CN105355354B - A kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder and preparation method thereof - Google Patents
A kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder and preparation method thereof Download PDFInfo
- Publication number
- CN105355354B CN105355354B CN201510930278.3A CN201510930278A CN105355354B CN 105355354 B CN105355354 B CN 105355354B CN 201510930278 A CN201510930278 A CN 201510930278A CN 105355354 B CN105355354 B CN 105355354B
- Authority
- CN
- China
- Prior art keywords
- magnetic
- rare earth
- phase
- grain
- iron
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Abstract
A kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder and preparation method thereof, belongs to field of rare-earth permanent magnetic.Constituent is：RxT100‑x‑y‑zM1yM2zNv, in formula, R is rare earth element Sm or Sm and other rare earth elements combination, 5≤x≤20；T is iron either iron and cobalt；M1 is at least one of Si, Al, Ni, Ti, V, Cr, Zr, Hf, Nb, Ta, Mo, W element, 0.1≤y≤10；M2 is at least one of Cu, Zn element, 0.1≤z≤10；0.5≤v≤20.The 2 of magnetic are provided:The low melting point that 17 type principal phases are made up of R, M2 element is mutually wrapped in, and can be accommodated rare earth element excessive in alloy and is unlikely to form SmFe2、SmFe3Phase, while contribute to 2 again:17 type main phase grains eliminate defect, the reverse farmland forming core point of reduction and uncoupling effect.Magnetic has good inoxidizability and corrosion resistance.
Description
Technical field
The invention belongs to field of rare-earth permanent magnetic, is related to a kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder and its system
Preparation Method, the magnetic are mainly used as preparing anisotropic bond permanent magnetism.
Background technology
The assistant river true man (Masato Sagawa) of nineteen eighty-two Sumitomo Special Metals have invented sintered Nd-Fe-B magnet, because
Its and preparation method less expensive with up to the present highest magnetic energy product, high-coercive force, raw material is simple and obtains extensively should
With being current most popular rare earth permanent magnet.The rapidly quenching Nd Fe B magnetic powder invented using General Electric Co. Limited is prepared into viscous
Knot magnet because of it there is high dimensional accuracy, convenience to prepare special-shaped magnet and also obtain being widely recognized as market.Rare earth permanent magnet turns into existing
Important basic material during generation is social, in computer, automobile, instrument, instrument, household electrical appliance, petrochemical industry, health care, boat
Extensive use in the industries such as empty space flight.
Nd-Fe-B bases magnet can be prepared into the magnet with high-coercive force, and its coercitive important sources is that have
Have mutually wrapped up by rich neodymium, the principal phase Nd of edge smoothing2Fe14The microstructure of B crystal grain, the principal phase in this microstructure is because of crystal grain
Demagnetizing field and stray magnetic field, the forming core field for improving reverse farmland are reduced because of edge smoothing, and Grain-Boundary Phase being capable of effectively pin magnetic
Farmland.
Nineteen ninety Ireland Trinity University Coey teaches seminar and Yang Yingchang academician seminar of Peking University is based on dilute
The interstitial atom effects of nitrogen in soil-transistion metal compound, find Sm2Fe17Nx(abbreviation samarium iron nitrogen) and Nd (Fe, M)12Nx(letter
Claim neodymium iron nitrogen) there is excellent intrinsic magnetic properties, it can be compared favourably with neodymium iron boron, and there is the Curie temperature higher than neodymium iron boron,
Samarium iron nitrogen and neodymium iron nitrogen are considered as the candidate of rare earth permanent magnet of future generation.
