CN102496437B - Anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material and preparation method thereof - Google Patents
Anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material and preparation method thereof Download PDFInfo
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- 238000002360 preparation method Methods 0.000 title claims abstract description 16
- 239000000463 material Substances 0.000 title claims abstract description 12
- 229910001172 neodymium magnet Inorganic materials 0.000 title claims abstract description 12
- QJVKUMXDEUEQLH-UHFFFAOYSA-N [B].[Fe].[Nd] Chemical compound [B].[Fe].[Nd] QJVKUMXDEUEQLH-UHFFFAOYSA-N 0.000 title claims abstract description 11
- 239000002159 nanocrystal Substances 0.000 title claims abstract description 9
- 239000012071 phase Substances 0.000 claims abstract description 52
- 239000007791 liquid phase Substances 0.000 claims abstract description 33
- 229910052684 Cerium Inorganic materials 0.000 claims abstract description 5
- 229910052692 Dysprosium Inorganic materials 0.000 claims abstract description 5
- 229910002546 FeCo Inorganic materials 0.000 claims abstract description 5
- 229910052688 Gadolinium Inorganic materials 0.000 claims abstract description 5
- 229910052777 Praseodymium Inorganic materials 0.000 claims abstract description 5
- 229910052771 Terbium Inorganic materials 0.000 claims abstract description 5
- 229910052746 lanthanum Inorganic materials 0.000 claims abstract description 5
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 5
- 238000007731 hot pressing Methods 0.000 claims description 34
- 239000000843 powder Substances 0.000 claims description 31
- RZJQYRCNDBMIAG-UHFFFAOYSA-N [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] Chemical class [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] RZJQYRCNDBMIAG-UHFFFAOYSA-N 0.000 claims description 20
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 20
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 16
- 230000005389 magnetism Effects 0.000 claims description 15
- 239000000696 magnetic material Substances 0.000 claims description 13
- 238000002844 melting Methods 0.000 claims description 11
- 230000008018 melting Effects 0.000 claims description 11
- 238000000034 method Methods 0.000 claims description 11
- 239000013078 crystal Substances 0.000 claims description 10
- 238000009792 diffusion process Methods 0.000 claims description 10
- 239000007789 gas Substances 0.000 claims description 10
- 239000002245 particle Substances 0.000 claims description 9
- 238000010791 quenching Methods 0.000 claims description 9
- 230000000171 quenching effect Effects 0.000 claims description 9
- 229910052786 argon Inorganic materials 0.000 claims description 8
- 230000001681 protective effect Effects 0.000 claims description 8
- 239000011812 mixed powder Substances 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 6
- 238000012545 processing Methods 0.000 claims description 4
- 229910052779 Neodymium Inorganic materials 0.000 claims description 2
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 229910052733 gallium Inorganic materials 0.000 claims description 2
- 230000014759 maintenance of location Effects 0.000 claims description 2
- 229910052718 tin Inorganic materials 0.000 claims description 2
- 229910052723 transition metal Inorganic materials 0.000 claims description 2
- 230000002708 enhancing effect Effects 0.000 abstract 1
- 150000002910 rare earth metals Chemical class 0.000 description 18
- 239000002114 nanocomposite Substances 0.000 description 17
- 238000005516 engineering process Methods 0.000 description 11
- 229910052774 Proactinium Inorganic materials 0.000 description 8
- 238000001816 cooling Methods 0.000 description 8
- 238000007578 melt-quenching technique Methods 0.000 description 8
- 238000010792 warming Methods 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 239000006247 magnetic powder Substances 0.000 description 4
- 238000000280 densification Methods 0.000 description 3
- 239000012530 fluid Substances 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 241000167880 Hirundinidae Species 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000010008 shearing Methods 0.000 description 1
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Abstract
The invention relates to an anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material which is characterized by comprising a nanocrystal-structure hard magnetic phase and a soft magnetic phase, wherein the hard magnetic phase is a (Nd,R)2Fe17B phase, and R is selected from at least one of La, Ce, Pr, Gd, Tb and Dy; and the soft magnetic phase is at least one of alpha-Fe alpha-FeCo or Fe3B. The invention also discloses a preparation method of the permanent-magnet material. Compared with the prior art, the permanent-magnet material has the following advantages: due to the introduction of the soft magnetic phase, the coercive force of the nano complex-phase magnet is far lower than that of the single hard magnetic phase magnet, and the liquid phase is diffused into the nano complex-phase magnet and positioned at the grain boundary, thereby obviously enhancing the coercive force of the magnet.
