosion current density of the as-cast substrate Fe-50Ni (1.410×10 -5 A / cm 2 ) is reduced by an order of magnitude, and the corrosion current density of Fe-50Ni as additively manufactured is 4.022×10 -6 A / cm 2 ) was reduced by 16%, showing good corrosion resistance.

[0078] Figure 9 This is the hysteresis loop of Example 2. It can be seen from the figure that the new FeNi(TiCu) xThe saturation magnetization intensity of the soft magnetic composite material is 322 emu / g and the coercive force is 6.34 Oe, which does not significantly reduce the soft magnetic properties compared with Fe-50Ni.

[0079] Figure 10 This is the finished product of the spinning tape in Example 1. The surface of the spinning tape is smooth and flat, the thickness is 100 μm, the width is 2 mm, and the length of a single tape is 500 mm.

[0080] Figure 11 This is a picture of the finished product of the actual application of Example 2.

[0081] Figure 12 This is a 3 / 4 cross-sectional view of the finished product of Example 2. As can be seen from the figure, there are no obvious pores or defects on the cross-sectional view, and the product is compactly formed.

[0082] The above description is merely a specific embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any modifications or substitutions that can be easily conceived by a person skilled in the art within the technical scope disclosed in the present invention should be included in the scope of protection of the present invention. Therefore, the scope of protection of the present invention should be based on the scope of protection of the claims.

Claims

1. A new type of FeNi(TiCu) x A soft magnetic composite material, characterized in that Calculated by atomic ratio, its chemical composition is: Fe 45%-50%, Ni 45%-50%, Cu 0-5%, and Ti 0-5%.

2. The method for preparing the material according to claim 1, characterized in that: It is prepared by rapid solidification coupled heat treatment or laser coaxial powder feeding additive manufacturing method.

3. The method according to claim 2, characterized in that The rapid solidification coupled heat treatment comprises the following steps: (1) Preparation of alloy raw materials: Weigh 99.99% pure electrolytic Fe, electrolytic Ni, electrolytic Cu, and pure Ti as raw materials; (2) Alloy smelting: placing the raw materials weighed in step (1) into a vacuum arc melting furnace, filling it with high-purity argon gas for protection and smelting to obtain a sample; (3) Spinning and forming: the sample obtained in step (2) is cut and polished and then placed in a special quartz tube, which is then placed in the induction coil of a single-roll vacuum spinning machine. After high vacuum, it is filled with argon gas and the thin strip is obtained by spinning and forming; (4) Heat treatment after stripping: The thin strip is washed with anhydrous ethanol and then blown dry. After being cut, it is placed in a tubular furnace for heat treatment to obtain the soft magnetic composite material.

4. The method according to claim 3, characterized in that In step (1), after weighing the alloy raw materials, the raw materials are placed in a vacuum drying oven at 105 °C for 2-5 hours.

5. The method according to claim 3, characterized in that In step (2), the raw materials weighed in step (1) are placed in a copper crucible of a non-consumable vacuum arc melting furnace and evacuated until the vacuum degree is stable below 5 × 10 -3 Pa, stop vacuuming and fill with high-purity argon gas for protection. The argon protection pressure is -0.05 Pa. The melting current is set to 280 A. The melting is repeated until the alloy has good fluidity.

6. The method according to claim 3, characterized in that In step (3), high vacuum was applied to 1×10 -3 Pa, stop vacuuming and fill with argon to -0.05 MPa; the parameters of the belt spinning machine are: copper roller speed is 10-25 m / s, belt spraying pressure is 0.01-0.1 MPa, the distance between the copper roller and the quartz tube mouth is 1 mm, and the thickness of the thin belt is 30-50 μm.

7. The method according to claim 3, characterized in that In step (4), the heat treatment parameters are: annealing at 800 °C for 2 h in an argon atmosphere, and then cooling to room temperature with the furnace.

8. The method according to claim 2, characterized in that The laser coaxial powder feeding additive manufacturing method comprises the following steps: (1) Mixed powder preparation: high-purity Fe powder, high-purity Ni powder, high-purity Cu powder, and high-purity Ti powder are weighed and prepared in the required proportion to obtain a mixed powder; (2) Ball milling mixed powder: ball milling the mixed powder prepared in step (1); (3) Near-net shape preparation: The mixed powder from step (2) is placed in a coaxial powder feeder for additive manufacturing.

9. The method according to claim 8, characterized in that In step (1), the particle size of the high-purity Fe powder, high-purity Ni powder, high-purity Cu powder, and high-purity Ti powder is 45-150 μm; In step (2), the ball mill speed is 180-220 r / min, and the ball milling time is 500-600 min; after mixing, the powder is placed in a vacuum drying oven at 150 °C and dried for 12 h.

10. The method according to claim 8, characterized in that In step (3), the parameters of additive manufacturing are: laser power 700-1000 W, laser movement rate 5-10 mm / s, powder feeding rate 0.2-0.5 r / min, and gas flow rate 3-8 L / min.

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