CN1132399A - Double-phase rare-earth-iron-boron magnetic powder and its prepn. method - Google Patents
Double-phase rare-earth-iron-boron magnetic powder and its prepn. method Download PDFInfo
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- CN1132399A CN1132399A CN 95102821 CN95102821A CN1132399A CN 1132399 A CN1132399 A CN 1132399A CN 95102821 CN95102821 CN 95102821 CN 95102821 A CN95102821 A CN 95102821A CN 1132399 A CN1132399 A CN 1132399A
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Abstract
A magnetic rare-earth -Fe-B powder is prepared through preparing rare-earth-Fe-B alloy, hydrogenating at 200-1000 deg.C in hydrogen or hydrogen and inertial gas mixed atomosphere while making hydrogen retain in the material, dehydrogenating at 600-1000 deg.C until hydrogen pressure is not higher than 0.1 torr, and cooling, and features that each particle is composed of two phases containing intermetallic compounds R2Fe14B and R2Fe17 respectively with square and rhombohedral crystal structures distributed alternatively with grain size of 0.1-10 micrometers.
Description
The present invention relates to a kind of rare-earth-iron-boron alloy permanent-magnet powder and manufacture method thereof with excellent magnetic energy.
Bonded permanent magnet can be made arbitrary shape owing to have the very high degree of freedom, therefore follows the development of high-tech to be expanded rapidly in various application in recent years.Bonded permanent magnet is formed with organic or soft metal binding agent bonding by Magnaglo, and its magnetic property is subjected to the influence of Magnaglo performance and packing density, and wherein the body of powder magnetic property is considered to primary factor.
So-called permanent magnet main feature is that magnet must have higher coercive force (Hc)--it is the symbol of the anti-demagnetization of magnet sexuality.Therefore coercive force is the structure sensitive parameter, depends on the structure of alloyed powder opisthosoma to a great extent, and people seek the crystal that can give full play to the permanent magnetism performance and the structure of alloy phase always in recent years.
The powder of rare earth permanent magnet can be regarded isolated small magnet as, as long as can comprise the structure that block magnet should have in these small magnets, just can guarantee to have the coercive force identical or approximate with block magnet.Because RCO
5Type and R
2CO
17Powder after the fragmentation of type rare earth permanent magnet sintered body has kept original structure, therefore still has the excellent magnetism energy, can be directly used in the making bonded permanent magnet.But, R
2Fe
14Category-B type rare earth permanent magnet has then shown tangible difference, has destroyed the desirable phase structure that produces high-coercive force after the sintered body fragmentation, therefore is difficult to be directly used in the making bonded permanent magnet.For this reason with make nanocrystalline and the millimicron crystalline substance described by following patent by the multiple NdFeB manufacturing method of power of purpose.
1. described a kind of rare-earth-iron-boron alloy among the U.S. Patent Publication No. US4802931 and be injected on the metal runner of high speed rotating, made the solution quench cooled form thickness and be no more than 500 microns strip or scale fusing.Material after the quench cooled has the microscopic structure of amorphous or superfine crystal grain, forms the crystallite that uniform crystallite dimension is no more than 500nm after the proper temperature crystallization is handled, and X-ray diffraction shows that this crystallite is the R of tetragonal
2Fe
14The B phase, when this when percentage by volume is not less than 80% in material, material has the coercive force that is not less than 1000 oersteds.
2. Chinese patent publication number CN1033018A has described a kind of rare-earth-iron-boron absorption hydrogen-put method that the hydrogen recrystallization method prepares the rare-earth-iron-boron Magnaglo of utilizing, basic step is at first to prepare the rare-earth-iron-boron alloy material, then, in hydrogen atmosphere, remain under 500 ℃ to the 1000 ℃ temperature, make the hydrogen occlusion in alloy material, subsequently, with alloy material dehydrogenation under 500 ℃ to 1000 ℃ temperature, drop to up to hydrogen pressure and to be not more than 1 * 10
-1Torr, cooling then, the recrystal grain degree that this method obtains is between 0.1 micron to 1 micron, powder has the coercive force greater than 5 kilo-oersteds.This method technology is simple, and the consistency of powder magnetic is better, and in addition, Zhi Bei rare-earth-iron-boron Magnaglo generally has the anisotropy characteristics in this way.