Description
Technical field
The present invention relates to a kind of permanent magnetic material, the invention still further relates to the preparation method of this permanent magnetic material.
Background technology
From third generation rare earth permanent-magnetic material-Nd eighties in last century
2fe
14since B finds, the researchers of countries in the world carry on further investigation, expect to find to have the new rare-earth permanent magnetic material of excellent permanent magnetism performance.The Development of Novel high performance permanent magnetic materials that is found to be of Nanocomposite permanent magnetic material has been opened up new thinking, has important scientific meaning and huge economic worth.Isotropic nanocrystalline complex phase permanent material is taking the high magnetic energy rapidly quenched magnetic powder of Magnequench exploitation as representative at present, form with bonded permanent magnet is able to extensive use, because this magnetic shows magnetic isotropy, and after making bonded permanent magnet, density is not high, cause magnet magnetic property not high, well below the anisotropic sintered Nd-Fe-B permanent magnetic material of densification.Macroscopic view magnetic anisotropy is to obtain the necessary condition of high permanent magnetism performance, how to realize that the magnetic anisotropy of Nanocomposite rare earth permanent-magnetic material is current to remain physically and technical huge challenge.
Hot pressing/thermal deformation technology is to prepare the effective means of block theoretical density anisotropy nanometer permanent magnet.It is generally acknowledged, due to tetragonal Nd
2fe
14the anisotropy of B crystal grain modulus of elasticity and strain energy, dissolving-precipitation-diffusion-the creep process occurring during high rare-earth content neodymium iron boron hot-fluid becomes, make magnet form flake crystalline structure, obtain strong magnetic anisotropy, the existence of rich rare earth liquid phase obtains texture to high rare-earth content magnet hot pressing/thermal deformation and has important function.In order to introduce soft/Hard Magnetic multiphase structure in anisotropy hot pressing/heat distortion magnet, Dayton university of the U.S., the researchers of the research institutions such as Pukyong national university of Korea S and Delaware university of the U.S. adopt the modes such as rich rare earth quenched powder mixes with poor rare earth quenched powder, the interpolation of soft magnetism phase particle, plated film to attempt, and make some progress.Micro-Structure Analysis shows, macroscopic anisotropy comes from the formation of the Hard Magnetic phase texture that has the generation of rich rare earth liquid phase region, the orientation and poor rare earth region does not wherein deform substantially, so wish obtains the good degree of orientation, the content of soft magnetism phase is extremely restricted, and this is unfavorable for the performance of the advantage of soft/Hard Magnetic built-up magnet.
Do not rely on rich rare earth liquid phase, the research of directly content of rare earth being carried out to hot pressing/thermal deformation lower than the nanocrystalline complex phase magnet just dividing shows, magnet also can obtain anisotropy to a certain degree.Now, Hard Magnetic phase texture derives from the shearing deformation occurring under pressure-acting, i.e. Nd
2fe
14the anisotropy of B crystal grain modulus of elasticity causes slippage and the rotation of crystal face, realizes the texture of crystal grain.But the degree of orientation of magnet and magnetic property are starkly lower than high rare earth hot pressing/thermal deformation Nd
2fe
14the level of B magnet, and along with soft magnetism phase content increases, the degree of orientation and the magnetic property of magnet decline rapidly, need higher pressure simultaneously, to process conditions and equipment requirement harshness.In the recent period, the domestic researcher of University On The Mountain Of Swallows separates out nanocrystalline multiphase structure by the lower noncrystal substrate hot-fluid change of strong pressure (～310MPa) effect, forming core preferentially occurs simultaneously realizes the texture of Hard Magnetic phase.This noncrystal substrate that utilizes is realized anisotropy, and keeps the research of soft or hard magnetic phase crystal grain boundary coherence still in the initial exploration stage, and magnet magnetic property and the single-phase hot pressing/heat distortion magnet of preparation still have larger gap at present.
