A multi-element high-abundance rare earth permanent magnet material, a preparation method thereof and an application thereof

Abstract

This invention relates to a multi-element high-abundance rare-earth permanent magnet material, its preparation method, and its application. The permanent magnet material is composed of the following atomic percentages: (Ce+La+Y) 15%-20%, Fe 70-80%, B 5-8%, Co 0.5-3%, Zr 0.1-2%; wherein the rare earth components are Ce 10-13.5%, La 1-4%, and Y 1-5%. The preparation method includes the following steps: preparing an alloy ingot of CeLaYFeCoZrB atomic percentage by arc melting of the alloy raw materials; crushing the alloy ingot and preparing alloy strips using a melt rapid quenching method; and vacuum annealing the quenched alloy strips in a magnetic field environment. Compared with the prior art, this invention uses only the high-abundance rare earth elements cerium, lanthanum, and yttrium as rare earth components, significantly improving the comprehensive magnetic properties of the high-abundance rare-earth permanent magnet material.

Description

Technical Field

[0001] This invention relates to the field of rare earth permanent magnet alloy technology, and in particular to a multi-element high-abundance rare earth permanent magnet material, its preparation method and application. Background Technology

[0002] Rare earth permanent magnet materials possess excellent properties such as high coercivity, high remanence, and high energy product, making them a core material in fields with high demand for permanent magnet materials, such as aerospace, advanced electronic equipment, medical equipment, and new energy vehicles. In the field of rare earth permanent magnet materials, high-abundance rare earth permanent magnet materials have attracted widespread attention due to their significantly lower raw material costs compared to traditional neodymium iron boron permanent magnet materials, indicating promising development prospects.

[0003] Ce, a high-abundance rare earth element, is currently abundant and inexpensive in the market, making it a primary target for development among high-abundance rare earth elements. However, the overall magnetic properties of Ce-Fe-B series alloys are limited by Ce₂Fe. 14 The intrinsic magnetic properties of boron and the inevitable presence of the paramagnetic CeFe2 phase during preparation. Some studies have used Ce to partially replace Nd in neodymium iron boron rare earth permanent magnets to control performance loss (Pathak AK et al. Advanced Materials, 2015, 27: 2663-2667), but this method offers limited cost reduction. Herbst's team used melt quenching technology to study this series of alloys and successfully prepared Ce-containing alloys. 17 Fe 78 The B6 alloy (Herbst et al. J. Appl. Phys., 2012, 111:07A718) achieves a remanence of 4.9 kG and a maximum energy product of 4.1 MGOe without significantly reducing the coercivity of cerium-iron-boron alloys, thus improving the overall magnetic properties of the alloy. However, it still lags far behind neodymium-iron-boron permanent magnet alloys.

[0004] CN110534279A discloses a pure, high-abundance rare-earth Ce,La,Y-based multi-component nanocrystalline permanent magnet alloy. By controlling the interaction of Ce, La, and Y, a high-abundance rare-earth Ce,La,Y-based multi-component nanocrystalline permanent magnet alloy without Nd, Pr, Dy, and Tb was prepared. However, this alloy still struggles to balance coercivity and maximum energy product; increasing the maximum energy product significantly reduces coercivity. Therefore, the development of novel high-abundance rare-earth permanent magnet alloys with excellent comprehensive magnetic properties remains a priority. Summary of the Invention

[0005] The purpose of this invention is to overcome the defects of the prior art and provide a multi-element high-abundance rare earth permanent magnet material, its preparation method and application.

[0006] The objective of this invention can be achieved through the following technical solutions: The first aspect of this invention provides a multi-element high-abundance rare-earth permanent magnet material, wherein the permanent magnet material is composed of the following atomic percentages: (Ce+La+Y) 15%-20%, Fe 70-80%, B 5-8%, Co 0.5-3%, Zr 0.1-2%; wherein, the rare earth portion comprises Ce 10-13.5%, La 1-4%, and Y 1-5%.

[0007] Furthermore, the permanent magnet material contains hard magnetic Ce2Fe 14 The relative volume fraction of the B phase is not less than 90%, and the relative volume fraction of the CeFe2 phase is not more than 10%.

[0008] Furthermore, compared to CN110534279A, the multi-element high-abundance rare-earth permanent magnet material of the present invention achieves a high maximum magnetic energy product while maintaining the coercivity without decreasing by introducing Co and Zr to exert a synergistic effect.