Known Sm2Fe17N3Just magnetic can show high coercivity when crystallite dimension is not more than single shaft particle, in order to obtain
The tiny tissue of crystal grain is obtained, existing method mainly there are two classes, and one kind is directly to prepare crystallite dimension to be less than single domain size
Foundry alloy, this kind of method have：Mechanical alloying method (MA), hydrogenation discrimination method (HDDR) and melt-quenching method (RQ)；Using this kind of
The patent of method have CN1202537C, CN1230755A, US5288339, US5395459, CN1286602C,
CN100513015C、EP1043099B1、EP1043099B1、US6334908、CN1144240C、CN1144240C、
CN1230755A, US6290782, CN102248157B, CN102737801B etc..It is another kind of to be, first prepare crystallite dimension compared with
Big foundry alloy, foundry alloy particle is directly then crushed to single domain size, or first nitrogenizes and be broken into single domain particle again, it is this kind of
Method has：Powder metallurgic method (PM), reduction-diffusion process (R/D)；Using the patent of this kind of method have US5482572,
CN1093311C, CN103785847A, CN1254338C, CN100437841C etc..Process above be formerly prepare it is single-phase
Foundry alloy on the basis of by nitridation obtain R2Fe17N3's.
The Yang Yingchang academician seminar of Peking University in 2002 takes the lead in using strip casting technology at home, it is therefore an objective to shortens
Prepare single-phase Sm2Fe17The time of alloy.
2006, poplar answered prosperous academician to be proposed in granted patent ZL200610113209.4, used rapid hardening slab technology, system
It is standby go out with the single Sm of flake crystalline microstructure2Fe17The alloy casting piece of phase, obtain having concurrently after broken nitridation fine grinding magnetic respectively to
The sheet magnetic of the opposite sex and shape anisotropy.
2012, CN102737801B patents, which propose to prepare using strip casting method, had column crystal Sm2Fe17Rapid hardening casting
Piece, rich Sm SmFe is distributed between column crystal principal phase2Or SmFe3Phase, slab is through crystallization and thermal treatment, coarse crushing, nitridation and fine grinding
And obtain anisotropic samarium iron nitrogen magnetic.
Nd-Fe-B bases magnet can be prepared into the magnet with high-coercive force, and its coercitive important sources is that have
There is the principal phase Nd that edge smoothing is mutually wrapped by rich neodymium2Fe14The microstructure of B crystal grain.It is this to adjust group using Nd-rich phase
The technology that there is selvedge circle uncoupling to act on simultaneously does not apply to but in samarium iron nitrogen, although because the samarium of directly excessive addition can
Nd-rich phase is formed, but these Nd-rich phases are easily decomposed in nitridation process and produce the α-Fe of soft magnetism, turns into anti-
To the forming core core of magnetic domain, this can seriously damage the coercivity of magnetic.Therefore, up to the present, all preparation anisotropy nitrogen
The technique of compound permanent magnetism powder is all first to obtain single-phase foundry alloy and then by crushing, nitrogenizing and being further ground into 1-3 μm
The single crystal grain with magnetic anisotropy is obtained after particle diameter.
In order to further simplify preparation technology, improve the coercivity of anisotropic nitride permanent magnetism powder, inoxidizability and resistance to
Corrosion, the composition that the present invention improves alloy are allowed to advantageously form the Grain-Boundary Phase with magnetic insulating effect, and have formulated corresponding
Preparation technology.
The content of the invention
It is an object of the invention to provide a kind of alloying component for being adapted to prepare anisotropic magnet powder and corresponding preparation technology,
This magnetic has good inoxidizability and corrosion resistance.To achieve the above objectives, the composition of present invention improvement alloy has been allowed to
Beneficial to Grain-Boundary Phase of the formation with magnetic insulating effect, and corresponding preparation technology is formulated.The composition and technique of this alloy are outstanding
It is adapted to prepare Sm2Fe17NxThe anisotropic magnet powder of (abbreviation samarium iron nitrogen) base.
Specifically, the present invention in samarium iron nitrogen magnetic using the constituent represented by atomic percent as：
RxT100-x-y-zM1yM2zNv
In formula, R is rare earth element Sm or Sm and other rare earth elements combination, 5≤x≤20；T be iron either iron and
Cobalt；M1 is at least one of Si, Al, Ni, Ti, V, Cr, Zr, Hf, Nb, Ta, Mo, W element, 0.1≤y≤10；M2 is in Cu, Zn
At least one element, 0.1≤z≤10；0.5≤v≤20.The samarium iron nitrogen magnetic is nitrogenized to obtain by foundry alloy magnetic, foundry alloy
By two class phase compositions, one kind is made up of R, T and M1, has Th2Zn17Or Th2Ni17The principal phase of type structure, its composed atom
Account for the 80-99% of foundry alloy；The another kind of Grain-Boundary Phase being made up of R and M2, its composed atom account for the 1-20% of foundry alloy.