3. Chinese patent publication number CN91102450 has described and has a kind ofly utilized the rare-earth-iron-boron alloy to inhale hydrogen at low temperature to produce distortion of lattice, and then the high-temperature dehydrogenation transition process that produces crystallization again prepares the method for rare-earth-iron-boron Magnaglo.Basic step is at first to prepare the rare-earth-iron-boron material, inhale hydrogen in 200 ℃ to 500 ℃ then, subsequently again in 600 ℃ to 1000 ℃ dehydrogenations, when proceeding to a certain degree, dehydrogenation in the material crystallization again takes place, when recrystal grain was controlled at 0.1 to 1 micron, the coercive force of powder was not less than 5000 oersteds.
As mentioned above, no matter the powder of acquisition still by the powder of using the hydrogen processing method directly to obtain of method 2,3 descriptions, all is included as in each powder particle and obtains the required some complete construction unit of high-coercive force by the thin slice of method 1 manufacturing is broken.This complete construction unit can be described as single R
2Fe
14The rich rare earth of distributing on the grain boundary of B phase mutually and rich rare earth amorphous phase, in other words rich rare earth mutually and rich rare earth amorphous phase with encirclement R
2Fe
14The form of B phase exists, and this fact is considered to produce bigger coercitive reason.This structure is interpreted as one-domain structure on the magnetic hardening mechanism, promptly has the ferromagnetism R of single domain size
2Fe
14B is surrounded mutually by the rich R of non-iron.In order to make material have the volume ratio of the common ferromagnetism phase of sufficiently high comprehensive magnetic property, generally be not less than 80%, therefore, material is all described in the foregoing invention with R
2Fe
14B is main mutually, exists mutually with a small amount of rich R simultaneously, because nonmagnetic rich rare earth exists mutually and reduced R
2Fe
14The volume ratio of B, thus the saturation magnetization value that has reduced magnetic can not be brought into play the intrinsic magnetic property of rare-earth-iron-boron alloy fully.
The purpose of this invention is to provide a kind of rare-earth-iron-boron Magnaglo, when this powder is used as bonded permanent magnet, demonstrate more excellent magnetism energy.
Formation of the present invention provides a kind of rare-earth-iron-boron powder, has comprised R in the independent powder particle of it each
2Fe
14B and R
2Fe
17The phase of two kinds of structures, independent R
2Fe
17Do not possess the high-coercive force characteristic mutually, but and R
2Fe
14B has similar saturation magnetization value, works as R
2Fe
17With R
2Fe
14R when exchange coupling takes place B
2Fe
17The high saturation and magnetic intensity advantage be utilized, and the low-coercivity value is overcome, thereby obtains than traditional in the past single R
2Fe
14B is the better magnetic of the material of principal phase.Because the exchange coupling of two-phase can only be brought into play in short range, therefore the crystallite dimension of two-phase can not be above 10 microns, though crystallite dimension may more help exchange coupling less than 0.1 micron, present technique is difficult to reach, so determines in the claim that mean grain size is 0.1 micron to 10 microns.Also having borderline phases such as a spot of rich R in the material except that above-mentioned two principal phases, because these borderline phases are the nonferromagnetic phase, and is not again for obtaining the necessary phase of high-coercive force, therefore will reducing its amount as far as possible.
Alloy is formed by the gathering of mixing mutually of two kinds of ad hoc structures, wherein R
2Fe
14B has tetragonal structure, R
2Fe
17Has water chestnut square crystal structure.Two-phase is with mutual over-over mode three-dimensional arrangement.When two-phase relative volume mark is roughly suitable, produce coupling effect preferably, can also slightly lay particular stress on, but two-phase is not the relation of principal phase and borderline phase generally.