Introduce the rich rare earth liquid phase of appropriate low melting point if adopt the method for crystal boundary diffusion in the nanocrystalline complex phase magnet of poor rare earth, can realize soft or hard Magnetic Phase and liquid phase coexists, meet the needed deformation orientation condition of hot pressing/thermal deformation technique, prepare the block magnet of fine and close anisotropy Nanocomposite.The present invention proposes a kind of the diffuse into rapidly quenched magnetic powder of low melting point liquid phase alloy along crystal boundary that utilize, to improve the deformation orientation ability of poor rare-earth nano-crystal complex phase fast quenching magnetic in thermal deformation process, thereby preparation has the brilliant complex phase permanent material of the densification lumpy nanometer of macroscopic anisotropy.
Summary of the invention
Technical problem to be solved by this invention is the anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material that a kind of high-coercive force is provided for the above-mentioned state of the art.
Another technical problem to be solved by this invention is to provide a kind of preparation method that can significantly improve the coercitive anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material of magnet.
The present invention solves the problems of the technologies described above adopted technical scheme: a kind of anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material, it is characterized in that this permanent magnetic material includes hard magnetic phase and the soft magnetism phase of nanocrystalline structure, aforesaid hard magnetic is (Nd, R) mutually
2fe
14b phase, wherein R is at least one being selected from La, Ce, Pr, Gd, Tb and Dy, aforesaid soft magnetism is α-Fe, α-FeCo or Fe mutually
3at least one in B, soft magnetism phase is 2～40% with the mutually shared volume ratio scope of permanent magnetism.
A preparation method for anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material, comprises the steps:
1. utilize rapid quenching technique to prepare Nd
2fe
14b/ α-Fe base, Nd
2fe
14b/Fe
3b base or Nd
2fe
14b/ α-FeCo base nanometer crystal complex phase quick quenching band, and be broken into particle diameter and be no more than 300
μthe principal phase powder of m;
2. prepare fusing point taking rare earth element and magnesium-yttrium-transition metal as composition lower than the low melting point liquid phase alloy RM of 800 DEG C, and be broken into particle diameter and be no more than the liquid phase powder of 50 μ m, or this low melting point liquid phase alloy is made to target, R is wherein at least one being selected from La, Ce, Pr, Nd, Gd, Tb and Dy, and M is at least one in Al, Cu, Ga, Co, Sn;
3. liquid phase alloy is mixed with principal phase powder, or liquid phase alloy is evenly coated on to principal phase powder surface, obtain mixed-powder;
4. mixed-powder is carried out under vacuum or protective atmosphere to hot pressing block blank, or mixed-powder is first carried out to high temperature heat diffusion treatment carry out again hot pressing block blank in vacuum or under protective atmosphere;
5. block blank is carried out to thermal deformation orientation and prepare anisotropy magnet, or hot pressing blank is first carried out to high temperature heat diffusion treatment under vacuum or protective atmosphere and carry out again thermal deformation and prepare anisotropy magnet.
Further, described liquid phase alloy and main-phase alloy mass ratio range are 0.5:99.5～15:85.
Further, the hot pressing condition of step in is 4. as follows: 500～850 DEG C of hot pressing temperatures, and pressure 100～500MPa, vacuum degree is higher than 1 × 10
-2under Pa condition, carry out hot pressing block blank.
Further, the high temperature heat diffusion treatment condition of step in is 4. as follows: temperature 500-850 DEG C, and temperature retention time 30～120 minutes, while processing under vacuum condition, vacuum degree is higher than 1 × 10
-2pa, while processing under protective atmosphere environment, protecting gas is argon gas, air pressure is lower than 0.2Mpa.