The effect of each composition of the present invention is that R, T, M1 element form Th2Zn17Or Th2Ni17Type structural compounds
Principal phase, M1, which has the function that to promote principal phase to be formed, suppresses α-Fe separates out and crystal grain thinning；M2 elements are difficult to enter Th2Zn17Or
Person Th2Ni17In type structural compounds lattice, but the phase of low melting point is formed with R, still with liquid phase in principal phase precipitation process
Fractions distribution eventually becomes Grain-Boundary Phase on crystal boundary.
M1 is nonmagnetic elements, excessive to add the saturated pole intensity decreases that cause magnetic, so needing M1's
Atomic percent is controlled within 10at%；R element preferentially combines to form the low melting point phase that fusing point is less than 1000 DEG C with M2, turns into
Grain-Boundary Phase between main phase grain；1mol M2 elements need 1-2mol R elements to form Grain-Boundary Phase, therefore M2 is preferably in a proportion of 1-
10at.%, the coercivity that Grain-Boundary Phase is advantageous to magnetic improve, and under excessive M2 then causes the magnetic polarization intensity of magnetic excessive
Drop.
In R2Fe17In compound, only Sm2Fe17Nitride there is uniaxial anisotropy；But, Y2Fe17N2.8、
Ce2Fe17N2.8、Pr2Fe17N2.8 and Nd2Fe17N2.5It is respectively provided with and compares Sm2Fe17N2.3Higher saturated pole intensity, with appropriate ratio
Y, Ce, Pr, Nd of example replace Sm to improve the remanent magnetism of magnetic on the premise of to keep principal phase be uniaxial anisotropy, therefore in R
30at.% Sm can be replaced with Ce, Pr, Nd.
In R2Fe17N3In, a small amount of Co substitutions Fe can improve its Curie temperature, and excessive substitution then damages magnetocrystalline anisotropy
, so Fe need to account for more than 70at.% in T.
Because R is preferentially combined with M2, therefore R amount should be enough to react to form R with whole Fe2Fe17, R's is preferably in a proportion of
10.5-20at.%
By chemical formula RxT100-x-y-zM1yM2zThe represented foundry alloy composition for being used to prepare anisotropic magnet powder of the present invention, can
Example is such as：
Sm11.9Cu4Febal
Sm13.6Cu4Febal
Sm13.6Cu4Co5Febal
Sm11.6Pr2Cu4Febal
Sm11.6Nd2Cu4Febal
Sm12.5Cu4Febal
Sm11.8Cu4Nb1Febal
Sm10.8La1Cu4Febal
Sm10.5Cu2Fe bal
Sm10.8Cu2Febal
Sm11.2Cu2Febal
Sm11.2Cu2Al 1Febal
Sm11.2Cu2ZrFebal
Sm11.8Zn4Febal
Sm13.6Zn4Febal
Sm11.6Pr2Zn4Febal
Sm11.6Nd2Zn4Febal
…………………………
The preparation technology of rare earth permanent magnet powder of the manufacture with above-mentioned foundry alloy composition comprises the following steps：
1) using metallic element R, T, M1, M2 as raw material, induction melting is carried out under argon gas protection, melt operating speed is
1-10m/s water-cooled copper roller casts thin slice (i.e. rapid hardening ingot casting)；
2) heat treatment of 0-2 hours is carried out under argon gas protection at 700-1000 DEG C to slab；
3) slab is carried out tentatively being broken into the powder that granularity is 50-2000 microns；
4) to high pure nitrogen 2-20 hour of the tentatively broken magnetic at 350-550 DEG C；
5) single crystal grain that granularity is 1-10 μm is further broken up into nitridation magnetic using ball mill.