[0009] A second aspect of this invention provides a method for preparing a multi-element high-abundance rare-earth permanent magnet material, the method comprising the following steps: S1: Prepare CeLaYFeCoZrB alloy ingots by electric arc melting according to atomic percentages of each alloy raw material; S2: After crushing the alloy ingot obtained from S1, quenched alloy strips are prepared by melt rapid quenching method; S3: The quenched alloy strips obtained in S2 are vacuum annealed in a magnetic field environment to finally obtain the multi-element high-abundance rare earth permanent magnet material.

[0010] Furthermore, in step S1, the entire arc melting process is carried out in an argon atmosphere of 0.11-0.12 MPa.

[0011] Furthermore, in step S1, the current for arc melting is 100-150 A.

[0012] Furthermore, in step S1, the time for a single melting process is 10-15 seconds.

[0013] Furthermore, in step S1, the electric arc melting is repeated 4-6 times.

[0014] Furthermore, in step S2, the rapid quenching of the melt is carried out entirely in an argon atmosphere of 0.04-0.08 MPa, preferably 0.06 MPa.

[0015] Furthermore, the chamber is evacuated to a level below 5 × 10⁻⁶ before the melt is rapidly quenched. -3 Pa, and argon gas is introduced as a protective gas.

[0016] Furthermore, in step S2, the melt temperature of the rapid melt quenching is 1600-1700 K, and the magnitude of the induced current is 100-180 A.

[0017] Furthermore, in step S2, the injection pressure difference of the melt rapid quenching method is 0.04-0.06 MPa, preferably 0.05 MPa, and the injection time is 1-2 s.

[0018] Furthermore, in step S2, the rotational speed of the copper roller in the melt rapid quenching method is 12-18 m / s, preferably 15 m / s.

[0019] Furthermore, in step S2, the width of the quenched alloy strip is 1-3 mm and the thickness is 20-40 μm.

[0020] Furthermore, in step S3, the vacuum degree of the vacuum annealing is lower than 5 × 10⁻⁶. -3 Pa.

[0021] Furthermore, in step S3, the heating rate of the vacuum annealing is 4-6 K / min.

[0022] Furthermore, in step S3, the holding temperature of the vacuum annealing is 10-20 K below the Curie temperature, and the holding time is 0.25-0.75 h.

[0023] Furthermore, in step S3, the strength of the magnetic field is 0.5-1.5 T, preferably 1 T.

[0024] Furthermore, in step S3, the long end of the quenched alloy strip is parallel to the direction of the applied magnetic field.

[0025] The third aspect of this invention provides the application of multi-element high-abundance rare earth permanent magnet materials in the preparation of permanent magnet motors, automotive auxiliary systems, and electronic devices.

[0026] Compared with the prior art, the present invention has the following technical advantages: (1) This invention uses high-abundance and low-cost rare earth elements La / Ce / Y, and utilizes the interaction of three high-abundance rare earth elements, cerium, lanthanum and yttrium, to significantly improve the magnetic phase Ce2Fe in high-abundance rare earth permanent magnet alloys. 14 The volume fraction of B phase increases the remanence and maximum energy product of the alloy, resulting in high-abundance rare-earth permanent magnet materials with excellent comprehensive magnetic properties and a cost far lower than that of NdFeB permanent magnet materials.

[0027] (2) The multi-element high-abundance rare earth permanent magnet material of the present invention, after magnetic field heat treatment, further optimizes the microstructure through magnetic field heat treatment, and the hard magnetic Ce2Fe in the alloy. 14The relative volume fraction of the B phase was further increased, thereby further improving the remanence and maximum magnetic energy product of the alloy.

[0028] (3) The preparation method of the multi-element high-abundance rare earth permanent magnet material of the present invention is simple, the preparation cost is low, it has good repeatability, and it is widely applicable. It can be further processed into other materials such as adhesive magnets, and has good application prospects in the fields of low-end permanent magnet motors, automotive auxiliary systems, and electronic devices. Attached Figure Description

[0029] Figure 1 Ce, as described in Embodiment 1 of the present invention 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 Thermogravimetric curve of B6 alloy strip.

[0030] Figure 2 The images show the XRD patterns of the alloy strips of Example 1 and Comparative Example 1 before magnetic field heat treatment.

[0031] Figure 3 Ce in Embodiments 1-3 of the present invention 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 XRD patterns of B6 alloy strips before and after magnetic field heat treatment.

[0032] Figure 4 Ce, as described in Embodiment 1 of the present invention 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 Elemental distribution diagram of B6 alloy strips before and after magnetic field heat treatment.