Further, the condition of the thermal deformation orientation preparation of step in is 5. as follows: 700～850 DEG C of heat distortion temperatures, and pressure 100～500MPa, vacuum degree is higher than 1 × 10
-2pa, or after vacuumizing, be filled with protection gas argon pressure approximately 10
2pa.
Compared with prior art, the invention has the advantages that: generally speaking, only tens microns of business neodymium iron boron rapidly quenched magnetic powder thickness, carry out liquid phase diffusion to quenched powder, can be easy to realize sufficient diffusion effect; Spread on the basis can soft or hard Magnetic Phase coexisting by liquid phase, introduce sufficient liquid phase alloy, meet hot pressing/hot-fluid and become the required liquid phase of orientation, obtain the texture of hard magnetic phase, realize the macroscopic anisotropy of magnet; Utilize magnet prepared by hot pressing/thermal deformation technique to have fine and close structure, density is high, and has anisotropy, and its magnetic property is far above current Nanocomposite bonded permanent magnet; Because magnet has soft/hard magnetic phase nanometer coupled structure, rare earth consumption is few, is conducive to the saving of rare earth resources; Due to the introducing of soft magnetism phase, the coercive force of nanocomposite magnets, far below the coercive force of single hard magnetic phase magnet, diffuses in nanocomposite magnets by liquid phase and is positioned at grain boundaries, can significantly improve magnet coercive force.
Brief description of the drawings
Fig. 1 is the electronic scanning displaing micro picture of the final magnet section of preparation in embodiment 2.
Embodiment
Below in conjunction with accompanying drawing, embodiment is described in further detail the present invention.
Embodiment 1:
1, utilize fast melt-quenching technology to prepare Nanocomposite quick quenching band, and be broken into the powder of particle diameter 150 μ m, alloying component is Nd21.452Pr0.42Fe74.294Co0.674B0.98Al0.479Cu0.11Nb1.591 (quality percentage composition);
2, utilize fast melt-quenching technology to prepare fusing point lower than the low melting point Nd90Cu10 liquid phase alloy of 800 DEG C, be broken into the powder of 50 μ m;
3, multiphase alloy powder is mixed with 95:5 mass ratio with liquid phase alloy powder;
4, powder being placed in to mould puts into vacuum hotpressing stove and is evacuated to 6 × 10
-3after Pa, be warming up to 700 DEG C, pressurization 270MPa, pressurize is cooling taking-up after 1 minute;
5, hot pressing blank being placed in to mould puts into vacuum hotpressing stove and is evacuated to 6 × 10
-3after Pa, be filled with 10
2pa argon gas, is warming up to 850 DEG C, pressurization 10
5the MPa orientation that deforms, pressurize is cooling taking-up after 0.5 minute, obtains anisotropy Nanocomposite permanent magnetic material.
Embodiment 2:
1, utilize fast melt-quenching technology to prepare Nanocomposite quick quenching band, and be broken into the powder of particle diameter 150 μ m, alloying component is Nd21.452Pr0.42Fe74.294Co0.674B0.98Al0.479Cu0.11Nb1.591 (quality percentage composition);
2, utilize fast melt-quenching technology to prepare fusing point lower than the low melting point Nd90Cu10 liquid phase alloy of 800 DEG C, be broken into the powder of 50 μ m;
3, multiphase alloy powder is mixed with 92:8 mass ratio with liquid phase alloy powder;
4, powder being placed in to mould puts into vacuum hotpressing stove and is evacuated to 6 × 10
-3after Pa, be warming up to 700 DEG C, pressurization 270MPa, pressurize is cooling taking-up after 40 seconds;
5, hot pressing blank being placed in to mould puts into vacuum hotpressing stove and is evacuated to 6 × 10
-3after Pa, be filled with 10
2pa argon gas, is warming up to 850 DEG C, pressurization 10
5the MPa orientation that deforms, pressurize is cooling taking-up after 0.5 minute, obtains anisotropy Nanocomposite permanent magnetic material.
The microstructure use emission scan electron microscope observation of final magnet, as shown in Figure 1, its crystal grain forms more uniform flake crystalline structure, illustrates that more significant deformation orientation has occurred magnet in thermal deformation process, forms macroscopic anisotropy.