Above-mentioned magnetic preparation technology, when the rapid hardening ingot casting technology of step 1) prepares slab, the linear resonance surface velocity scope of copper roller
It is 1-5m/s, for institute's cast alloy scale flake thickness between 100 μm -500 μm, its microscopic structure has following characteristics：By R, T,
The principal phase of M1 elements composition has Th2Zn17Or Th2Ni17Type structure, crystallite dimension are 2-50 μm；It is made up of M2 and R element
Grain-Boundary Phase fusing point is less than 1000 DEG C, is evenly distributed on principal phase grain boundaries, and thickness is 1nm-5 μm.
Above-mentioned magnetic preparation technology, the effect of step 2) are removal process 1) in fail to react complete α-Fe；Optimization is brilliant
Between phase distribution, improve the border micro-structural of principal phase, reduce corner sharp on main phase grain.
Above-mentioned magnetic preparation technology, the effect of step 3) are to improve the dynamic performance of magnetic nitridation so that foundry alloy is equal
It is even, fully nitrogenize, eliminate do not nitrogenize complete foundry alloy to the coercitive infringement of magnetic.
Above-mentioned magnetic preparation technology, the effect of step 4) are that nitrogen-atoms enters Th2Zn17Or Th2Ni17Type principal phase, promotes
Th2Zn17Or Th2Ni17Type Sm-Fe based compounds become easy c-axis magnetization from the magnetization of easy basal plane；Nitridation is being provided with agitating device
Rotating furnace body in carry out.
Above-mentioned magnetic preparation technology, in step 4) after magnetic via nitride, magnetic is by Sm2Fe17Nx(abbreviation samarium iron nitrogen), composition
For M2 and R crystal boundary phase composition.
Above-mentioned magnetic preparation technology, the effect of step 5) are further broken magnetics, form single crystal grain, turn into magnetic respectively to
The samarium iron nitrogen magnetic of the opposite sex.The principal phase of this magnetic has that microstructural flaws are less, there is Grain-Boundary Phase cladding on surface, thus had
Excellent magnetic property and good inoxidizability and corrosion resistance.
The distinguishing feature of the present invention is that the foundry alloy composition for preparing samarium iron nitrogen magnetic is easily formed born of the same parents' shape group
Knit --- low melting point Grain-Boundary Phase, which is wrapped in, provides the 2 of magnetic:17 type principal phases.In Nd-Fe-B base permanent magnetism, it is distributed in crystal boundary
The rich neodymium of low melting point has the function that very crucial relative to the technology magnetic property of magnet：Rich neodymium can mutually make the side of main phase grain
Boundary is smooth, clearly reduces stray magnetic field, removes the reversely farmland forming core point such as borderline α-Fe, improves the forming core field of magnet.Therefore,
The rich neodymium for being distributed in neodymium iron boron crystal boundary mutually rises on the superior intrinsic magnetic properties energy of neodymium iron boron principal phase performance, the coercivity for ensureing magnet
The effect of key.However, in the preparation of Sm-Fe-N base permanent magnetism, if adding excessive Sm, the SmFe of formation in dispensing2、
SmFe3The mutually easily decomposes precipitation α-Fe in nitridation, the serious coercivity for damaging magnetic；If Sm adds deficiency, directly formed
α-Fe.Because Sm is very easy to volatilization, it is difficult to be precisely controlled to during master alloy melting point, therefore, although Sm2Fe17N3
With very superior intrinsic magnetic properties energy, but delay to mass produce.
In the present invention, the composition of foundry alloy is easily formed cellular structure --- the 2 of magnetic are provided:17 type principal phases are by R, M2
The low melting point of element composition is mutually wrapped in.This Grain-Boundary Phase has the function that, similar to rich neodymium phase in neodymium iron boron, conjunction can be accommodated
Excessive rare earth element in gold and be unlikely to form SmFe2、SmFe3Phase, while contribute to 2 again:17 type main phase grains, which eliminate, to be lacked
Fall into, reduce reverse farmland forming core point and uncoupling effect.