[0033] Figure 5 The image shows the demagnetization curves of the alloy strips of Embodiment 1 and Comparative Example 1 before magnetic field heat treatment.

[0034] Figure 6 Ce in Embodiments 1-3 of the present invention 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 Demagnetization curves of B6 alloy strips before and after magnetic field heat treatment, compared with Comparative Example 2. Detailed Implementation

[0035] The present invention will now be described in detail with reference to the accompanying drawings and specific embodiments. These embodiments are based on the technical solution of the present invention and provide detailed implementation methods and specific operating procedures. However, the scope of protection of the present invention is not limited to the following embodiments.

[0036] Unless otherwise specified, the reagents, methods, instruments, and equipment used in this invention are conventional in the art. Unless otherwise specified, the reagents and materials used in the following examples are all commercially available.

[0037] The purity of Ce, La, Fe, Co, and Zr is ≥99.5%, and FeB is industrial grade.

[0038] Example 1: This embodiment provides a high-performance multi-element, high-abundance rare-earth permanent magnet material, wherein the alloy composition of the high-abundance rare-earth permanent magnet material is Ce. 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 B6 (in atomic percentage).

[0039] The specific preparation method of the high-abundance rare-earth permanent magnet material in this embodiment is as follows: S1. Preparation of the master alloy: The required raw materials Ce, La, Fe, Co, Zr, and FeB are stacked in a melting furnace and evacuated to a vacuum of 3 × 10⁻⁶. -3 The alloy ingot was smelted under an argon atmosphere with a smelting current of 120 A and a single smelting time of 12 s. The smelting was repeated 4 times to obtain an alloy ingot with uniform composition.

[0040] S2. Preparation of quenched alloy strips: The alloy ingot is placed in a quartz tube and vacuumed to 3×10⁻⁶. -3 Under an argon atmosphere, the casting process was carried out by spinning the strip. The melting current was adjusted to 150 A, and the ingot was completely melted by heating with an induction coil to a temperature of 1623 K. The molten metal was then sprayed from a quartz tube nozzle onto the surface of a rotating copper roller using a pressure difference, initially obtaining a crystalline alloy strip with uniform thickness. The rotation speed of the copper roller was 15 m / s, the chamber pressure was 0.06 MPa, the spray pressure difference was 0.05 MPa, and the spray time was 1.5 s.

[0041] S3. Preparation of Alloy Strips for Magnetic Field Heat Treatment: The alloy strips obtained in S2 were placed in a magnetic field annealing furnace with the long end of the strip parallel to the direction of the applied magnetic field for magnetic field heat treatment. The magnetic field heat treatment was carried out at 18 K below its Curie temperature (i.e., 443 K), with a magnetic field strength of 1 T, a heating rate of 5 K / min, and a holding time of 0.5 h. A magnetic field and a vacuum (3 × 10⁻⁶ K / min) were applied throughout the entire magnetic field heat treatment process (including heating, holding, and cooling). -3 After cooling to room temperature, the sample is removed, and the final high-performance multi-element high-abundance rare earth permanent magnet material is obtained.

[0042] This embodiment uses thermogravimetric analysis (TGA) to test the alloy strip obtained after S2 strip spinning. For example... Figure 1 From the TG curve, we can see that Ce 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 Curie temperature T of B6 alloy strip C Since the temperature is 461 K, the temperature for magnetic field heat treatment is 443 K.

[0043] Example 2: This embodiment provides a high-performance multi-element, high-abundance rare-earth permanent magnet material, and the specific preparation method is the same as in Example 1. The difference is that the alloy magnetic field heat treatment in step S3 is carried out at 28 K (i.e., 433 K) below its Curie temperature.

[0044] Example 3: This embodiment provides a high-performance multi-element, high-abundance rare-earth permanent magnet material, and the specific preparation method is the same as in Example 1. The difference is that the alloy magnetic field heat treatment in step S3 is carried out at 8 K (i.e., 453 K) below its Curie temperature.

[0045] Comparative Example 1: This comparative example provides a permanent magnet material that uses only a single high-abundance rare earth element, cerium, and its alloy composition is Ce. 17 Fe 76.5 Co1Zr 0.5 B6 (in atomic percentage), the preparation steps prior to magnetic field heat treatment are described in Example 1.

[0046] Comparative Example 2: This comparative example provides a high-abundance rare-earth permanent magnet material with an alloy composition of Ce. 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 B6 (in atomic percentage), the specific preparation method is described in Example 1.