According to the said structure feature, the composition of alloy is by R
xFe
100-x-yB
yExpression, wherein x is 10.5～16, if x＜10.5at%, to there be the unnecessary α Fe outside the equilibrium chemistry dosage to occur, this α Fe exists with thick dendritic crystal in ingot casting, both made and between 1000 ℃ to 1100 ℃, carried out long-time homogenizing and handle and also can not eliminate, and heat treatment process subsequently can not refinement, therefore seriously destroy the coercive force of material.As x＞16at%, a large amount of nonmagnetic rich R borderline phases will appear in the alloy, and material remanent magnetization and magnetic energy product are reduced significantly.Definition Y is 1.5～6at% in the formula, if y＞6at% alloy will become single R
2Fe
14B phase and possible a small amount of rich R borderline phase.As y＜1.5at%, R
2Fe
17Volume ratio is excessive, has just lost and R
2Fe
14Produce the optimum condition of exchange coupling between B, thereby make permanent magnetism performance rapid deterioration.
According to foregoing description, the R in the composition formula can be Ce, La, and Pr, Sm, Gd, Nd, Dy, Eu, rare earth elements such as Tb, but wherein have only Nd
2Fe
17/ Nd
2Fe
14B and Pr
2Fe
17/ Pr
2Fe
14B possesses the highest saturation magnetization value.Can replace Pr with other rare earth element of part in order to improve temperature characterisitic or to improve coercivity value, Nd, but too much unsuitable, otherwise influence comprehensive magnetic property, therefore require at least a selection Nd among the R, Pr (or PrNd enriched substance), and content is no less than 50% of R total amount.
B forms R in alloy
2Fe
14The mutually indispensable element of B its role is to change its lattice constant in the R-Fe alloy when B adds, thereby change exchange energy its residence reason temperature is improved, and reaches the level with Practical significance.Near in the periodic table of elements B other element also has similar effect, so B can be by C, N, and Si, Ge, element substitutions such as P, but the independent or compound use of these elements does not all reach the effect of B, therefore limits the amount of substituting and is no more than 40% of B total amount.
Multiple transition element can be used to part and substitutes Fe with minor betterment magnetism of material energy in the periodic table of elements, but removes Co in these elements, and the outer overwhelming majority of Ni is a non-ferromagnetic elements, and excessive alternative meeting causes saturation magnetization to reduce, and has destroyed main body phase R
2Fe
14B and R
2Fe
17Formation.Therefore its content must not be greater than following ratio:
20at％Co，?4.5at％Ti，5.0at％Nb，8.0at％Mn，7.5at％V，?5.5at％Cr，
7.0at％Ta，5.5at％Al，9.5at％Zr，5.5at％Ga，8.0at％Mo，7.0at％W
3.0at％Bi，5.5at％Cu，2.5at％Sb，3.5at％Sn，1.5at％Zn，9.0at％Ni
Manufacture method of the present invention is--iron--boron ingot casting of at first making the rare earth of required composition, and ingot casting can be smelted with induction furnace, and also available electric arc furnace smelting is smelted and carried out under vacuum and protective atmosphere, to prevent a large amount of oxidations of rare earth element.Subsequently ingot casting is broken into corase particles and places vacuum heat treatment furnace, vacuum reaches 5 * 10
-5, and then feed the mist of hydrogen or hydrogen and inert gas, make that the hydrogen dividing potential drop reaches 0.1～1 atmospheric pressure in the vacuum chamber.Then vacuum chamber is moved in the body of heater that has heated or with stove and heat up, keep tens of branches behind the arrival design temperature to a few hours.The temperature that keeps is selected between 200 ℃～1000 ℃, and the retention period in this temperature range, a large amount of hydrogen are inhaled into alloy, and are trapped in the alloy, but the mode of being detained has difference with the difference that keeps temperature.Hydrogen mainly is inhaled in the middle of the lattice vacancy of alloy between 200 ℃～500 ℃, causes that meanwhile lattice produces big distortion.When maintaining the temperature between 600 ℃～1000 ℃ the R behind the alloy suction hydrogen in the former ingot casting of variation of generation phase
2Fe
14B inhales mutually that disproportionation is to be of a size of 0.1～0.3 micron RH behind the hydrogen
x+ Fe
2B+ α Fe mixture, the R in the former ingot casting
2Fe
17Disproportionation is size RH similar to the above
x+ α Fe.By the diffusion of B and Fe atom, adjust element and distribute subsequently, make former R
2Fe
14B and R
2Fe
17Phase region all becomes uniform RH
x+ Fe
2B+ α Fe mixture.