Embodiment 3:
1, utilize fast melt-quenching technology to prepare Nanocomposite quick quenching band, and be broken into the powder of particle diameter 150 μ m, alloying component is Nd21.452Pr0.42Fe74.294Co0.674B0.98Al0.479Cu0.11Nb1.591 (quality percentage composition);
2, utilize fast melt-quenching technology to prepare fusing point lower than the low melting point Nd90Cu10 liquid phase alloy of 800 DEG C, be broken into the powder of 50 μ m;
3, multiphase alloy powder is mixed with 92:8 mass ratio with liquid phase alloy powder;
4, powder being placed in to mould puts into vacuum hotpressing stove and is evacuated to 6 × 10
-3after Pa, be warming up to 700 DEG C, pressurization 270MPa, pressurize is cooling taking-up after 1 minute;
5, by hot pressing blank timeliness 30 minutes under 400 DEG C of vacuum environments;
6, hot pressing blank being placed in to mould puts into vacuum hotpressing stove and is evacuated to 6 × 10
-3after Pa, be filled with 10
2pa argon gas, is warming up to 850 DEG C, pressurization 10
5the MPa orientation that deforms, pressurize is cooling taking-up after 0.5 minute, obtains anisotropy Nanocomposite permanent magnetic material.
Embodiment 4:
1, utilize fast melt-quenching technology to prepare Nanocomposite quick quenching band, and be broken into the powder of particle diameter 150 μ m, alloying component is Nd21.452Pr0.42Fe74.294Co0.674B0.98Al0.479Cu0.11Nb1.591 (quality percentage composition);
2, utilize fast melt-quenching technology to prepare low melting point Nd90Cu10 liquid phase alloy, be broken into the powder of 50 μ m;
3, multiphase alloy powder is mixed with 90:10 mass ratio with liquid phase alloy powder;
4, powder being placed in to mould puts into vacuum hotpressing stove and is evacuated to 6 × 10
-3after Pa, be warming up to 700 DEG C, pressurization 270MPa, pressurize is cooling taking-up after 1 minute;
5, hot pressing blank being placed in to mould puts into vacuum hotpressing stove and is evacuated to 6 × 10
-3after Pa, be filled with 10
2pa argon gas, is warming up to 850 DEG C, pressurization 10
5the MPa orientation that deforms, pressurize is cooling taking-up after 0.5 minute, obtains anisotropy Nanocomposite permanent magnetic material.
Table 1 prepare for each embodiment anisotropy nanocomposite magnets magnetic property
| Magnet type | Remanent magnetism (kGs) | HCJ Hcj(kOe) | Magnetic energy product (MGOe) |
| Embodiment 1 | 9.79 | 9.72 | 20.10 |
| Embodiment 2 | 10.95 | 13.64 | 26.30 |
| Embodiment 3 | 10.61 | 14.76 | 24.86 |
| Embodiment 4 | 10.92 | 14.83 | 27.70 |
From above-described embodiment, by low melting point liquid phase method of diffusion, strengthen the texture of Nanocomposite neodymium iron boron base rapidly quenched magnetic powder in thermal deformation process and formed ability, successfully prepared the block magnet of densification anisotropy with soft/hard magnetic phase nano composite structure.
Claims (5)
1. a preparation method for anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material, is characterized in that this permanent magnetic material includes hard magnetic phase and the soft magnetism phase of nanocrystalline structure, and aforesaid hard magnetic is (Nd, R) mutually
2fe
14b phase, wherein R is at least one being selected from La, Ce, Pr, Gd, Tb and Dy, aforesaid soft magnetism is α-Fe, α-FeCo or Fe mutually
3at least one in B, soft magnetism phase is 2～40% with the mutually shared volume ratio scope of permanent magnetism; And comprise the steps:
1. utilize rapid quenching technique to prepare Nd
2fe
14b/ α-Fe base, Nd
2fe
14b/Fe
3b base or Nd
2fe
14b/ α-FeCo base nanometer crystal complex phase quick quenching band, and be broken into particle diameter and be no more than the principal phase powder of 300 μ m;
2. prepare fusing point taking rare earth element and magnesium-yttrium-transition metal as composition lower than the low melting point liquid phase alloy RM of 800 DEG C, and be broken into particle diameter and be no more than the liquid phase powder of 50 μ m, or this low melting point liquid phase alloy is made to target, R is wherein at least one being selected from La, Ce, Pr, Nd, Gd, Tb and Dy, and M is at least one in Al, Cu, Ga, Co, Sn;
3. liquid phase alloy is mixed with principal phase powder, or liquid phase alloy is evenly coated on to principal phase powder surface, obtain mixed-powder;
4. mixed-powder is carried out under vacuum or protective atmosphere to hot pressing block blank, or mixed-powder is first carried out to high temperature heat diffusion treatment carry out again hot pressing block blank in vacuum or under protective atmosphere;
5. block blank is carried out to thermal deformation orientation and prepare anisotropy magnet, or hot pressing blank is first carried out to high temperature heat diffusion treatment under vacuum or protective atmosphere and carry out again thermal deformation and prepare anisotropy magnet.
2. preparation method according to claim 1, is characterized in that described liquid phase alloy and main-phase alloy mass ratio range are 0.5:99.5～15:85.
3. preparation method according to claim 1, is characterized in that the hot pressing condition during step is is 4. as follows: 500～850 DEG C of hot pressing temperatures, and pressure 100～500MPa, vacuum degree is higher than 1 × 10
-2under Pa condition, carry out hot pressing block blank.
4. preparation method according to claim 1, is characterized in that the high temperature heat diffusion treatment condition during step is is 4. as follows: temperature 500-850 DEG C, and temperature retention time 30～120 minutes, while processing under vacuum condition, vacuum degree is higher than 1 × 10
-2pa, while processing under protective atmosphere environment, protecting gas is argon gas, air pressure is lower than 0.2Mpa.
5. preparation method according to claim 1, is characterized in that the condition of the thermal deformation orientation preparation during step is is 5. as follows: 700～850 DEG C of heat distortion temperatures, and pressure 100～500MPa, vacuum degree is higher than 1 × 10
-2pa, or after vacuumizing, be filled with protection gas argon pressure 10
2pa.
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| CN201110386059.5A CN102496437B (en) | 2011-11-17 | 2011-11-29 | Anisotropic nanocrystal complex-phase compact block neodymium-iron-boron permanent-magnet material and preparation method thereof |
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|---|---|---|---|
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| CN103258609B (en) * | 2013-05-14 | 2016-08-10 | 深圳大学 | The preparation method of anisotropism nanometer rare earth permanent magnetic material |
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| CN103794324A (en) * | 2014-02-26 | 2014-05-14 | 江门市新会区宇宏科技有限责任公司 | Method for preparing nanocrystalline complex phase permanent magnetic powder |
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| CN105321646A (en) * | 2015-11-25 | 2016-02-10 | 中国科学院宁波材料技术与工程研究所 | Nanocrystalline thermal deformation rare-earth permanent magnet with high coercivity and preparation method of nanocrystalline thermal deformation rare-earth permanent magnet |
| CN105355411B (en) * | 2015-11-25 | 2019-01-29 | 中国科学院宁波材料技术与工程研究所 | Rare earth permanent-magnetic material and preparation method thereof |
| CN105869876B (en) * | 2016-04-06 | 2018-05-04 | 中国科学院宁波材料技术与工程研究所 | A kind of rare-earth permanent magnet and its manufacture method |
| US10629341B2 (en) | 2016-08-22 | 2020-04-21 | Ford Global Technologies, Llc | Magnetic phase coupling in composite permanent magnet |
| CN108987016B (en) * | 2018-07-13 | 2021-06-18 | 杭州电子科技大学 | Preparation process of nanocrystalline neodymium-iron-boron magnet |
| CN111627631B (en) * | 2020-03-19 | 2022-07-05 | 中国科学院宁波材料技术与工程研究所 | Preparation method of nano composite permanent magnetic material |
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