Help to be formed main phase grain size uniform using rapid hardening slab technology, the group of Grain-Boundary Phase is distributed with around crystal grain
Knit.
Brief description of the drawings
Fig. 1 is the SEM back scattering microscopic images of rapid hardening slab, the white Grain-Boundary Phase being made up of M2-R elements, is distributed in
On the principal phase crystal boundary of black.
Embodiment
Embodiment 1
The rare-earth Sm for being 99.9% with purity, pure iron, pure Cu are raw material, according to following 5 kinds of chemical formula dispensings：(1)
Sm10.53Fe89.47, (2) Sm11.32Fe87.28Al0.40Cu1.00, (3) Sm13.68Fe81.92Al0.40Cu4.00, (4)
Sm15.26Fe7834Al0.40Cu6.00, (5) Sm18.42Fe71.18Al0.40Cu10.00；Because Sm is readily volatilized, on the basis of amount of calculation
Add 10% as compensation.The rare-earth Sm prepared, pure iron, pure Cu raw materials are put into induction melting furnace, fire door is closed, is evacuated to
0.01Pa, applying argon gas are into body of heater to 0.9atm；Melted completely uniformly using sensing heating alloy to raw material, at this time melt
Temperature is about 1550 DEG C, and alloy pig is poured into water cooled copper mould；Alloy pig is broken into granularity about 10mm fritter, puts 20g conjunctions
In quartz ampoule, quartzy bottom of the tube is provided with directly for 0.8mm osculum ingot, under argon gas protection, is prepared with 2m/s roller speed
Rapid hardening slab；Slab is placed in corundum crucible, air cooling after 1-2 hour heat treatments is carried out under 750 DEG C, argon gas protection, will be cast
Piece is broken into 100-300 μm of particle；Magnetic 10 hours is nitrogenized at 450 DEG C using high pure nitrogen, by gas-solid reaction by principal phase
It is nitrided into Sm2Fe17Nx；Nitride is become anisotropic magnet powder after ball mill crushing is 2-5 microns into granularity again, through magnetic field
After orientation, the magnetic property of magnetic is as follows：
Magnetic property after each composition foundry alloy nitridation of table 1.
| Foundry alloy composition | Br(T) | Hcj(kA/m) | (BH)max(kJ/m3) | Tc(K) |
| Sm10.53Fe89.47 | 1.1 | 543 | 147 | 743 |
| Sm11.32Fe87.28Al0.40Cu1.00 | 1.38 | 1173 | 367 | 743 |
| Sm13.68Fe81.92Al0.40Cu4.00 | 1.34 | 1696 | 349 | 743 |
| Sm15.26Fe7834Al0.40Cu6.00 | 1.26 | 1860 | 305 | 743 |
| Sm18.42Fe71.18Al0.40Cu10.00 | 1.16 | 2024 | 244 | 743 |
Embodiment 2
The rare-earth Sm for being 99.9% with purity, pure iron, pure Zn are raw material, according to according to following 5 kinds of chemical formula dispensings：(1)
Sm11.32Fe87.28Al0.40Zn1.00, (2) Sm13.68Fe81.92Al0.40Zn4.00, (3) Sm15.26Fe7834Al0.40Zn6.00, (4)
Sm18.42Fe71.18Al0.40Zn10.00；Because Sm is readily volatilized, add 10% on the basis of amount of calculation as compensation.It will prepare
Rare-earth Sm, pure iron, pure Zn raw materials be put into induction melting furnace, close fire door, be evacuated to 0.01Pa, applying argon gas into body of heater extremely
0.9atm；Melted completely uniformly using sensing heating alloy to raw material, at this time the temperature of melt is about 1550 DEG C, uses water-cooled copper
Mould pours into alloy pig；Alloy pig is broken into granularity about 10mm fritter, puts 20g alloy pigs in quartz ampoule, quartz ampoule bottom
Portion is provided with directly for 0.8mm osculum, and under argon gas protection, rapid hardening slab is prepared with 2m/s roller speed；Slab is placed in corundum
In crucible, air cooling after 1-2 hour heat treatments is carried out under 900 DEG C, argon gas protection, slab is broken into 100-300 μm of particle；
Magnetic is nitrogenized at 450 DEG C 10 hours, principal phase is nitrided into by Sm by gas-solid reaction using high pure nitrogen2Fe17Nx；Nitride
Anisotropic magnet powder is become after ball mill crushing is 2-5 microns into granularity again, after magnetic field orientating, the magnetic property of magnetic is such as
Under：
Magnetic property after each composition foundry alloy nitridation of table 2.
