CN117352249A - MnBiCu permanent magnet alloy with ultralow temperature and high coercivity and preparation method thereof - Google Patents
MnBiCu permanent magnet alloy with ultralow temperature and high coercivity and preparation method thereof Download PDFInfo
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- CN117352249A CN117352249A CN202311472471.8A CN202311472471A CN117352249A CN 117352249 A CN117352249 A CN 117352249A CN 202311472471 A CN202311472471 A CN 202311472471A CN 117352249 A CN117352249 A CN 117352249A
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- 239000000956 alloy Substances 0.000 title claims abstract description 75
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 74
- 238000002360 preparation method Methods 0.000 title claims abstract description 20
- 239000000203 mixture Substances 0.000 claims abstract description 6
- 239000010949 copper Substances 0.000 claims description 38
- 239000011572 manganese Substances 0.000 claims description 35
- 239000000843 powder Substances 0.000 claims description 28
- 239000002994 raw material Substances 0.000 claims description 19
- 238000000034 method Methods 0.000 claims description 16
- 238000010438 heat treatment Methods 0.000 claims description 15
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 12
- 229910052802 copper Inorganic materials 0.000 claims description 12
- 238000002844 melting Methods 0.000 claims description 10
- 230000008018 melting Effects 0.000 claims description 9
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 230000006698 induction Effects 0.000 claims description 6
- 229910052797 bismuth Inorganic materials 0.000 claims description 5
- 238000001816 cooling Methods 0.000 claims description 5
- 239000002245 particle Substances 0.000 claims description 5
- 238000012216 screening Methods 0.000 claims description 4
- 229910052582 BN Inorganic materials 0.000 claims description 3
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 3
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 claims description 3
- 238000000227 grinding Methods 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 2
- 239000011261 inert gas Substances 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims description 2
- 238000004321 preservation Methods 0.000 claims description 2
- 238000005086 pumping Methods 0.000 claims 1
- 238000012360 testing method Methods 0.000 abstract description 8
- 150000002736 metal compounds Chemical class 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 17
- 238000002441 X-ray diffraction Methods 0.000 description 9
- KYAZRUPZRJALEP-UHFFFAOYSA-N bismuth manganese Chemical compound [Mn].[Bi] KYAZRUPZRJALEP-UHFFFAOYSA-N 0.000 description 8
- 229910001152 Bi alloy Inorganic materials 0.000 description 7
- 229910016629 MnBi Inorganic materials 0.000 description 7
- 230000005291 magnetic effect Effects 0.000 description 7
- 230000008569 process Effects 0.000 description 6
- 230000005294 ferromagnetic effect Effects 0.000 description 5
- 230000005415 magnetization Effects 0.000 description 5
- 229910052761 rare earth metal Inorganic materials 0.000 description 5
- 150000002910 rare earth metals Chemical class 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 238000003723 Smelting Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 230000005298 paramagnetic effect Effects 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- 229910000881 Cu alloy Inorganic materials 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 238000000498 ball milling Methods 0.000 description 2
- 238000001938 differential scanning calorimetry curve Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 238000005481 NMR spectroscopy Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000010431 corundum Substances 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000002059 diagnostic imaging Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000010348 incorporation Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910001004 magnetic alloy Inorganic materials 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002074 melt spinning Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000004570 mortar (masonry) Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000010453 quartz Substances 0.000 description 1
- 238000005057 refrigeration Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
Abstract
The invention discloses an ultralow-temperature high-coercivity MnBiCu permanent magnet alloy and a preparation method thereof, wherein the composition of the MnBiCu permanent magnet alloy is Mn 55 Bi 45‑x Cu x X is more than or equal to 1 and less than or equal to 4. The invention generates a metal compound Mn by doping proper amount of Cu element 0.9 Bi 0.1 Cu and increase Mn by adjusting doping amount 0.9 Bi 0.1 The Cu purity is greatly improved after the test, and the low-temperature high coercivity of the alloy material is found; the preparation process is simple and easy to implement, and has a very low-temperature application prospect.