[0047] The difference from Example 1 is that the temperature of the magnetic field heat treatment in step S3 is 2 K above the Curie temperature (i.e., 463 K), and other parameters are the same as in Example 1.

[0048] Figure 2 The alloy strip Ce in Example 1 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 B6 and the alloy strip Ce in Comparative Example 1 17 Fe 76.5 Co1Zr 0.5XRD pattern of B6 before magnetic field heat treatment, where Example 1 is represented by CeLaY and Comparative Example 1 is represented by Ce only. Figure 2 The XRD results show that using multiple rare earth elements Ce, La, and Y to replace single Ce element in high-abundance rare earth permanent magnet materials can significantly reduce the relative volume fraction of CeFe2 phase in the alloy.

[0049] Ce in Examples 1-3 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 XRD patterns of B6 alloy strips before and after magnetic field heat treatment are shown below. Figure 3 As shown, the initial sample is shown before heat treatment, and the samples after heat treatment are represented by 433K×1T (Example 2), 443K×1T (Example 1), and 453K×1T (Example 3). It can be observed that after magnetic field heat treatment, Ce... 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 The relative volume fraction of the CeFe2 phase in the B6 alloy will further decrease.

[0050] Ce in Example 1 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 The elemental distribution diagrams of B6 alloy strips before and after magnetic field heat treatment are as follows: Figure 4 As shown. According to Figure 4 The elemental distribution diagram of element a shows that the three elements exhibit different segregation patterns in the alloy. Ce forms a hard magnetic 2:14:1 phase and a paramagnetic 1:2 phase, while La tends to move away from the 2:14:1 phase, and Y tends to enter the 2:14:1 phase. According to... Figure 4 The elemental distribution diagram of b shows that the enrichment of La element decreases after magnetic field heat treatment at 443 K. The main reason for this is that the magnetic field heat treatment causes the unstable La-rich phase to decompose, and the La element diffuses and reacts with the B-rich grain boundaries to form a new 2:14:1 phase. This can, to some extent, increase the relative content of the hard magnetic 2:14:1 phase and further improve the remanence and maximum magnetic energy product of the alloy.

[0051] Based on the successful preparation of the above permanent magnet alloy strip, the present invention further uses a vibrating sample magnetometer (VSM) to test the magnetic properties of the alloy strip before and after the magnetic field heat treatment.

[0052] The test conditions were: an external magnetic field of 1.8 T was applied at room temperature, and the test type was hysteresis loop. The overall magnetic properties of the alloy were analyzed by examining parameters such as coercivity, remanence, maximum energy product, and saturation magnetization.

[0053] The alloy strip Ce in Example 1 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 B6, compared with the alloy strip Ce in Comparative Example 1 17 Fe 76.5 Co1Zr 0.5 The demagnetization curve of B6 before magnetic field heat treatment is as follows: Figure 5 As shown, Example 1 is represented by CeLaY, and Comparative Example 1 is represented by Ce only. The demagnetization curves show that the Ce in Comparative Example 1... 17 Fe 76.5 Co1Zr 0.5 The alloy remanence of B6 alloy strips is B. r =0.41 T, maximum magnetic energy product (BH) max = 26.1 kJ / m 3 Ce in Example 1 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 The alloy remanence of B6 alloy strips is B. r =0.62 T, maximum magnetic energy product (BH) max =57.9 kJ / m 3 The remanence and maximum energy product were increased by 51.2% and 121.8% respectively compared to the sample in Comparative Example 1. This shows that the performance of multi-element rare earth elements is significantly improved compared to that of single rare earth elements. Therefore, the synergistic effect of using appropriate amounts of Ce, La, and Y, three high-abundance rare earth elements, in high-abundance rare earth permanent magnet materials can significantly improve the magnetic properties of alloy strips.

[0054] Furthermore, Ce in Examples 1-3 11.5 La 2.5 Y3Fe 76.5 Co1Zr 0.5 The demagnetization curves of alloy B6 before and after magnetic field heat treatment, compared with those of Comparative Example 2, are shown below. Figure 6 As shown, the initial sample is shown before heat treatment, and the samples after heat treatment are represented by 433K×1T (Example 2), 443K×1T (Example 1), 453K×1T (Example 3), and 463K×1T (Comparative Example 2). The demagnetization curves show that the initial Ce in the quenched state... 11.5 La 2.5 Y3Fe 76.5 Co1Zr0.5 The remanence of B6 alloy B r = 0.62 T, coercivity H ci = 485.9 kA / m, maximum energy product (BH) max = 57.9 kJ / m 3 Coercivity H ci = 487.8 kA / m, remanence B of the alloy in Example 1 after magnetic field heat treatment r = 0.66 T, maximum energy product (BH) max = 62.7 kJ / m 3 Compared with the alloy sample without magnetic field heat treatment, the coercivity remained stable, while the remanence and maximum energy product of the alloy increased by 6.5% and 8.3%, respectively. Therefore, it can be concluded that the multi-element high-abundance rare-earth permanent magnet material of the present invention can be further significantly improved by subjecting it to magnetic field heat treatment at a certain temperature below the Curie temperature Tc of the alloy.