In hydrogen or hydrogen and noble gas mixtures atmosphere, keep enough to after carry out dehydrogenation and handle.Hydrogen plays very key effect in whole technical process, but can not have hydrogen atom to remain in the magnetic in end-state, otherwise has a strong impact on magnetic property, the hydrogen dividing potential drop is dropped to be not more than 1 * 10
-1, desorption temperature is chosen in 600 ℃ to 1000 ℃.For inhaling the alloy that hydrogen is handled at 200--600 ℃, crystallization again takes place in certain embodiments, be lower than 600 ℃ again crystallization carry out very slow, inadvisable on technology, be higher than 1000 ℃ of crystallization crystal grain and too grow up, surpass the size of effective exchange coupling, make magnetic property can not reach desired quantity; Again cohesive process takes place in the alloy for inhaling hydrogen at 600 ℃～1000 ℃ in certain embodiments, again in conjunction with at first occurring in RH
x, Fe
2B, the intersection of α Fe, RH
2After losing hydrogen, through the composition diffusion, with Fe
2B, α Fe recombines into Nd
2Fe
14B compound phase, meanwhile simple the combination with α Fe forms R
2Fe
17Compound, this two-phase evenly distribute at space-alternating provides desirable magnetic exchange coupling distribution.Be lower than 600 ℃ combination transformation does not again take place, be higher than 1000 ℃, foregoing crystal grain takes place too grow up, so desorption temperature is chosen between 600 ℃～1000 ℃.Through the optimised process dehydrogenation, the material cooled after the processing to room temperature is fixed up its optimum structure.
Before inhaling the hydrogen processing, the structural state of ingot casting is very big to last powder magnetic property influence.In the ingot casting cooling procedure, because nonequilibrium freezing has a lot of thick dendroid α Fe to exist.Although in inhaling the hydrogen process, can eliminate part α Fe, but eliminate very difficult fully, these α Fe not only have a strong impact on the magnetic of final powder, also make the ingot casting fragmentation very difficult, for this reason in manufacture method of the present invention, for guaranteeing best powder magnetic property, should increase before the ingot casting fragmentation between 800 ℃～1200 ℃ of the one-levels with elimination dendroid α Fe is the uniform ingredients processing of purpose.Uniform ingredientsization is to lean on the diffusion way of atom to carry out, and it is very slow that temperature is lower than 800 ℃ of diffusions, along with the rising diffusion process of temperature is accelerated, but can not be higher than 1200 ℃, otherwise the ingot casting fusing.
The invention has the advantages that: utilize gained magnetic of the present invention and bonded permanent magnet, because the R in the crystal grain
2Fe
14B and R
2Fe
17All be the ferromagnetism phase, do not need the rich R borderline phase of nonferromagnetic,, so can obtain than in the past by R as necessary the condition that obtains high-coercive force
2Fe
14B has higher saturation magnetization and magnetic energy product value with the magnet that rich R borderline phase is purchased.
Below with several example explanation the present invention.