Description
Technical Field
The invention belongs to the technical field of permanent magnet materials, and particularly relates to a MnBiCu permanent magnet alloy with ultralow temperature and high coercivity and a preparation method thereof. The permanent magnet alloy prepared by the method has excellent magnetic performance, and the permanent magnet material with excellent and stable performance can be prepared by simple smelting reaction, heat treatment process and ball milling.
Background
High performance permanent magnets are of great interest due to the strong demand for electromagnetic devices, sensors and motor applications. Rare earth based permanent magnets and ferrites have been widely put to practical use, however, ferrite has a low energy product due to low iron content and ferromagnetic behavior, and at the same time, high performance rare earth permanent magnets have limited cost effectiveness due to limited supply of rare earth elements and high price. Therefore, the search for low cost permanent magnets with properties intermediate between ferrite and rare earth permanent magnets has been the subject of extensive research. Manganese bismuth alloys with Low Temperature Phases (LTP) are considered promising candidate materials to fill the gap between ferrite and rare earth permanent magnets due to their high magnetic susceptibility, high Magnetocrystalline Anisotropy (MA), high curie temperature, and especially positive temperature coefficient of coercivity, which makes LTP-MnBi very promising for high temperature applications.
So far, the preparation and the performance of the manganese bismuth alloy are greatly improved. The manganese bismuth powder prepared by the low-energy ball milling method obtains room-temperature coercivity of 1.9T; a high purity alpha-MnBi phase having a saturation magnetization value of (78 emu/g) was prepared by a melt spinning method. The research shows that due to the fact that the content of the ferromagnetic LTP-MnBi is increased, the saturated magnetic susceptibility can be improved by proper Sn and Zr substitution, and B, C, fe, ga is beneficial to greatly improving the coercive force. However, manganese bismuth alloy with high coercivity at ultralow temperature has not been reported, which limits the application of manganese bismuth alloy in ultralow temperature environment
Therefore, it is of great importance to develop a manganese bismuth alloy that can still have a high coercivity in an ultra-low temperature environment.
Disclosure of Invention
In view of the above, the present invention aims to provide a MnBiCu permanent magnet alloy with ultralow temperature and high coercivity, and a preparation method thereof, wherein the prepared MnBiCu permanent magnet alloy has high coercivity and local positive coercivity temperature coefficient at low temperature, and has low-temperature application capability
Specifically, the invention provides a MnBiCu permanent magnet alloy with ultralow temperature and high coercivity, which is characterized in that the composition of the MnBiCu permanent magnet alloy is Mn 55 Bi 45-x Cu x Wherein x is more than or equal to 1 and less than or equal to 4.
In some embodiments of the invention, 3.ltoreq.x.ltoreq.4.
The invention also provides a preparation method of the MnBiCu permanent magnet alloy with ultralow temperature and high coercivity, which comprises the following steps:
s1 according to the nominal molecular formula Mn 55 Bi 45-x Cu x Preparing raw materials, wherein x is more than or equal to 0 and less than or equal to 4;
s2, fully melting the raw materials prepared in the step S1 under the protection of inert gas, and cooling to obtain an alloy ingot;
s3: performing heat treatment on the alloy ingot obtained in the step S2 to obtain a heat-treated alloy ingot;
s4: and (3) crushing and screening the alloy ingot obtained in the step (S3) to obtain the MnBiCu permanent magnet alloy with ultralow temperature and high coercivity.
In some embodiments of the invention, the mid-melting of step S2 is accomplished in a vacuum induction melting furnace.
In some embodiments of the present invention, the specific operation steps of the step S2 are: placing the raw materials configured in the step S1 into a crucible of a vacuum induction melting furnace, and vacuumizing the melting furnace to 10 -3 Under Pa, high-purity argon is introduced, and then the raw materials are heated to be fully melted and poured into a water-cooled copper mold to prepare an alloy ingot.
In some embodiments of the invention, the crucible is made of high purity boron nitride.
In some embodiments of the invention, the number of remelting in step S3 is 2 or more.
In some embodiments of the present invention, the raw materials in step S1 are high purity manganese flakes, bismuth ingots, and copper particles, all having a purity of not less than 99.97%.
In some embodiments of the present invention, the specific operation steps of step S4 are: crushing and grinding the alloy ingot prepared in the step S3 into powder, and screening by a mesh screen to obtain MnBiCu permanent magnet alloy powder.