[0055] When high-abundance rare-earth permanent magnet materials are at the Curie temperature T of the alloy C When heat-treated at the above levels (e.g., 463K), the remanence B of the alloy after magnetic field heat treatment is... r = 0.63 T, maximum energy product (BH) max = 53.6 kJ / m 3 The magnetic properties then begin to decline. This may be because when the magnetic field heat treatment temperature exceeds the Curie temperature of the alloy, the magnetic field has less impact on the alloy's magnetic properties. Furthermore, the high temperature induces grain coarsening, resulting in a certain degree of decrease in the alloy's magnetic property parameters. Therefore, the multi-element high-abundance rare-earth permanent magnet magnetic material of this invention needs to undergo magnetic field heat treatment within a suitable range below its alloy Curie temperature. Magnetic field heat treatment temperatures above the alloy Curie temperature will actually inhibit the improvement of the alloy's magnetic properties.

[0056] The magnetic properties of the multi-element high-abundance rare-earth permanent magnet alloy of the present invention are superior to those of existing high-abundance rare-earth nanocrystalline permanent magnet alloys, as shown in Table 1 below: Table 1 Comparison of the properties of various permanent magnet alloys The comparisons mentioned are as follows: Comparative Example 3: Zhang K H, Mao Z X, Li H N, Xia Y B, Tan X H, Xu H. A novel grainrefinement of Ce-Fe-B magnets induced by magnetic field annealing. J. Magn.Magn. Mater., 2024, 611: 172607。

[0057] Comparative Example 4: Zhang K H, Zhu Y M, Li F, Tan X H, Xu H. Synergistic effect of Lasubstitution and magnetic field annealing on CeFe2 suppression andperformance enhancement in Ce-Fe-B magnets. J. Mater. Sci. Technol., 2026,252: 116-126。

[0058] Comparative Example 5: Liao X F, Zhang J S, He J Y, Fan W B, Yu H Y, Zhong X C, Liu Z W.Development of cost-effective nanocrystalline multi-component (Ce,La,Y)-Fe-Bpermanent magnetic alloys containing no critical rare earth elements of Dy,Tb, Pr and Nd. J. Mater. Sci. Technol., 2021, 76: 215-221。

[0059] Comparative Example 6: Liao X F, Zhang J S, Li W, Khan A J, Yu H Y, Zhong X C, Liu Z W. Performance improvement and element segregation behavior in Y substituted nanocrystalline (La,Ce)-Fe-B permanent magnetic alloys without critical RE elements. J. Alloys Compd., 2020, 834: 155226。

[0060] Comparative Example 7: Grigoras M, Lostun M, Borza F, Porcescu M, Lupu N. The effect of the Mo addition on the magnetic properties and phase constituents of the Ce-(FeCo)–B ribbons. Intermetallics, 2022, 141: 107425。

[0061] Comparative Example 8: Rehman S U, Li Y, Jing, X, et al. Effects of Ge doping on structure, magnetic properties and intergranular exchange coupling of melt-spun CeFeB alloys[J]. Journal of Magnetism and Magnetic Materials, 2024, 593: 171464。

[0062] Comparative Example 9: Lian L Y, Zhang X W, Liu Y, Li J, Wang R Q. Improvement of the microstructure and magnetic properties of (La,Ce)-Fe-B nanocrystalline ribbons. Chin. Phys. B, 2023, 32(7): 077501。

[0063] Comparative Example 10: Zhou C, Pan MX, Wu Q, Yang H F. Improvement of magnetic properties for Ti doped Ce-Fe-B alloys: Effectively inhibiting CeFe2 phase formation. J.Magn. Magn. Mater., 2020, 502: 166564.

[0064] Comparative Example 11: Zeng WJ, Yang HF, Wu Q, Pan MX, Yu NJ, Gu Y, Ge H L. Effect of the Ga Content on the Magnetic Properties and Microstructure of the Nanocrystalline Ce-Fe-B Alloys. J. Supercond. Nov. Magn., 2021, 34: 1225-1229.

[0065] Comparative Example 12: Zhang JS, Li W, Liao XF, Yu HY, Zhao LZ, Zeng HX, Peng DR, LiuZ W. Improving the hard magnetic properties by intragrain pinning for Tadoped nanocrystalline Ce-Fe-B alloys. J. Mater. Sci. Technol., 2019, 35:1877-1885.

[0066] In summary, the multi-element high-abundance rare-earth permanent magnet material of this invention uses only high-abundance and inexpensive rare-earth elements. The cost of the resulting high-abundance rare-earth permanent magnet material is much lower than that of neodymium iron boron permanent magnet material, while maintaining high comprehensive magnetic performance. Its cost-effectiveness is better than that of traditional neodymium iron boron permanent magnet material, and it has good application prospects in low-to-mid-end permanent magnet motors, automotive auxiliary systems, electronic devices and other fields.

[0067] The above description of the embodiments is provided to enable those skilled in the art to understand and use the invention. It will be apparent to those skilled in the art that various modifications can be made to these embodiments, and the general principles described herein can be applied to other embodiments without inventive effort. Therefore, the present invention is not limited to the above embodiments, and any improvements and modifications made by those skilled in the art based on the disclosure of the present invention without departing from the scope of the invention should be within the protection scope of the present invention.

Claims

1. A multi-element, high-abundance rare-earth permanent magnet material, characterized in that, The permanent magnet material is composed of the following atomic percentages: (Ce+La+Y) 15%-20%, Fe 70-80%, B 5-8%, Co 0.5-3%, Zr 0.1-2%; The rare earth components are Ce 10-13.5%, La 1-4%, and Y 1-5%.

2. A method for preparing the multi-element high-abundance rare-earth permanent magnet material according to claim 1, characterized in that, The preparation method includes the following steps: S1: Prepare CeLaYFeCoZrB alloy ingots by electric arc melting according to atomic percentages of each alloy raw material; S2: After crushing the alloy ingot obtained from S1, quenched alloy strips are prepared by melt rapid quenching method; S3: The quenched alloy strips obtained in S2 are vacuum annealed in a magnetic field environment to finally obtain the multi-element high-abundance rare earth permanent magnet material.

3. The method for preparing multi-element high-abundance rare-earth permanent magnet materials according to claim 2, characterized in that, In step S1, the entire arc melting process is carried out in an argon atmosphere of 0.11-0.12 MPa.

4. The method for preparing multi-element high-abundance rare-earth permanent magnet materials according to claim 2, characterized in that, In step S1, the current of the electric arc melting is 100-150 A, the melting time for a single melting is 10-15 s, and the melting is repeated 4-6 times.

5. The method for preparing multi-element high-abundance rare-earth permanent magnet materials according to claim 2, characterized in that, In step S2, the rapid quenching of the melt is carried out entirely in an argon atmosphere of 0.04-0.08 MPa.

6. The method for preparing multi-element high-abundance rare-earth permanent magnet material according to claim 2, characterized in that, In step S2, the melt temperature of the melt rapid quenching is 1600-1700 K, and the magnitude of the induced current is 100-180 A; The injection pressure difference for the rapid melt quenching method is 0.04-0.06 MPa, and the injection time is 1-2 s. The rotational speed of the copper roller in the melt rapid quenching method is 12-18 m / s.

7. The method for preparing multi-element high-abundance rare-earth permanent magnet material according to claim 2, characterized in that, In step S2, the width of the quenched alloy strip is 1-3 mm and the thickness is 20-40 μm.

8. The method for preparing multi-element high-abundance rare-earth permanent magnet materials according to claim 2, characterized in that, In step S3, the vacuum degree of the vacuum annealing is lower than 5 × 10⁻⁶. -3 Pa; The vacuum annealing process involves a heating rate of 4-6 K / min, a holding temperature of 10-20 K below the Curie temperature, and a holding time of 0.25-0.75 h.

9. The method for preparing multi-element high-abundance rare-earth permanent magnet material according to claim 2, characterized in that, In step S3, the strength of the magnetic field is 0.5-1.5 T; The long end of the quenched alloy strip is parallel to the direction of the applied magnetic field.

10. The application of the multi-element high-abundance rare earth permanent magnet material as described in claim 1 in the preparation of permanent magnet motors, automotive auxiliary systems, and electronic devices.

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