| Foundry alloy composition | Br(T) | Hcj(kA/m) | (BH)max(kJ/m3) | Tc(K) |
| Sm11.32Fe87.28Al0.40Zn1.00 | 1.36 | 1103 | 361 | 743 |
| Sm13.68Fe81.92Al0.40Zn4.00 | 1.35 | 1586 | 339 | 743 |
| Sm15.26Fe7834Al0.40Zn6.00 | 1.22 | 1720 | 315 | 743 |
| Sm18.42Fe71.18Al0.40Zn10.00 | 1.09 | 1934 | 242 | 743 |
| Sm10.68Nd3Fe81.92Al0.40Zn4.00 | 1.38 | 1447 | 358 | 737 |
Claims (1)
1. a kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder, it is characterised in that samarium iron nitrogen magnetic is with represented by atomic percent
Constituent is：
RxT100-x-y-zM1yM2zNv
In formula, R is rare earth element Sm or Sm and other rare earth elements combination, 5≤x≤20；T is iron either iron and cobalt；
M1 is at least one of Si, Al, Ni, Ti, V, Cr, Zr, Hf, Nb, Ta, Mo, W element, 0.1≤y≤10；M2 be in Cu, Zn extremely
A kind of few element, 0.1≤z≤10；0.5≤v≤20；
The samarium iron nitrogen magnetic is nitrogenized to obtain by foundry alloy magnetic, and for foundry alloy by two class phase compositions, one kind is by R, T and M1 group
Into, there is Th2Zn17Or Th2Ni17The principal phase of type structure, its composed atom account for the 80-99% of foundry alloy；It is another kind of be by R and
The Grain-Boundary Phase of M2 compositions, its composed atom account for the 1-20% of foundry alloy；
M1 atomic percent will be controlled within 10at%；M2 ratio is 1-10at.%；
Fe need to account for more than 70at.% in T；
Preparation technology comprises the following steps：
1) using metallic element R, T, M1, M2 as raw material, induction melting is carried out under argon gas protection, melt operating speed is 1-
10m/s water-cooled copper roller casts thin slice, i.e. rapid hardening ingot casting；
2) heat treatment of 0-2 hours is carried out under argon gas protection at 600-1000 DEG C to slab；
3) slab is carried out tentatively being broken into the powder that granularity is 50-2000 microns；
4) under 350-550 DEG C of high pure nitrogen is nitrogenized to tentatively broken magnetic 2-20 hours；
5) single crystal grain that granularity is 1-10 μm is further broken up into nitridation magnetic using ball mill；
When the rapid hardening ingot casting technology of step 1) prepares slab, the linear resonance surface velocity scope of copper roller is 1-5m/s, institute's cast alloy scale
For thickness between 100 μm -500 μm, its microscopic structure has following characteristics：The principal phase being made up of R, T, M1 element has Th2Zn17
Or Th2Ni17Type structure, crystallite dimension are 2-50 μm；The Grain-Boundary Phase fusing point being made up of M2 and R element is less than 1000 DEG C, uniformly
Principal phase grain boundaries are distributed in, thickness is 1nm-5 μm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510930278.3A CN105355354B (en) | 2015-12-15 | 2015-12-15 | A kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510930278.3A CN105355354B (en) | 2015-12-15 | 2015-12-15 | A kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105355354A CN105355354A (en) | 2016-02-24 |
| CN105355354B true CN105355354B (en) | 2017-12-08 |
Family
ID=55331306
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510930278.3A Active CN105355354B (en) | 2015-12-15 | 2015-12-15 | A kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105355354B (en) |