In some embodiments of the invention, the mesh screen has a mesh size of 1000 mesh; the particle size of the MnBiCu permanent magnet alloy powder is not more than 13 mu m.
Compared with the prior art, the MnBiCu permanent magnet alloy with ultralow temperature and high coercivity provided by the invention is prepared by doping proper content of copper into the manganese-bismuth alloy, and the addition of copper causes the structural transformation of the manganese-bismuth alloy, so that a new intermetallic phase Mn is formed 0.9 Cu 0.1 Bi, mn with Curie temperature of about 162K 0.9 Cu 0.1 The Bi phase has paramagnetic properties at room temperature, but has high coercivity and a local positive coercivity temperature coefficient at low temperatures, indicating that it has low temperaturesThe potential of application can be widely applied to magnet refrigeration, experimental physics, medical imaging, space science and nuclear magnetic resonance spectroscopy. In addition, the preparation method provided by the invention is simple and easy to implement, has mild conditions, is favorable for reducing the production cost, and has great commercial application prospect.
Drawings
In order to more clearly illustrate the embodiments of the invention or the technical solutions in the prior art, the drawings that are required in the embodiments or the description of the prior art will be briefly described, it being obvious that the drawings in the following description are only some embodiments of the invention, and that other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
FIG. 1 is a non-isothermal DSC curve of the transformation of an alloy ingot after heat treatment during the preparation of examples 1-4 and comparative examples;
FIG. 2 is an XRD pattern of alloy ingots prepared in examples 1 to 4 and comparative example step 2;
FIG. 3 is an XRD pattern of the permanent magnet alloy powders prepared in examples 1 to 4 and comparative example;
FIG. 4 is a graph showing the change in saturation magnetization of the permanent magnet alloy powder prepared in step (4) in examples 1 to 4 or comparative example with an increase in temperature;
fig. 5 is a graph showing the coercive force of the permanent magnetic alloy powders prepared in step (4) in examples 1 to 4 or comparative example as a function of temperature.
Detailed Description
The technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it should be apparent that the described embodiments are only some of the embodiments of the present invention and should not be used to limit the protection scope of the present invention. All other embodiments, which can be made by those skilled in the art based on the embodiments of the present invention without making any inventive effort, are intended to fall within the scope of the present invention.
Example 1: mn (Mn) 55 Bi 44 Cu 1 Preparation of permanent magnet alloy powder
Mn 55 Bi 44 Cu 1 The preparation method of the permanent magnet alloy powder comprises the following steps:
(1) The elementary substances of three elements of manganese, bismuth and copper with purity not lower than 99.97 percent are Mn according to nominal compositions 55 Bi 44 Cu 1 Preparing an alloy raw material, wherein 8wt.% of Mn is added in consideration of volatilization of Mn element;
(2) Sequentially placing the alloy raw materials prepared in the step (1) into a boron nitride crucible, placing the crucible into an induction coil in an induction smelting furnace, and vacuumizing a chamber of the smelting furnace to enable the vacuum degree to reach 10 -3 Pa, closing a vacuum pump, filling a proper amount of high-purity argon into the cavity, slowly lifting the induced current until the alloy is completely melted, preserving heat for 10min, pouring into a water-cooled copper mold, and taking out an alloy ingot after full cooling;
(3) Placing the alloy ingot obtained in the step (2) into a corundum crucible, placing into a vacuum tube furnace for heat treatment, and vacuumizing by a molecular pump to ensure that the vacuum degree in the quartz tube reaches 10 -5 Pa, then heating from room temperature to 300 ℃ at a heating rate of 5 ℃/min, preserving heat for 24 hours, and slowly cooling along with a furnace after the heat preservation is finished to obtain an alloy ingot after heat treatment;
(4) Crushing the alloy ingot obtained in the step (3) after heat treatment, grinding into powder by using a mortar, and then passing through a 1000-mesh stainless steel screen to obtain Mn with uniform particle size of not more than 13 mu m 55 Bi 44 Cu 1 Alloy powder.
Example 2: mn (Mn) 55 Bi 43 Cu 2 Preparation of permanent magnet alloy powder
Mn (Mn) 55 Bi 43 Cu 2 The process for producing permanent magnet alloy powder was substantially the same as in example 1, except that the raw material was added in an amount corresponding to Mn 55 Bi 43 Cu 2 Is a ratio match of (c).
Example 3: mn (Mn) 55 Bi 42 Cu 3 Preparation of permanent magnet alloy powder
Mn (Mn) 55 Bi 42 Cu 3 Process for the preparation of permanent magnet alloy powder, which is substantially the same as in example 1The difference is the addition amount of the raw materials, the addition amount of the raw materials and Mn 55 Bi 42 Cu 3 Is a ratio match of (c).
Example 4: mn (Mn) 55 Bi 41 Cu 4 Preparation of permanent magnet alloy powder
Mn (Mn) 55 Bi 41 Cu 4 The process for producing permanent magnet alloy powder was substantially the same as in example 1, except that the raw material was added in an amount corresponding to Mn 55 Bi 41 Cu 4 Is a ratio match of (c).
Comparative example: mn (Mn) 55 Bi 45 Preparation of permanent magnet alloy powder
Mn (Mn) 55 Bi 45 The process for producing permanent magnet alloy powder was substantially the same as in example 1, except that the raw material was added in an amount and that the raw material did not contain Cu, and that the raw material was added in an amount and Mn 55 Bi 45 Is a ratio match of (c).
Example 5: thermal transformation behavior test of alloy ingots after heat treatment during preparation of examples 1 to 4 and comparative example
The thermal phase transition behavior of the alloy ingots after heat treatment in the preparation process of examples 1 to 4 and comparative example was tested by using a Differential Scanning Calorimeter (DSC), and the test results are shown in FIG. 1.
As shown in fig. 1, the DSC curve of the comparative example shows three distinct endothermic peaks, corresponding to three phase transition processes. As the example doping copper increased, the second endotherm gradually decreased from 628K (comparative example) to 607.6K (example 1) and further to 603K (example 2); furthermore, in example 4, the second peak completely disappeared. Thus, this suggests that the transition of the magnetic phase from the Ferromagnetic (FM) state to the Paramagnetic (PM) state gradually weakens until completely disappearing due to the reduced content of ferromagnetic LTP-MnBi.
Example 6: x-ray diffraction analysis (XRD) test of permanent magnet alloy powders prepared in examples 1 to 4 and comparative example
The microstructure, phase composition and lattice parameters of the as-cast alloy ingots prepared in examples 1 to 4 and comparative example step 2 were measured by X-ray diffraction analysis (XRD), and the test results are shown in fig. 3.
The microstructure, phase composition and lattice parameter of the permanent magnet alloy powders prepared in examples 1 to 4 and comparative example were measured by X-ray diffraction analysis (XRD), and the test results are shown in fig. 3.
As can be seen from FIGS. 2 and 3, the alloy powder prepared in the comparative example is composed mainly of LTP-MnBi phase and contains a small amount of residual Mn and Bi phases. In the examples after the incorporation of copper at low concentrations, a new intermetallic Mn was detected 0.9 Cu 0.1 The diffraction peak of Bi indicates that the addition of copper induces phase transformation of the Mn-Bi-Cu alloy. XRD patterns clearly show the MnBi phase and Mn in the examples 0.9 Cu 0.1 The positions of the different peaks of the Bi phase. Mn as copper concentration increases 0.9 Cu 0.1 The Bi peak becomes more prominent.
Example 7: magnetic property test of permanent magnet alloy powders prepared in examples 1 to 4 or comparative example in step (4) at low temperature to room temperature
In order to more intuitively reflect the influence of Cu doping at low temperature, the magnetic properties of the permanent magnet alloy powders obtained in examples 1 to 4 or step (4) of comparative example were measured using a Physical Properties Measurement System (PPMS), and the test results are shown in fig. 4 and 5, respectively.