Embodiment 1
Select neodymium (Nd) and iron and boron and smelts in intermediate frequency furnace and be cast into ingot from rare earth element, its composition is expressed as Nd with the atom composition
12.5Fe
83.5B
4.0, after 1060 ℃ of homogenizing were handled, alloy was mainly by the Nd of mean grain size＜10 μ m
2Fe
14B and Nd
2Fe
17Phase composition, general proportions are 6: 4, and the ingot casting coarse crushing after homogenizing is handled is placed on and is evacuated to 5 * 10 in the quartz ampoule
-5Torr charges into 1 atmospheric pressure hydrogen then, puts into and presets 900 ℃ heating furnace, is incubated 1 hour, meanwhile, does not change with hydrogen pressure in the air bag holding tube.Be evacuated to 5 * 10 once more after inhaling hydrogen
-5Torr is got rid of hydrogen, subsequently with the powder quench cooled.
The magnet powder that obtains is carried out X-ray analysis show, main diffraction maximum sign goes out to have the metal of tetragonal with compound Nd
2Fe
14B and intermetallic compound Nd with water chestnut square structure
2Fe
17, visible Magnaglo of the present invention is mainly by Nd
2Fe
14B and Nd
2Fe
17Phase composition.
The epoxy resin of above-mentioned Magnaglo and 3% (weight) is blended in 7 tons/centimetre
2Pressure under compression moulding, then pressed compact was kept 1 hour down at 140 ℃, make it to solidify, obtain bonded permanent magnet, its magnetic property is listed in table 1.
Comparative Examples 1
Rare earth alloy ingot casting among the embodiment 1 can be expressed as Nd by its composition atom composition
12.5Fe
80.5B
7Be processed into for the nd-fe-b alloy Magnaglo that contrasts usefulness by embodiment 1.The X-ray diffraction spectral line shows that alloy is mainly by Nd under this composition
2Fe
14The single-phase composition of B, the rich neodymium borderline phase that contains trace is followed.
Then this magnetic and 3% (weight) epoxy resin is mixed, make bonded permanent magnet by embodiment 1 described condition, its magnetic property is listed in table 1.
Table 1
| Sample type | Magnetic average particle size (micron) | Bonded permanent magnet density (grams per cubic centimter) | Bonded permanent magnet magnetic characteristic Br 1Hc (BH) max (thousand height) (kilooersted) (hundred Wan Gaoao) |
| Embodiment 1 | ??110 | ??5.7 | ??6.3???13.2???8.6 |
| Comparative Examples 1 | ??110 | ??5.7 | ??5.4???11.1???6.4 |
Embodiment 2
From rare earth, select praseodymium and iron, boron melting in the vacuum intermediate frequency furnace, cast atom and consist of Pr
11.8Fe
84.7B
3.5Alloy pig, according to the method for the manufacturing Magnaglo of embodiment 1, in 800 ℃ inhale hydrogen, dehydrogenation is handled, after be cooled to room temperature and wait to make bonded permanent magnet and use.Method by the manufacturing bonded permanent magnet of embodiment 1 is made bonded permanent magnet with magnetic, and its magnetic property is listed in table 2.
Embodiment 3
From rare earth, select the melting in vacuum arc furnace ignition of neodymium, praseodymium, dysprosium and iron, boron, cast atom and consist of Nd
8Pr
4Dy
1.5Fe
81B
5.5Alloy pig, it is stand-by that the method for making Magnaglos according to embodiment 2 obtains Magnaglo.
Magnaglo and 6% (weight) nylon is mixed, at 7 tons/centimetre
2Pressure under compression molding after 210 ℃ kept 1 hour, make nylon softening, be cooled to room temperature subsequently, magnet is solidified, the bonded permanent magnet magnetic property is listed in table 2.
Embodiment 4
In rare earth, select neodymium,, cast atom and consist of Nd with the melting in intermediate frequency furnace of iron, boron, carbon
12.5Fe
83B
3.5C
1.0Alloy pig.Inhale hydrogen, dehydrogenation processing according to the method for embodiment 1 described manufacturing Magnaglo.Mix with 3% (weight) epoxy resin after being cooled to room temperature, make bonded permanent magnet by the similarity condition of embodiment 1, the magnetic property of bonded permanent magnet is also listed in table 2.
Table 2
| Sample type | Magnetic average particle size (micron) | Bonded permanent magnet density (grams per cubic centimter) | Bonded permanent magnet magnetic characteristic Br 1Hc (BH) max (thousand height) (kilooersted) (hundred Wan Gaoao) |
| Embodiment 2 | ????65 | ??5.7 | ????5.9??13.4??8.0 |
| Embodiment 3 | ????110 | ??5.8 | ????5.4??16.7??5.1 |
| Embodiment 4 | ????110 | ??5.8 | ????5.1??10.2??5.9 |
Embodiment 5
From rare earth, select neodymium and iron, cobalt, boron melting in vacuum arc furnace ignition, cast the atom composition and be expressed as Nd
12.1Fe
72.4Co
11B
4.5Alloy pig.Press the manufacture method of embodiment 1 described rare-earth-iron-boron Magnaglo, select 770 ℃ for inhaling hydrogen, desorption temperature.Mix with 3% (weight) epoxy resin after being cooled to room temperature, make bonded permanent magnet by the similarity condition of embodiment 1, the magnetic property of bonded permanent magnet is listed in table 3.
Embodiment 6
From rare earth, select neodymium and iron, boron, niobium melting in vacuum arc furnace ignition, cast the atom composition and be expressed as Nd
12.1Fe
83.2B
4.5Nb
0.2Alloy pig.Connect the method for embodiment 1 described acquisition Magnaglo, select 900 ℃ to be desorption temperature for inhaling hydrogen temperature and 800 ℃.Cooled Magnaglo and 3% (weight) epoxy resin mixes, and makes bonded permanent magnet by the similarity condition of embodiment 1, and the magnetic property of bonded permanent magnet is listed in table 3.
Embodiment 7
From rare earth, select neodymium and iron, boron melting in vacuum arc furnace ignition, cast the atom composition and be expressed as Nd
15.5Fe
81.5B
3.5Alloy pig.The method of pressing embodiment 1 described acquisition Magnaglo obtains Magnaglo.Cooled Magnaglo places the mild steel die sleeve of internal diameter 15 * 15 * 30mm, 700 ℃ of heating half an hour, after carry out hot extrusion deformation, make it to become closely knit magnet.Subsequently with the magnet behind the hot extrusion deformation, carrying out Mechanical Crushing once more, to become average particle size be the anisotropic magnetic powder of 25 μ m.Mix with 3% (weight) epoxy resin, at 2 tons/centimetre
2Pressure under, in applying compression moulding under the 30 kilooersted pulsed magnetic field situations, subsequently briquetting is placed in the soft rubber cover further closely knit in waiting under the static pressure.Then pressed compact is kept making it in 1 hour to solidify at 140 ℃, anisotropic bonded magnet, magnetic property are also listed in table 3.
Claims (5)
1. a two-phase rare earth--iron--boron alloy magnetic is characterized in that each individual particle is all by R
2Fe
14B and R
2Fe
17Two kinds of fine-grain formations that intermetallic compound is a principal phase, (R represents rare earth element in the formula), these two kinds of intermetallic compounds are that 0.1～10 micron crystal grain constitutes by mean grain size, its percent by volume in material is not less than 90%, and the grainiess in the magnetic powder particle is by the Nd with tetragonal structure
2Fe
14B crystal grain and Nd with water chestnut square structure
2Fe
17Crystal grain is assembled formation, and the atom of alloy material is formed can be expressed as R
xFe
100-x-yB
y, x is 10.5～16 in the formula, and y is 1.5～6.0, and the magnetic hardening that alloy material can the alloy cast ingot form offers is subsequently handled.
2. according to the described two-phase rare earth of claim 1--iron--boron alloy magnetic, it is characterized in that R at least a selection Nd or Pr or Nd, Pr enrichment mishmetal, its content can not be less than 50% of R total amount.(percentage by weight)
3. according to the described two-phase rare earth of claim 1--iron--boron alloy magnetic, it is characterized in that the B in the alloy can be by C, N, Si, Ge, at least a element among the P replaces, but the replacement amount must not surpass 40% (percentage by weight) of B total amount.
4. according to the described two-phase rare earth of claim 1--iron--boron alloy magnetic, it is characterized in that the Fe in the alloy can be by at least a M element substitution, its alternative amount must not be greater than following setting:
20at％Co，?4.5at％Ti，5.0at％Nb，8.0at％Mn，7.5at％V，?5.5at％Cr，
7.0at％Ta，5.5at％Al，9.5at％Zr，5.5at％Ga，8.0at％Mo，7.0at％W
3.0at％Bi，5.5at％Cu，2.5at％Sb，3.5at％Sn，1.5at％Zn，9.0at％Ni
5. the preparation method of a two-phase rare earth--iron--boron alloy magnetic; it is characterized in that preparation technology is--iron--boron ingot casting of at first making the rare earth of required composition; ingot casting can be with responding to or electric arc furnace smelting; smelting is carried out under vacuum or protective atmosphere; subsequently ingot casting is broken into corase particles and places vacuum heat treatment furnace, vacuum degree is 5 * 10
-5Torr, and then the mist of feeding hydrogen or hydrogen and inert gas, make that the hydrogen dividing potential drop reaches 0.1～1 atmospheric pressure in the vacuum chamber, then vacuum chamber is moved in the body of heater that has heated or with stove and heat up, be incubated 10～120 minutes after arriving 200～1000 ℃, make hydrogen occlusion in alloy, and then make it, reduce to less than 1 * 10 until the pressure of hydrogen 600 ℃～1000 ℃ following dehydrogenations
-1Torr is cooled to room temperature then.
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|---|---|---|---|
| CN95102821A CN1061163C (en) | 1995-03-27 | 1995-03-27 | Double-phase rare-earth-iron-boron magnetic powder and its prepn. method |
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|---|---|---|---|
| CN95102821A CN1061163C (en) | 1995-03-27 | 1995-03-27 | Double-phase rare-earth-iron-boron magnetic powder and its prepn. method |
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|---|---|
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| CN102447315A (en) * | 2011-11-04 | 2012-05-09 | 无锡天宝电机有限公司 | Neodymium-iron-boron magnet used by high speed electric machine |
| CN103545079A (en) * | 2013-09-30 | 2014-01-29 | 赣州诚正有色金属有限公司 | Double-principal-phase yttrium-contained permanent magnet and preparing method of double-principal-phase yttrium-contained permanent magnet |
| CN105655076A (en) * | 2016-04-06 | 2016-06-08 | 湖北汽车工业学院 | Multi-main-phase high-coercivity NdFeB permanent magnet material for driving motor and preparation method of multi-main-phase high-coercivity NdFeB permanent magnet material |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0637693B2 (en) * | 1988-01-06 | 1994-05-18 | 株式会社トーキン | Rare earth permanent magnet material excellent in mechanical properties, manufacturing method thereof and inspection method thereof |
| CN1024968C (en) * | 1991-04-20 | 1994-06-08 | 北京科技大学 | Preparation method of rare earth-iron-boron permanent-magnetic powder |
| US5387291A (en) * | 1992-03-19 | 1995-02-07 | Sumitomo Special Metals Co., Ltd. | Process for producing alloy powder material for R-Fe-B permanent magnets and alloy powder for adjusting the composition therefor |
-
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- 1995-03-27 CN CN95102821A patent/CN1061163C/en not_active Expired - Fee Related
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| CN102447315A (en) * | 2011-11-04 | 2012-05-09 | 无锡天宝电机有限公司 | Neodymium-iron-boron magnet used by high speed electric machine |
| CN102447315B (en) * | 2011-11-04 | 2015-02-11 | 无锡天宝电机有限公司 | Neodymium-iron-boron magnet used by high speed electric machine |
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