Families Citing this family (22)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105957673B (en) * | 2016-03-14 | 2017-11-28 | 北京科技大学 | A kind of isotropism rare earth permanent magnet powder and preparation method thereof |
| CN105609224B (en) * | 2016-03-14 | 2018-01-16 | 北京科技大学 | A kind of preparation method of anisotropy samarium iron nitrogen permanent magnetism powder |
| JP6596370B2 (en) * | 2016-03-18 | 2019-10-23 | 株式会社東芝 | Permanent magnet, rotating electric machine and vehicle |
| CN105788795B (en) * | 2016-05-23 | 2018-09-07 | 温州弘恒电子科技有限公司 | A kind of preparation method of SmCo nitrogen permanent-magnet material |
| CN110168674B (en) * | 2017-03-10 | 2022-10-28 | 国立研究开发法人产业技术综合研究所 | Magnet powder containing Sm-Fe-N crystal grains, sintered magnet produced from the magnet powder, and method for producing the magnet powder and the sintered magnet |
| US11476020B2 (en) * | 2017-06-30 | 2022-10-18 | Toyota Jidosha Kabushiki Kaisha | Rare earth magnet and production method thereof |
| JP7095310B2 (en) | 2018-02-28 | 2022-07-05 | 大同特殊鋼株式会社 | Sm-Fe-N magnet material and Sm-Fe-N bond magnet |
| US20200105446A1 (en) * | 2018-09-28 | 2020-04-02 | Tdk Corporation | Samarium-iron-bismuth-nitrogen-based magnet powder and samarium-iron-bismuth-nitrogen-based sintered magnet |
| CN109273182B (en) * | 2018-10-19 | 2020-06-16 | 广东省稀有金属研究所 | Single crystal magnetic powder and preparation method and application thereof |
| CN109192428B (en) * | 2018-10-19 | 2020-06-16 | 广东省稀有金属研究所 | Low-cost monocrystalline magnetic powder and preparation method and application thereof |
| CN109273183B (en) * | 2018-10-19 | 2020-06-16 | 广东省稀有金属研究所 | Corrosion-resistant monocrystalline magnetic powder and preparation method and application thereof |
| CN109273184B (en) * | 2018-10-19 | 2020-08-04 | 广东省稀有金属研究所 | Low-cost corrosion-resistant monocrystalline magnetic powder and preparation method and application thereof |
| CN109243745B (en) * | 2018-10-19 | 2020-08-04 | 广东省稀有金属研究所 | High-temperature-resistant corrosion-resistant monocrystalline magnetic powder and preparation method and application thereof |
| CN111411325A (en) * | 2019-01-04 | 2020-07-14 | 董元 | Samarium iron nitrogen or neodymium iron nitrogen anisotropic bonded magnetic powder and preparation method thereof |
| CN112863798A (en) * | 2019-11-27 | 2021-05-28 | 横店集团东磁股份有限公司 | Samarium-iron-nitrogen magnetic powder and preparation method thereof |
| CN111755191A (en) * | 2020-07-09 | 2020-10-09 | 浙江工业大学 | High-abundance rare earth Ce/Y/Nd/La substituted samarium-iron-nitrogen-based magnetic powder with high maximum magnetic energy product |
| CN112086280B (en) * | 2020-09-22 | 2022-04-08 | 宁波磁性材料应用技术创新中心有限公司 | Preparation method of rare earth iron intermetallic nitride powder |
| CN112951535A (en) * | 2021-02-05 | 2021-06-11 | 华南理工大学 | Single crystal magnetic powder and preparation method and application thereof |
| CN113611470B (en) * | 2021-08-24 | 2022-12-16 | 横店集团东磁股份有限公司 | Interstitial rare earth permanent magnet alloy material and preparation method thereof |
| CN114974779A (en) | 2022-06-20 | 2022-08-30 | 横店集团东磁股份有限公司 | Samarium-based rare earth permanent magnetic material and preparation method and application thereof |
| CN116612973B (en) * | 2023-03-30 | 2023-12-05 | 广东省科学院资源利用与稀土开发研究所 | Preparation method of high-density neodymium iron nitrogen magnet |