FIGS. 4 and 5 show the temperature dependence of magnetization and coercive force of MnBi-Cu alloys under a 1T magnetic field at a temperature in the range of 10 to 350K, respectively. For the undoped Cu comparative example, both magnetization and coercivity changed around 120K. At this temperature, the easy axis of the MnBi lattice is flipped from the ab-plane to the c-axis, transitioning from planar anisotropy to uniaxial anisotropy. Therefore, magnetization starts to decrease and coercive force increases. Due to Mn 0.9 Bi 0.1 The permanent magnet alloy powders prepared in examples 1-4 exhibit a specific Mn over a temperature range of 10K to 200K in the presence of Cu 55 Bi 45 Higher coercivity.
The foregoing is only a specific embodiment of the invention to enable those skilled in the art to understand or practice the invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown and described herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (10)
1. A MnBiCu permanent magnet alloy with ultralow temperature and high coercivity is characterized in that the composition of the MnBiCu permanent magnet alloy is Mn 55 Bi 45-x Cu x Wherein x is more than or equal to 1 and less than or equal to 4.
2. The MnBiCu permanent magnet alloy with ultralow temperature and high coercivity according to claim 1, wherein x is more than or equal to 3 and less than or equal to 4.
3. A preparation method of a MnBiCu permanent magnet alloy with ultralow temperature and high coercivity is characterized by comprising the steps of,
the method comprises the following steps:
s1: according to the nominal molecular formula Mn 55 Bi 45-x Cu x Preparing raw materials, wherein x is more than or equal to 0 and less than or equal to 4;
s2: fully melting the raw materials prepared in the step S1 under the protection of inert gas, and cooling to obtain an alloy ingot;
s3: performing heat treatment on the alloy ingot obtained in the step S2 to obtain a heat-treated alloy ingot;
s4: and (3) crushing and screening the alloy ingot obtained in the step (S3) to obtain the MnBiCu permanent magnet alloy with ultralow temperature and high coercivity.
4. The method for preparing a MnBiCu permanent magnet alloy with ultra-low temperature and high coercivity according to claim 3, wherein the medium melting in the step S2 is completed in a vacuum induction melting furnace.
5. The method for preparing a MnBiCu permanent magnet alloy with ultra-low temperature and high coercivity according to claim 4, characterized in that the steps are as followsThe specific operation steps of the step S2 are as follows: placing the raw materials configured in the step S1 into a crucible of a vacuum induction melting furnace, and vacuumizing the melting furnace to 10 -3 Under Pa, high-purity argon is introduced, and then the raw materials are heated to be fully melted and poured into a water-cooled copper mold to prepare an alloy ingot.
6. The method for preparing a MnBiCu permanent magnet alloy with ultralow temperature and high coercivity according to claim 5, wherein the crucible is made of high-purity boron nitride.
7. The method for preparing the MnBiCu permanent magnet alloy with ultralow temperature and high coercivity according to claim 3, wherein the specific operation steps of the heat treatment in the step S3 are as follows: placing the alloy ingot prepared in the step S2 into a crucible, and then pumping the crucible to a vacuum degree of 10 by a molecular pump -5 And (3) high vacuum of Pa, then heating from room temperature to 300 ℃ at a heating rate of 5 ℃/min, preserving heat for 24 hours, and slowly cooling along with a furnace after the heat preservation is finished to obtain the alloy ingot after heat treatment.
8. The method for preparing the MnBiCu permanent magnet alloy with ultralow temperature and high coercivity according to claim 3, wherein the raw materials in the step S1 are high-purity manganese flakes, bismuth ingots and copper particles with purity not lower than 99.97%.
9. The method for preparing the MnBiCu permanent magnet alloy with the ultralow temperature and high coercivity according to claim 3, wherein the specific operation steps of the step S4 are as follows: crushing and grinding the alloy ingot prepared in the step S3 into powder, and screening by a mesh screen to obtain MnBiCu permanent magnet alloy powder.
10. The method for producing a MnBiCu permanent magnet alloy with ultra-low temperature and high coercivity according to claim 9, in which the mesh number of the mesh screen is 1000 mesh; the particle size of the MnBiCu permanent magnet alloy powder is not more than 13 mu m.
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| CN202311472471.8A CN117352249A (en) | 2023-11-07 | 2023-11-07 | MnBiCu permanent magnet alloy with ultralow temperature and high coercivity and preparation method thereof |
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