| CN116487169B (en) * | 2023-03-30 | 2023-10-13 | 广东省科学院资源利用与稀土开发研究所 | Low-cost core-shell structure neodymium iron nitrogen magnetic powder and preparation method thereof |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1163914C (en) * | 1998-05-26 | 2004-08-25 | 日立金属株式会社 | Nitride type rare-earth permanent magnet material and bonded magnet using same |
| JP3727863B2 (en) * | 2001-03-29 | 2005-12-21 | 株式会社東芝 | Manufacturing method of magnet material |
| CN102737801B (en) * | 2012-07-11 | 2014-09-17 | 北京科技大学 | Method for preparing Sm-Fe-N anisotropic magnetic powder |
-
2015
- 2015-12-15 CN CN201510930278.3A patent/CN105355354B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN105355354A (en) | 2016-02-24 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105355354B (en) | A kind of samarium iron nitrogen base anisotropy rare earth permanent magnet powder and preparation method thereof | |
| CN105609224B (en) | A kind of preparation method of anisotropy samarium iron nitrogen permanent magnetism powder | |
| JP5856953B2 (en) | Rare earth permanent magnet manufacturing method and rare earth permanent magnet | |
| CN105957673B (en) | A kind of isotropism rare earth permanent magnet powder and preparation method thereof | |
| JP6446092B2 (en) | Composite magnetic material and method for producing the same | |
| Rong et al. | Nanocrystalline and nanocomposite permanent magnets by melt spinning technique | |
| Ni et al. | Study on magnetic properties of Ce17Fe78− xZrxB6 (x= 0–2.0) alloys | |
| CN104851545B (en) | A kind of permanent-magnet material preparation method with grain boundary decision layer | |
| WO2016201944A1 (en) | Preparation method of ndfeb magnet having low melting point light rare-earth-copper alloy at grain boundary | |
| WO2021249159A1 (en) | Heavy rare earth alloy, neodymium-iron-boron permanent magnet material, raw material, and preparation method | |
| WO2014190558A1 (en) | Rare-earth permanent magnetic powders, bonded magnet comprising same, and device using bonded magnet | |
| CN106319323B (en) | A kind of Sintered NdFeB magnet assistant alloy slab and preparation method thereof | |
| CN103680919B (en) | A kind of preparation method of the high anti-corrosion sintered Nd-Fe-B permanent magnet of tough height of high-coercive force | |
| CN108063045A (en) | A kind of no heavy rare earth Nd-Fe-B permanent magnet material and preparation method thereof | |
| Madugundo et al. | Recent developments in nanostructured permanent magnet materials and their processing methods | |
| JP2013197414A (en) | Sintered compact and production method therefor | |
| CN103559972A (en) | Preparation method for sintered Nd-Fe-B permanent-magnet material | |
| JP2010010665A (en) | HIGH COERCIVE FIELD NdFeB MAGNET AND CONSTRUCTION METHOD THEREFOR | |
| CN103137314B (en) | A kind of method preparing rare earth-iron-boron permanent magnet | |
| CN104752048B (en) | A kind of preparation method of sintered Nd-Fe-B permanent magnet | |
| KR20230126733A (en) | Main part alloy neodymium iron boron magnetic material and its manufacturing method | |
| CN114156031A (en) | Neodymium-iron-boron magnet and preparation method thereof | |
| JP2015529004A (en) | Rare earth permanent magnet powder, bonded magnet and device using the bonded magnet | |
| CN105913989A (en) | High-remanence material and preparation method | |
| CN105938747B (en) | A kind of high-coercive force high performance nano composite permanent magnetic body and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |