CN101521068A - Rare earth permanent magnet and method of manufacturing the same - Google Patents

Rare earth permanent magnet and method of manufacturing the same Download PDF

Info

Publication number
CN101521068A
CN101521068A CNA2008101799497A CN200810179949A CN101521068A CN 101521068 A CN101521068 A CN 101521068A CN A2008101799497 A CNA2008101799497 A CN A2008101799497A CN 200810179949 A CN200810179949 A CN 200810179949A CN 101521068 A CN101521068 A CN 101521068A
Authority
CN
China
Prior art keywords
sintered body
powder
alloy
surplus
crystal boundary
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.)
Granted
Application number
CNA2008101799497A
Other languages
Chinese (zh)
Other versions
CN101521068B (en
Inventor
永田浩昭
野村忠雄
美浓轮武久
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Shin Etsu Chemical Co Ltd
Original Assignee
Shin Etsu Chemical Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority claimed from JP2007068823A external-priority patent/JP4482769B2/en
Application filed by Shin Etsu Chemical Co Ltd filed Critical Shin Etsu Chemical Co Ltd
Publication of CN101521068A publication Critical patent/CN101521068A/en
Application granted granted Critical
Publication of CN101521068B publication Critical patent/CN101521068B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Landscapes

  • Hard Magnetic Materials (AREA)
  • Manufacturing Cores, Coils, And Magnets (AREA)
  • Powder Metallurgy (AREA)

Abstract

A rare earth permanent magnet is prepared by disposing a powdered metal alloy containing at least 70 vol% of an intermetallic compound phase on a sintered body of R-Fe-B system, and heating the sintered body having the powder disposed on surface thereof below the sintering temperature of the sintered body in vacuum or in an inert gas for diffusion treatment. The advantages include efficient productivity, excellent magnetic performance, a minimal or zero amount of Tb or Dy used, an increased coercive force, and a minimized decline of remanence.

Description

Rare-earth permanent magnet and preparation method thereof
Technical field
The present invention relates to a kind of R-Fe-B permanent magnet, wherein intermetallic compound combines with the sintered magnet body with the coercive force that improves it and simultaneously its remanent magnetism decline is reduced to minimum, and relates to its preparation method.
Background technology
Because excellent magnetism, the range of application of Nd-Fe-B permanent magnet enlarges day by day.The challenge that nearest environmental problem is brought expands to industrial equipment, electric automobile and wind-driven generator with the range of application of these magnets from electrical home appliances.This just requires further to improve the performance of Nd-Fe-B magnet.
The performance index of magnet comprise remanent magnetism (or residual magnetic flux density) and coercive force.Can be by improving Nd 2Fe 14The bulk factor of B compound and improve crystal orientation and realize that the remanent magnetism of Nd-Fe-B sintered magnet increases.For this reason, made a large amount of improvements.In order to improve coercive force, known have a diverse ways, comprises grain refinement, adopts the alloy composition with bigger Nd content and add and improve coercitive element such as Al and Ga.The most general current method is with the alloy composition that contains Dy or Tb instead of part Nd.
It is believed that the coercitive generation mechanism of Nd-Fe-B magnet is the nucleation type, wherein the nucleation of the reverse magnetic domain at crystal boundary place has determined coercive force.Usually, at crystal boundary or produce the unordered of crystal structure at the interface.If crystal structure is unordered at Nd 2Fe 14The near interface of B compound (it is the magnet primary phase) crystal grain extends some nanometers to depth direction, this generation that will cause the reduction of magnetocrystalline anisotropy and promote reverse magnetic domain so, thereby reduce coercive force and (see K.D.Durst and H.Kronmuller, " THE COERCIVE FIELD OFSINTERED AND MELT-SPUN NdFeB MAGNETS ", Journal of Magnetism and MagneticMaterials, 68 (1987), 63-75).Nd 2Fe 14Dy or Tb have improved the anisotropy field of this compound phase to the replacement of part Nd in the B compound, so have improved coercive force.Yet when adding Dy or Tb in a conventional manner, the loss of remanent magnetism is inevitably, because Dy or Tb replace the near interface that does not occur over just primary phase, and even occurs in the inside of primary phase.Must use the Tb of a certain amount of costliness and Dy also to produce other problem.
In addition, a large amount of trials have been carried out for the coercive force that improves the Nd-Fe-B magnet.A kind of exemplary trial is two alloyages: prepare the Nd-Fe-B magnet by mixing two kinds of different alloy powder and these mixtures of sintering of forming.The powder of alloy A is by R 2Fe 14The B primary phase is formed, and wherein R is mainly Nd and Pr.The powder of alloy B comprises various additional elements, comprises Dy, Tb, Ho, Er, Al, Ti, V and Mo, and the typical case is Dy and Tb.Then alloy A and B are mixed.Meticulous after this pulverizing, compacting in magnetic field, sintering and Ageing Treatment are prepared the Nd-Fe-B magnet thus.The sintered magnet generation high-coercive force that obtains like this makes remanent magnetism descend simultaneously and reduces to minimum, and this is because R 2Fe 14B compound primary phase crystal grain center does not exist Dy or Tb, on the contrary is positioned at (seeing JP-B 5-31807 and JP-A5-21218) near the crystal boundary such as the additional elements of Dy and Tb.Yet in this method, Dy or Tb diffuse into the inside of primary phase crystal grain during sintering, make that be positioned near the thickness that contains the layer of Dy or Tb the crystal boundary is equal to or greater than about 1 micron, the degree of depth that this significantly takes place greater than the reverse magnetic domain nucleation.It is very satisfied that such result still can not make us.
Recently, developed some kinds of methods make element-specific from the surface of R-Fe-B sintered body to diffusion inside so that improve magnet performance.In a kind of exemplary method, use evaporation or sputtering technology deposition of rare-earth metal (as Yb, Dy, Pr or Tb) or Al or Ta on the surface of Nd-Fe-B magnet, with after-baking.Referring to JP-A 2004-296973, JP-A 2004-304038, JP-A 2005-11973; K.T.Park, K.Hiraga and M.Sagawa, " Effect of Metal-Coating and Consecutive HeatTreatment on Coercivity of Thin Nd-Fe-B Sintered Magnets, " Proceedingsof the 16th International Workshop on Rare-Earth Magnets and TheirApplications.Sendai, p.257 (2000); And K.Machida, et al., " GrainBoundary Modification of Nd-Fe-B Sintered Magnet and MagneticProperties, " Abstracts of Spring Meeting of Japan Society of Powder andPowder Metallurgy, 2004, p.202.Another kind of exemplary method relates to the powder and the heat treatment of using rare earth inorganic compound such as fluoride or oxide on the surface of sintered body, as described in WO 2006/043348 A1.Use these methods, be arranged in the crystal boundary that the lip-deep element of sintered body (for example Dy or Tb) during heating treatment passes sintered body structure and diffuse into sintered body inside then.Therefore, Dy or Tb can be at the crystal boundary place or near the intragranular crystal boundary of sintered body primary phase with high concentration enrichment.Compare with above-described pair of alloyage, these methods produce desirable form.Because magnet character has been reacted this form, therefore realized minimizing and coercitive raising of remanent magnetism decline.Yet, utilize these methods of evaporation or sputter when extensive enforcement, to have the many problems relevant, and have bad productivity ratio with unit and step.
Summary of the invention
An object of the present invention is to provide a kind of R-Fe-B sintered magnet, this magnet prepares by the following method: use the dual alloy billet powder and implement DIFFUSION TREATMENT on sintered body, the feature of described magnet is that the coercive force and the minimized remanent magnetism of effective productivity ratio, excellent magnetism, few or zero Tb or Dy use amount, raising descends.Another purpose is to provide the method for this magnet of preparation.
The inventor finds, when by to R-Fe-B sintered body surface applied based on the alloy powder of the intermetallic compound phase of easy efflorescence and when implementing DIFFUSION TREATMENT and adjusting the R-Fe-B sintered body, the method raising that is improved compared to existing technology of the productivity ratio of this method, and the near interface enrichment of the component of this diffusion alloy primary phase crystal grain in sintered body makes coercive force improve and makes the remanent magnetism reduced minimum simultaneously.The present invention is based on this discovery.
The invention provides rare-earth permanent magnet and preparation method thereof, be defined as follows.
[1] a kind of method for preparing rare-earth permanent magnet may further comprise the steps:
Arrange alloy powder consisting of on the sintered body surface of Ra-T1b-Bc, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, and the b of surplus, described alloy powder consist of R 1 i-M 1 jAnd the intermetallic compound phase that comprises at least 70 volume %, wherein R 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, " i " and " j " expression atomic percentage and scope are: 15<j≤99, the i of surplus, and
The sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is heat-treated, so that make the R in the powder 1And M 1In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside.
[2] method in [1], wherein said deposition step comprises: grind and consist of R 1 i-M 1 jAnd the alloy that comprises at least 70 volume % intermetallic compound phases, wherein R 1, M 1, i and j definition as above, grind to form the average particle size particle size powder of 500 μ m at the most, this powder is dispersed in organic solvent or the water, the slurry that obtains is applied in the sintered body surface, and dry.
[3] method in [1] or [2], wherein heat treatment step is included in 200 ℃ and heat-treats to the temperature between (Ts-10) ℃ and continue 1 minute to 30 hours, and wherein Ts represents the sintering temperature of sintered body.
[4] method in [1], [2] or [3], wherein the shape of sintered body comprises having the least part that size is equal to or less than 20mm.
[5] a kind of method for preparing rare-earth permanent magnet may further comprise the steps:
Consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of R 1 xT 2 yM 1 zAnd the intermetallic compound phase that comprises at least 70 volume %, wherein R 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, T 2Be at least a element that is selected among Fe and the Co, M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, x, y and z represent that atomic percentage and scope are: 5≤x≤85,15<z≤95, surplus be y and y greater than 0, and
The sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is heat-treated, so that make the R in the powder 1And M 1In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside.
[6] method in [5], wherein said deposition step comprises: grind and consist of R 1 xT 2 yM 1 zAnd the alloy that comprises the intermetallic compound phase of at least 70 volume %, wherein R 1, T 2, M 1, x, y and z definition as above, grind to form the average particle size particle size powder of 500 μ m at the most, this powder is dispersed in organic solvent or the water, the slurry that obtains is applied on the sintered body surface, and dry.
[7] method in [5] or [6], wherein heat treatment step is included in 200 ℃ and heat-treats to the temperature between (Ts-10) ℃ and continue 1 minute to 30 hours, and wherein Ts represents the sintering temperature of sintered body.
[8] method in [5], [6] or [7], wherein the shape of sintered body comprises having the least part that size is equal to or less than 20mm.
[9] a kind of rare-earth permanent magnet, it is prepared as follows: consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage table and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of R 1 i-M 1 jAnd the intermetallic compound phase that comprises at least 70 volume %,, R wherein 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, " i " and " j " expression atomic percentage and scope are: 15<j≤99, the i of surplus, the sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is then heat-treated, wherein
R in the powder 1And M 1In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside, thereby the coercive force of described magnet brought up to the magnetic that is higher than former sintered body.
[10] a kind of rare-earth permanent magnet, it is prepared as follows: consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of R 1 xT 2 yM 1 zAnd the intermetallic compound phase that comprises at least 70 volume %, wherein R 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, T 2Be at least a element that is selected among Fe and the Co, M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, x, y and z represent that atomic percentage and scope are: 5≤x≤85,15<z≤95, surplus is y and greater than 0, the sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is then heat-treated, wherein
R in the powder 1And M 1In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside, thereby the coercive force of described magnet brought up to the magnetic that is higher than former sintered body.
[11] a kind of method for preparing rare-earth permanent magnet may further comprise the steps:
Consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of M 1 d-M 2 eAnd the intermetallic compound phase that comprises at least 70 volume %, wherein M 1And M 2Each is selected from least a element among Al, Si, C, P, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, M naturally 1With M 2Difference, " d " and " e " expression atomic percentage and scope are: 0.1≤e≤99.9, the d of surplus, then
The sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is heat-treated, so that make M and M in the powder 2In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside.
[12] method in [11], wherein said deposition step comprises: grind and consist of M 1 d-M 2 eAnd the alloy that comprises the intermetallic compound phase of at least 70 volume %, wherein M 1, M 2, d and e definition as above, grind to form the average particle size particle size powder of 500 μ m at the most, this powder is dispersed in organic solvent or the water, the gained slurry is administered to the surface of this sintered body, and dry.
[13] method in [11] or [12], wherein heat treatment step is included in 200 ℃ and heat-treated 1 minute to 30 hours to the temperature between (Ts-10) ℃, and wherein Ts represents the sintering temperature of sintered body.
[14] method in [11], [12] or [13], wherein the shape of sintered body comprises having the least part that size is equal to or less than 20mm.
[15] a kind of rare-earth permanent magnet, it is prepared as follows: consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of M 1 d-M 2 eAnd the intermetallic compound phase that comprises at least 70 volume %, wherein M 1And M 2Each is selected from least a element among Al, Si, C, P, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, M naturally 1With M 2Different, " d " and " e " expression atomic percentage and scope are: 0.1≤e≤99.9, the d of surplus, the sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is then heat-treated, wherein
M in the powder 1And M 2In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside, thereby the coercive force of this magnet brought up to the magnetic that is higher than former sintered body.
Benefit of the present invention
According to the present invention, the R-Fe-B sintered magnet is by the alloy powder of compound between using based on easy crushing metal on the sintered body and implements the DIFFUSION TREATMENT preparation.The advantage of gained magnet comprises that the coercive force and the minimized remanent magnetism of productivity ratio efficiently, excellent magnetism, few or zero Tb or Dy use amount, raising descend.
Embodiment
In brief, prepare the R-Fe-B sintered magnet in the following way according to the present invention: on sintered body, use the dual alloy billet powder and implement DIFFUSION TREATMENT.The advantage of the magnet that obtains comprises excellent magnetism and few Tb or Dy use amount or does not have Tb or Dy.
The parent material that the present invention uses is to consist of R a-T 1 b-B cSintered body, it is commonly called " female sintered body ".Here R is at least a element that is selected from the rare earth element that comprises scandium (Sc) and yttrium (Y), especially is selected from Sc, Y, La, Ce, Pr, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Yb and Lu.Preferably, most of R are Nd and/or Pr.Preferably, comprise that the rare earth element of Sc and Y accounts for the 12-20 atom % (at%) of whole sintered body, and more preferably account for the 14-18at% of whole sintered body.T 1It is at least a element in chosen from Fe (Fe) and the cobalt (Co).B is a boron, and preferably accounts for the 4-7at% of whole sintered body.Especially, when B is 5-6at%, realized coercitive remarkable improvement by DIFFUSION TREATMENT.Surplus is by T 1Form.
Preparation is used for the alloy of female sintered body by the following method: at vacuum or inert gas atmosphere (preferred argon atmospher) deposite metal or alloy raw material, then with melt cast to flat mould, book mould or carry out Strip casting.A kind of possible replacement scheme is a so-called pair-alloyage, and this method comprises: preparation and the R that constitutes the associated alloys primary phase respectively 2Fe 14The B compound is formed approaching alloy and the rich rare earth alloy that serves as the liquid phase auxiliary agent under sintering temperature, with their fragmentations, weigh then and mix.Especially, form approaching alloy with primary phase and stand the homogenizing processing where necessary, so that improve this R 2Fe 14The amount of B compound phase, residual because primary crystal α-Fe has probably, this depends on cooldown rate and alloy composition between casting cycle.It is to continue at least one hour heat treatment down in 700-1200 ℃ in vacuum or Ar atmosphere that homogenizing is handled.As an alternative, can prepare the alloy that this is formed near primary phase by the Strip casting technology.For the rich rare earth alloy that serves as the liquid phase auxiliary agent, can use melt quenching and Strip casting technology and above-mentioned foundry engieering.
Usually the broken or corase grind size to 0.05 to 3mm with alloy, particularly 0.05 to 1.5mm.Broken step adopts Brown mill or hydrogenation to pulverize, and preferably adopts hydrogenation to pulverize for those alloys of Strip casting.Then, for example, on the jet mill that uses high pressure nitrogen, it is 0.2 to 30 μ m that the corase meal fine powder is broken to average particle size particle size, particularly 0.5 to 20 μ m.
Fine powder is pressed shape with forming press under magnetic field.Then, green compact are put into sintering furnace, in this sintering furnace, usually under 900-1250 ℃ of temperature, preferably under 1000-1100 ℃, in vacuum or inert gas atmosphere, carry out sintering.The agglomerate of Huo Deing comprises 60-99 volume % like this, the R of the tetragonal crystal system of preferred 80-98 volume % 2Fe 14The B compound is as primary phase, surplus be 0.5-20 volume % rich rare earth mutually and 0.1-10 volume % be selected from least a compound in the rare earth oxide, and deposit carbide, nitride and the hydroxide of impurity by chance, with and composition thereof or compound.
Can or be processed into reservation shape with the machine work of gained agglomerate.In the present invention, wait to be diffused into the R of sintered body inside 1And/or M 1And T 2, or M 1And/or M 2Provide from this sintered body surface.Therefore, if the part of this sintered body minimum has excessive size, purpose so of the present invention just can not realize.Therefore, described shape comprises that size is equal to or less than 20mm, preferably is equal to or less than 10mm, and lower limit is equal to or greater than the least part of 0.1mm.Described sintered body comprises the restricted especially largest portion of size, and the largest portion size wishes to be equal to or less than 200mm.
According to the present invention, alloy powder is arranged on the described sintered body and stands DIFFUSION TREATMENT.It is to consist of R 1 i-M 1 jOr R 1 xT 2 yM 1 zOr M 1 d-M 2 ePowder metallurgy.This alloy is commonly called " diffusion alloy ".R herein 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, and preferred most of R 1Be Nd and Pr.M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi.At alloy M 1 d-M 2 eIn, M 1And M 2Different mutually, and be selected from the group that above-mentioned element constitutes.T 2Be Fe and/or Co.At alloy R 1 i-M 1 jIn, M 1(that is, j=15-99), surplus is R to account for 15-99at% 1At alloy R 1 xT 2 yM 1 zIn, M 1Account for 15-95at% (that is, z=15-95), and R 1(that is, x=5-85), surplus is T to account for 5-85at% 2In other words, y〉0, and T 2Be preferably 0.5-75at%.At alloy M 1 d-M 2 eIn, M 2Account for 0.1-99.9at%, in other words, the scope of e is: 0.1≤e≤99.9.M 1Be to remove M 2Remainder afterwards, promptly d is a surplus.
Described diffusion alloy can comprise idol and deposit impurity such as nitrogen (N) and oxygen (O), and the acceptable total amount of these impurity is equal to or less than 4at%.
The invention is characterized in that described diffusion alloy material comprises the intermetallic compound phase of at least 70 volume % in its structure.If described diffusion material is made of single metal or eutectic alloy, then be difficult for pulverizing, and need special technique, for example carry out efflorescence to obtain fine powder.On the contrary, described intermetallic compound is hard and frangible mutually usually in essence.When the alloy based on these intermetallic compound phases is used as diffusion material, can be simply by utilizing the alloy preparation or the reducing mechanism that in making the R-Fe-B sintered magnet, use easily to obtain fine powder.This is very favourable aspect productivity ratio.Because described diffusion alloy material is advantageously pulverized easily, therefore preferably comprise at least 70 volume % and the more preferably intermetallic compound phase of at least 90 volume %.Should be understood that term " volume % " can exchange with the area percentage of intermetallic compound in the alloy structure cross section.
Can by be prepared as follows comprise at least 70 volume % with R 1 i-M 1 j, R 1 xT 2 yM 1 zOr M 1 d-M 2 eThe diffusion alloy of intermetallic compound phase of expression, as the alloy of female sintered body as described in being used for: at vacuum or inert gas atmosphere (preferred argon atmospher) motlten metal or alloy raw material, then with melt cast in flat mould or book mould.Electric arc melting or Strip casting method also are acceptable.Then, utilize Brown mill or hydrogenation to pulverize with alloy broken or corase grind to the size of about 0.05-3mm, particularly about 0.05-1.5mm.Then, with the meticulous pulverizing of described corase meal, for example by ball mill, vibration milling or utilize the jet mill of high pressure nitrogen.Powder particle size is more little, and diffuser efficiency is high more.Described diffusion alloy comprises with R 1 i-M 1 j, R 1 xT 2 yM 1 zOr M 1 d-M 2 eThe intermetallic compound phase of expression, after powdered, preferred average particle size particle size is equal to or less than 500 μ m, more preferably is equal to or less than 300 μ m, and even more preferably is equal to or less than 100 μ m.Yet if described particle size is too little, the influence of surface oxidation just becomes significantly so, and operational hazards.Therefore the lower limit of average particle size particle size preferably is equal to or greater than 1 μ m.Can use the particle size distribution measuring instrument that for example relies on laser diffractometry or the like, press weight-average diameter D 50(particle diameter or median diameter when accumulating 50 weight %) measures " average particle size particle size " used herein.
After diffusion-alloyed powder was arranged on female sintered body surface, described female sintered body and diffusion-alloyed powder had been equal to or less than in the atmosphere of vacuum or inert gas such as argon (Ar) or helium (He) under the temperature of sintered body sintering temperature (be expressed as Ts unit be ℃) and are heat-treating.This heat treatment is called as " DIFFUSION TREATMENT ".By this DIFFUSION TREATMENT, the R in the diffusion alloy 1, M 1Or M 2Be diffused near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of described sintered body inside.
In the following way diffusion-alloyed powder is arranged on female sintered body surface: for example be dispersed in described powder in the water or in the organic solvent to form slurry, sintered body is immersed slurry, then by air-dry, the heated-air drying or the sintered body of dry dipping in a vacuum.Spraying also is fine.Described slurry can comprise the powder of 1-90 weight %, and the powder of preferred 5-70 weight %.
When the activity coefficient from the element of the diffusion alloy that is applied is minimum 1 volume %, preferably obtains better result during at least 10 volume %, described activity coefficient is with the mean value calculation in the sintered body surrounding space that is equal to or less than the 1mm distance that stretches out from the sintered body surface.The upper limit of activity coefficient is generally equal to or less than 95 volume %, and preferably is equal to or less than 90 volume %, although this is not important.
The condition of DIFFUSION TREATMENT changes with the type and the composition of diffusion alloy, and preferably selects to make at the crystal boundary place of sintered body inside and/or near the enrichment R intragranular crystal boundary of sintered body primary phase 1And/or M 1And/or M 2The temperature of DIFFUSION TREATMENT is equal to or less than the sintering temperature (be expressed as Ts unit ℃) of sintered body.If the temperature of DIFFUSION TREATMENT is higher than Ts, then following problem can take place: (1) thus the structure of sintered body may change make magnetic deterioration and (2) thus because thermal deformation can not keep mach size.Therefore, the temperature of DIFFUSION TREATMENT is equal to or less than Ts ℃ of sintered body, and preferably is equal to or less than (Ts-10) ℃.Can suitably select the lower limit of temperature, yet be typically at least 200 ℃, and preferably at least 350 ℃.The time of DIFFUSION TREATMENT is typically 1 minute to 30 hours.When being less than 1 minute, DIFFUSION TREATMENT is incomplete.If the processing time, then the structure of sintered body may change greater than 30 hours, thereby the component oxidation or the evaporation that take place inevitably make magnetic deterioration, perhaps M 1Or M 2Not only in the crystal boundary place and/or near the enrichment intragranular crystal boundary of sintered body primary phase of sintered body inside, and diffuse into the inside of primary phase crystal grain.The preferred time of DIFFUSION TREATMENT is 1 minute to 10 hours, more preferably 10 minutes to 6 hours.
By suitable DIFFUSION TREATMENT, be arranged in the component R of the lip-deep diffusion alloy of sintered body 1, M 1Or M 2Diffuse into sintered body, main simultaneously crystal boundary migration along sintered body structure inside.This causes following structure: R wherein 1, M 1Or M 2Be enriched near the crystal boundary place and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside.
So the coercive force of the permanent magnet that obtains is improved, because R 1, M 1Or M 2Thereby diffusion improved near the form the primary phase crystal boundary in this structure suppressed primary phase crystal boundary place magnetocrystalline anisotropy decline or produce cenotype at the crystal boundary place.Because described diffusion alloy element does not diffuse into the inside of primary phase crystal grain, therefore suppressed the decline of remanent magnetism.This magnet is high performance permanent magnet.
After the DIFFUSION TREATMENT, described magnet can further be accepted Ageing Treatment to improve coercitive enhancing under 200 to 900 ℃ temperature.
Embodiment
Provide embodiment below and further set forth the present invention, but the present invention is not limited to these embodiment.
Embodiment 1 and Comparative Examples 1
Be prepared as follows magnet alloy: use Nd, Fe and the Co metal of purity at least 99 weight %, and ferroboron, in argon atmospher medium-high frequency heat fused, then alloy melt is poured in the casting in bronze type.On the Brown mill, described alloy ground to form the particle size corase meal of 1mm at the most.
Subsequently, meticulous being ground into of described corase meal had the fine powder that the mass median particle diameter is 5.2 μ m utilizing on the jet mill of high pressure nitrogen.At about 300kg/cm 2Pressure under to described fine powder press just as the time at 1592kAm -1Magnetic field in be orientated.Then, green compact are put into vacuum sintering furnace, in this vacuum sintering furnace under 1060 ℃ with its sintering 1.5 hours, obtain agglomerate.Use the diamond grinding instrument, on all surface, described agglomerate is machined to the shape of size 4 * 4 * 2mm.With alkaline solution, deionized water, nitric acid and deionized water it is cleaned successively, and dry, obtain to consist of Nd 16.0Fe Ba1Co 1.0B 5.3Female sintered body.
Use the Nd of purity at least 99 weight % and Al metal and in argon atmospher electric arc melting, prepare and consist of Nd 33Al 67And mainly by intermetallic compound phase NdAl 2The diffusion alloy that constitutes.On ball mill, utilize organic solvent to be ground into the fine powder that the mass median particle diameter is 7.8 μ m with described alloy is meticulous.By electron probe microanalysis (EPMA) (EPMA), described alloy comprises the intermetallic compound phase NdAl of 94 volume % 2
The described diffusion-alloyed powder of 15g mixed forming slurry with 45g ethanol, under ultrasonic agitation, female sintered body immersed in the described slurry 30 seconds.Take out sintered body then and use heated-air drying immediately.
The sintered body that is coated with diffusion-alloyed powder carries out one hour DIFFUSION TREATMENT in a vacuum under 800 ℃, produce the magnet of embodiment 1.Do not having under the situation of diffusion-alloyed powder, described sintered body is being carried out one hour heat treatment separately in a vacuum under 800 ℃, producing the magnet of Comparative Examples 1.
Table 1 has gathered intermetallic compound main in the composition, diffusion alloy of female sintered body in embodiment 1 and the Comparative Examples 1 and diffusion alloy, the temperature and time of DIFFUSION TREATMENT.Table 2 shows the magnetic property of the magnet of embodiment 1 and Comparative Examples 1.As can be seen, the coercive force of the magnet of embodiment 1 (Hcj) is than the big 1300kAm of Comparative Examples 1 -1, and remanent magnetism (Br) decline only is 15mT.
Table 1
Figure A200810179949D00161
Table 2
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 1 1.310 1970 332
Comparative Examples 1 1.325 670 318
Embodiment 2 and Comparative Examples 2
Be prepared as follows magnet alloy: use Nd, Fe and the Co metal of purity at least 99 weight %, and ferroboron, in argon atmospher medium-high frequency heat fused, then alloy melt is poured in the casting in bronze type.On the Brown mill, described alloy ground to form the particle size corase meal of 1mm at the most.
Subsequently, meticulous being ground into of described corase meal had the fine powder that the mass median particle diameter is 5.2 μ m utilizing on the jet mill of high pressure nitrogen.At about 300kg/cm 2Pressure under to described fine powder press just as the time at 1592kAm -1Magnetic field in be orientated.Then, green compact are put into vacuum sintering furnace, in this vacuum sintering furnace under 1060 ℃ with its sintering 1.5 hours, obtain agglomerate.Use the diamond grinding instrument, on all surface, described agglomerate is machined to the shape of size 4 * 4 * 2mm.With alkaline solution, deionized water, nitric acid and deionized water it is cleaned successively, and dry, obtain to consist of Nd 16.0Fe Ba1Co 1.0B 5.3Female sintered body.
Utilize purity be Nd, Fe, Co and the Al metal of at least 99 weight % and in argon atmospher electric arc melting, prepare and have the Nd of consisting of 35Fe 25Co 20Al 20Diffusion alloy.On ball mill, utilize organic solvent to be ground into the fine powder that the mass median particle diameter is 7.8 μ m with described alloy is meticulous.Analyze by EPMA, described alloy comprises Nd (FeCoAl) 2, Nd 2(FeCoAl) and Nd 2(FeCoAl) 17Deng the intermetallic compound phase, has the intermetallic compound phase of 87 volume % altogether.
The described diffusion-alloyed powder of 15g mixed forming slurry with 45g ethanol, under ultrasonic agitation, female sintered body immersed in the described slurry 30 seconds.Take out sintered body then and use heated-air drying immediately.
The sintered body that is coated with diffusion-alloyed powder carries out one hour DIFFUSION TREATMENT in a vacuum under 800 ℃, produce the magnet of embodiment 2.Do not having under the situation of diffusion-alloyed powder, described sintered body is being carried out one hour heat treatment separately in a vacuum under 800 ℃, producing the magnet of Comparative Examples 2.
Table 3 has gathered intermetallic compound main in the composition, diffusion alloy of female sintered body in embodiment 2 and the Comparative Examples 2 and diffusion alloy, the temperature and time of DIFFUSION TREATMENT.Table 4 shows the magnetic property of the magnet of embodiment 2 and Comparative Examples 2.As can be seen, the coercive force of the magnet of embodiment 2 (Hcj) is than the big 1150kAm of Comparative Examples 2 -1, and its remanent magnetism decline only is 18mT.
Table 3
Figure A200810179949D00171
Table 4
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 2 1.307 1820 330
Comparative Examples 2 1.325 670 318
Embodiment 3
Be prepared as follows magnet alloy: use Nd, Fe and the Co metal of purity at least 99 weight %, and ferroboron, in argon atmospher medium-high frequency heat fused, then alloy melt is poured in the casting in bronze type.On the Brown mill, described alloy ground to form the particle size corase meal of 1mm at the most.
Subsequently, be ground into the fine powder that the mass median particle diameter is 5.2 μ m with described corase meal is meticulous utilizing on the jet mill of high pressure nitrogen.At about 300kg/cm 2Pressure under to described fine powder press just as the time at 1592kAm -1Magnetic field in be orientated.Then, green compact are put into vacuum sintering furnace, in this vacuum sintering furnace under 1060 ℃ with its sintering 1.5 hours, obtain agglomerate.Utilize the diamond grinding instrument, on all surface, described agglomerate is machined to the shape (embodiment 3-1) of size 50 * 50 * 15mm or is of a size of the shape (embodiment 3-2) of 50 * 50 * 25mm.With alkaline solution, deionized water, nitric acid and deionized water it is cleaned successively, and dry, obtain to consist of Nd 16.0Fe Ba1Co 1.0B 5.3Female sintered body.
Utilize purity be the Nd of at least 99 weight % and Al metal and in argon atmospher electric arc melting, prepare and consist of Nd 33Al 67And mainly by intermetallic compound phase NdAl 2The diffusion alloy of forming.On ball mill, utilize organic solvent to be ground into the fine powder that the mass median particle diameter is 7.8 μ m with described alloy is meticulous.Analyze by EPMA, described alloy comprises the intermetallic compound phase NdAl of 93 volume % 2
The 30g diffusion-alloyed powder is mixed the formation slurry with 90g ethanol, the female sintered body with embodiment 3-1 and 3-2 under ultrasonic agitation immersed respectively wherein 30 seconds.Take out sintered body then and use heated-air drying immediately.
The sintered body that is coated with diffusion-alloyed powder carries out 6 hours DIFFUSION TREATMENT in a vacuum under 850 ℃, produce the magnet of embodiment 3-1 and 3-2.
Table 5 has gathered main intermetallic compound, the temperature and time of DIFFUSION TREATMENT and the size of sintered body least part in the composition, diffusion alloy of the female sintered body of embodiment 3-1 and 3-2 and diffusion alloy.Table 6 shows the magnetic property of the magnet of embodiment 3-1 and 3-2.As can be seen, be of a size of among the embodiment 3-1 of 15mm 1584kAm at the sintered body least part -1Coercive force show that DIFFUSION TREATMENT produces bigger effect.By contrast, sintered body least part size surpasses the sintered body of 20mm, for example is of a size of the sintered body of 25mm among the embodiment 3-2, and DIFFUSION TREATMENT produces less influence.
Table 5
Figure A200810179949D00181
Table 6
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 3-1 1.305 1584 329
Embodiment 3-2 1.305 653 308
Embodiment 4 to 52
Press embodiment 1, apply various female sintered bodies and carry out the DIFFUSION TREATMENT certain time at a certain temperature with various diffusion alloy.Table 7 and 8 has gathered the temperature and time of the type of compound between the composition, the major metal in the diffusion alloy of female sintered body and diffusion alloy and quantity, DIFFUSION TREATMENT.Table 9 and 10 shows the magnetic property of magnet.Notice that the amount of intermetallic compound is to adopt the EPMA assay determination in the diffusion alloy.
Table 7
Figure A200810179949D00191
Table 8
Table 9
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 4 1.300 1871 327
Embodiment 5 1.315 1831 333
Embodiment 6 1.310 1879 331
Embodiment 7 1.305 1966 329
Embodiment 8 1.240 844 286
Embodiment 9 1.260 1059 297
Embodiment 10 1.280 892 304
Embodiment 11 1.335 1059 339
Embodiment 12 1.252 756 292
Embodiment 13 1.245 780 288
Embodiment 14 1.225 892 283
Embodiment 15 1.220 1855 282
Embodiment 16 1.265 1887 305
Embodiment 17 1.306 1528 318
Embodiment 18 1.351 1250 341
Embodiment 19 1.305 1457 323
Embodiment 20 1.348 1297 338
Embodiment 21 1.311 1520 322
Embodiment 22 1.308 1719 326
Embodiment 23 1.298 1767 322
Embodiment 24 1.304 1695 316
Embodiment 25 1.306 1703 325
Embodiment 26 1.273 1306 304
Embodiment 27 1.265 1361 305
Embodiment 28 1.292 1106 312
Embodiment 29 1.254 1258 291
Embodiment 30 1.325 1083 332
Table 10
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 31 1.300 1910 324
Embodiment 32 1.315 1871 329
Embodiment 33 1.310 1934 328
Embodiment 34 1.318 1958 330
Embodiment 35 1.305 1966 326
Embodiment 36 1.314 1974 328
Embodiment 37 1.311 2006 330
Embodiment 38 1.263 1528 297
Embodiment 39 1.220 1130 269
Embodiment 40 1.180 1186 251
Embodiment 41 1.235 1051 278
Embodiment 42 1.245 1146 289
Embodiment 43 1.242 1154 286
Embodiment 44 1.104 971 221
Embodiment 45 1.262 1043 293
Embodiment 46 1.173 1098 255
Embodiment 47 1.307 971 311
Embodiment 48 1.285 1178 309
Embodiment 49 1.311 1226 325
Embodiment 50 1.268 939 298
Embodiment 51 1.252 1003 290
Embodiment 52 1.352 860 341
Embodiment 53
Be prepared as follows magnet alloy: use Nd, Fe and the Co metal of purity at least 99 weight %, and ferroboron, in argon atmospher medium-high frequency heat fused, then alloy melt is poured in the casting in bronze type.On the Brown mill, described alloy ground to form the particle size corase meal of 1mm at the most.
Subsequently, be ground into the fine powder that the mass median particle diameter is 5.2 μ m with described corase meal is meticulous utilizing on the jet mill of high pressure nitrogen.At about 300kg/cm 2Pressure under to described fine powder press just as the time at 1592kAm -1Magnetic field in be orientated.Then, green compact are put into vacuum sintering furnace, in this vacuum sintering furnace under 1060 ℃ with its sintering 1.5 hours, obtain agglomerate.Use the diamond grinding instrument, on all surface, described agglomerate is machined to the shape of size 4 * 4 * 2mm.With alkaline solution, deionized water, nitric acid and deionized water it is cleaned successively, and dry, obtain to consist of Nd 16.0Fe Ba1Co 1.0B 5.3Female sintered body.
Utilize purity be the Al of at least 99 weight % and Co metal and in argon atmospher electric arc melting, prepare and consist of Al 50Co 50(atom %) and the diffusion alloy that mainly constitutes by intermetallic compound phase AlCo.On ball mill, utilize organic solvent to be ground into the fine powder that the mass median particle diameter is 8.5 μ m with described alloy is meticulous.Analyze by EPMA, described alloy comprises the intermetallic compound phase AlCo of 93 volume %.
The described diffusion-alloyed powder of 15g mixed forming slurry with 45g ethanol, under ultrasonic agitation, female sintered body immersed in this slurry 30 seconds.Take out sintered body then and use heated-air drying immediately.
The sintered body that is coated with diffusion-alloyed powder carries out DIFFUSION TREATMENT in a vacuum and continues for an hour under 800 ℃, produce the magnet of embodiment 53.
Table 11 has gathered the temperature and time of compound, DIFFUSION TREATMENT between the composition, the major metal in the diffusion alloy of female sintered body among the embodiment 53 and diffusion alloy.Table 12 shows the magnetic property of the magnet of embodiment 53.As can be seen, the coercive force of the magnet of embodiment 53 is than the Comparative Examples 1 big 1170kAm of front -1, and remanent magnetism decline only is 20mT.
Table 11
Table 12
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 53 1.305 1840 329
Embodiment 54 and Comparative Examples 3
Be prepared as follows magnet alloy: use Nd, Fe and the Co metal of purity at least 99 weight %, and ferroboron, in argon atmospher medium-high frequency heat fused, then alloy melt is poured in the casting in bronze type.On the Brown mill, described alloy ground to form the particle size corase meal of 1mm at the most.
Subsequently, be ground into the fine powder that the mass median particle diameter is 5.2 μ m with described corase meal is meticulous utilizing on the jet mill of high pressure nitrogen.At about 300kg/cm 2Pressure under to described fine powder press just as the time at 1592kAm -1Magnetic field in be orientated.Then, green compact are put into vacuum sintering furnace, in this vacuum sintering furnace under 1060 ℃ with its sintering 1.5 hours, obtain agglomerate.Utilize the diamond grinding instrument, on all surface, agglomerate is machined to the shape (embodiment 54) of size 50 * 50 * 15mm or is of a size of the shape (Comparative Examples 3) of 50 * 50 * 25mm.With alkaline solution, deionized water, nitric acid and deionized water it is cleaned successively, and dry, obtain to consist of Nd 16.0Fe Ba1Co 1.0B 5.3Female sintered body.
Utilize purity be the Al of at least 99 weight % and Co metal and in argon atmospher electric arc melting, prepare and consist of Al 50Co 50(atom %) and the diffusion alloy that mainly constitutes by intermetallic compound phase AlCo.On ball mill, utilize organic solvent to be ground into the fine powder that the mass median particle diameter is 8.5 μ m with described alloy is meticulous.Analyze by EPMA, described alloy comprises the intermetallic compound phase AlCo of 92 volume %.
The described diffusion-alloyed powder of 30g mixed forming slurry with 90g ethanol, under ultrasonic agitation, female sintered body of embodiment 54 and Comparative Examples 3 immersed in this slurry 30 seconds.Take out sintered body then and use heated-air drying immediately.
The sintered body that is coated with diffusion-alloyed powder is carried out DIFFUSION TREATMENT in a vacuum continue 6 hours under 850 ℃, produce the magnet of embodiment 54 and Comparative Examples 3.
Table 13 has gathered compound, the temperature and time of DIFFUSION TREATMENT and the size of sintered body least part between the composition, the major metal in the diffusion alloy of female sintered body of embodiment 54 and Comparative Examples 3 and diffusion alloy.Table 14 shows the magnetic property of the magnet of embodiment 54 and Comparative Examples 3.As can be seen, the sintered body least part is of a size of among the embodiment 54 of 15mm, 1504kAm -1Coercive force demonstrate DIFFUSION TREATMENT and produced bigger effect.By contrast, when the least part of sintered body has size above 20mm, the size of 25mm in the Comparative Examples 3 for example, as coercive force almost increase confirm that DIFFUSION TREATMENT does not almost tell on.
Table 13
Figure A200810179949D00241
Table 14
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 54 1.306 1504 328
Comparative Examples 3 1.306 710 309
Embodiment 55 to 84
According to embodiment 53, apply different female sintered bodies and carry out the DIFFUSION TREATMENT of uniform temperature certain hour with different diffusion-alloyed powders.Table 15 has gathered the type mutually of compound between the composition, the major metal in the diffusion alloy of female sintered body and diffusion alloy and the temperature and time of quantity, DIFFUSION TREATMENT.Table 16 shows the magnetic property of magnet.Notice that the amount of intermetallic compound phase is to adopt the EPMA assay in the diffusion alloy.
Table 15
Figure A200810179949D00251
Table 16
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 55 1.303 1815 327
Embodiment 56 1.295 1847 320
Embodiment 57 1.290 1982 319
Embodiment 58 1.315 1902 334
Embodiment 59 1.282 1688 310
Embodiment 60 1.297 1815 324
Embodiment 61 1.190 1664 268
Embodiment 62 1.173 1258 260
Embodiment 63 1.246 1186 290
Embodiment 64 1.370 1473 350
Embodiment 65 1.305 1528 327
Embodiment 66 1.313 1401 329
Embodiment 67 1.312 1656 325
Embodiment 68 1.296 1449 317
Embodiment 69 1.236 1640 288
Embodiment 70 1.312 1576 330
Embodiment 71 1.247 1656 295
Embodiment 72 1.309 1775 320
Embodiment 73 1.295 1369 323
Embodiment 74 1.335 1290 340
Embodiment 75 1.331 1242 337
Embodiment 76 1.301 1178 322
Embodiment 77 1.263 1297 295
Embodiment 78 1.258 1098 292
Embodiment 79 1.314 1616 330
Embodiment 80 1.303 1703 322
Embodiment 81 1.311 1560 326
Embodiment 82 1.342 1210 342
Embodiment 83 1.227 1043 280
Embodiment 84 1.290 971 314
Embodiment 85 to 92 and Comparative Examples 4
Be prepared as follows magnet alloy: use Nd, Fe and the Co metal of purity at least 99 weight %, and ferroboron, in argon atmospher medium-high frequency heat fused, then alloy melt is poured in the casting in bronze type.On the Brown mill, described alloy ground to form the particle size corase meal of 1mm at the most.
Subsequently, be ground into the fine powder that the mass median particle diameter is 4.2 μ m with described corase meal is meticulous utilizing on the jet mill of high pressure nitrogen.Atmosphere is become inert gas atmosphere to suppress the oxidation of fine powder.Then, at about 300kg/cm 2Pressure under to described fine powder press just as the time at 1592kAm -1Magnetic field in be orientated.Then, green compact are put into vacuum sintering furnace, in this vacuum sintering furnace,, obtain agglomerate 1060 ℃ of following sintering 1.5 hours.Utilize the diamond grinding instrument, on all surface, agglomerate is machined to the shape of size 4 * 4 * 2mm.With alkaline solution, deionized water, nitric acid and deionized water it is cleaned successively, and dry, obtain to consist of Nd 13.8Fe Ba1Co 1.0B 6.0Female sintered body.
Utilize Dy, Tb, Nd, Pr, Co, Ni and the Al metal of purity at least 99 weight % and in argon atmospher electric arc melting, prepare the different diffusion alloy of forming (atom%) that have shown in table 17.On ball mill, utilize organic solvent to be ground into the fine powder that the mass median particle diameter is 7.9 μ m with each alloy is meticulous.Analyze by EPMA, each alloy all comprises the intermetallic compound phase of 94 volume %, and is shown in table 17.
The 15g diffusion-alloyed powder is mixed the formation slurry with 45g ethanol, under ultrasonic agitation, each female sintered body was immersed this slurry 30 seconds.Take out this sintered body then and use heated-air drying immediately.
The sintered body that is coated with diffusion-alloyed powder is carried out 10 hours DIFFUSION TREATMENT in a vacuum under 840 ℃, produce the magnet of embodiment 85 to 92.The magnet of Comparative Examples 4 also obtains by repeating above-mentioned operation, does not just use diffusion-alloyed powder.
Table 17 has gathered the temperature and time of compound, DIFFUSION TREATMENT between the composition, the major metal in the diffusion alloy of female sintered body of embodiment 85 to 92 and Comparative Examples 4 and diffusion alloy.Table 18 shows the magnetic property of the magnet of described embodiment 85 to 92 and Comparative Examples 4.As can be seen, the coercive force of the magnet of embodiment 85 to 92 is significantly greater than the coercive force of Comparative Examples 4, and remanent magnetism descends and only is about 10mT.
Table 17
Figure A200810179949D00281
Table 18
Br(T) Hcj(kAm -1) (BH) max(kJ/m 3)
Embodiment 85 1.411 1720 386
Embodiment 86 1.409 1740 384
Embodiment 87 1.412 1880 388
Embodiment 88 1.410 1890 385
Embodiment 89 1.414 1570 387
Embodiment 90 1.413 1580 386
Embodiment 91 1.409 1640 384
Embodiment 92 1.408 1660 382
Comparative Examples 4 1.422 890 377

Claims (15)

1. method for preparing rare-earth permanent magnet may further comprise the steps:
Consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of R 1 i-M 1 jAnd the intermetallic compound phase that comprises at least 70 volume %, wherein R 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, " i " and " j " expression atomic percentage and scope are: 15<j≤99, the i of surplus and
The sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is heat-treated, so that make the R in the powder 1And M 1In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside.
2. method according to claim 1, wherein said deposition step comprises: grind and consist of R 1 i-M 1 jAnd the alloy that comprises at least 70 volume % intermetallic compound phases, wherein R 1, M 1, i and j definition as above, grind to form the average particle size particle size powder of 500 μ m at the most, described powder is dispersed in organic solvent or the water, the slurry that obtains is applied in the surface of sintered body, and dry.
3. method according to claim 1, wherein said heat treatment step are included in 200 ℃ and carry out 1 minute to 30 hours heat treatment between (Ts-10) ℃, and wherein Ts represents the sintering temperature of sintered body.
4. method according to claim 1, the shape of wherein said sintered body comprise having the least part that size is equal to or less than 20mm.
5. method for preparing rare-earth permanent magnet may further comprise the steps:
Consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of R 1 xT 2 yM 1 zAnd the intermetallic compound phase that comprises at least 70 volume %, wherein R 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, T 2Be at least a element that is selected among Fe and the Co, M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, x, y and z represent that atomic percentage and scope are: 5≤x≤85,15<z≤95, surplus be y and greater than 0 and
The sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is heat-treated, so that make the R in the powder 1And M 1In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside.
6. method according to claim 5, wherein said deposition step comprises: grind and consist of R 1 xT 2 yM 1 zAnd the alloy that comprises at least 70 volume % intermetallic compound phases, wherein R 1, T 2, M 1, x, y and z definition as above, grind to form the average particle size particle size powder of 500 μ m at the most, described powder is dispersed in organic solvent or the water, the slurry that obtains is applied in the surface of sintered body, and dry.
7. method according to claim 5, wherein said heat treatment step are included in 200 ℃ and heat-treat to the temperature of (Ts-10) ℃ and continue 1 minute to 30 hours, and wherein Ts represents the sintering temperature of sintered body.
8. method according to claim 5, the shape of wherein said sintered body comprise having the least part that size is equal to or less than 20mm.
9. rare-earth permanent magnet, it is to adopt following method preparation: consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of R 1 i-M 1 jAnd the intermetallic compound phase that comprises at least 70 volume %, wherein R 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, " i " and " j " expression atomic percentage and scope are: 15<j≤99, the i of surplus, the sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is then heat-treated, wherein
R in the powder 1And M 1In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside, thereby the coercive force of described magnet brought up to the magnetic that is higher than former sintered body.
10. rare-earth permanent magnet, it is to adopt following method preparation: consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of R 1 xT 2 yM 1 zAnd the intermetallic compound phase that comprises at least 70 volume %, wherein R 1Be at least a element that is selected from the rare earth element that comprises Y and Sc, T 2Be at least a element that is selected among Fe and the Co, M 1It is at least a element that is selected among Al, Si, C, P, Ti, V, Cr, Mn, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, x, y and z represent that atomic percentage and scope are: 5≤x≤85,15<z≤95, surplus is y and greater than 0, the sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is then heat-treated, wherein
R in the powder 1And M 1In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside, thereby the coercive force of described magnet brought up to the magnetic that is higher than former sintered body.
11. a method for preparing rare-earth permanent magnet may further comprise the steps:
Consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of M 1 d-M 2 eAnd the intermetallic compound phase that comprises at least 70 volume %, wherein M 1And M 2Each is selected from least a element among Al, Si, C, P, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, M naturally 1With M 2Difference, " d " and " e " expression atomic percentage and scope are: 0.1≤e≤99.9, the d of surplus and
The sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is heat-treated, so that make the M in the powder 1And M 2In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside.
12. method according to claim 11, wherein said deposition step comprises: grind and consist of M 1 d-M 2 eAnd the alloy that comprises at least 70 volume % intermetallic compound phases, wherein M 1, M 2, d and e definition as above, grind to form the average particle size particle size powder of 500 μ m at the most, in organic solvent or water, disperse described powder, the slurry that obtains is applied in the surface of sintered body, and dry.
13. method according to claim 11, wherein said heat treatment step are included in 200 ℃ and heat-treat to the temperature of (Ts-10) ℃ and continue 1 minute to 30 hours, wherein Ts represents the sintering temperature of sintered body.
14. comprising, method according to claim 11, the shape of wherein said sintered body have the least part that size is equal to or less than 20mm.
15. a rare-earth permanent magnet, it is to adopt following method preparation: consisting of R a-T 1 b-B cThe sintered body surface on arrange alloy powder, wherein R is at least a element that is selected from the rare earth element that comprises Y and Sc, T 1Be at least a element that is selected among Fe and the Co, B is a boron, and " a ", " b " and " c " expression atomic percentage and scope are: 12≤a≤20,4.0≤c≤7.0, the b of surplus, described alloy powder consist of M 1 d-M 2 eAnd the intermetallic compound phase that comprises at least 70 volume %, wherein M 1And M 2Each is selected from least a element among Al, Si, C, P, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Ga, Ge, Zr, Nb, Mo, Ag, In, Sn, Sb, Hf, Ta, W, Pb and the Bi, M naturally 1With M 2Different, " d " and " e " represent that atomic percentage and scope are: 0.1≤e≤99.9, the d of surplus, the sintered body that is furnished with described powder in vacuum or inert gas on being equal to or less than under the temperature of sintered body sintering temperature the surface is then heat-treated, wherein
M in the powder 1And M 2In at least a Elements Diffusion near the crystal boundary and/or the intragranular crystal boundary of sintered body primary phase of sintered body inside, thereby the coercive force of described magnet brought up to the magnetic that is higher than former sintered body.
CN2008101799497A 2007-03-16 2008-03-14 Rare earth permanent magnet and method of manufacturing the same Active CN101521068B (en)

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP2007068803 2007-03-16
JP2007068823 2007-03-16
JP2007068823A JP4482769B2 (en) 2007-03-16 2007-03-16 Rare earth permanent magnet and manufacturing method thereof
JP2007068803 2007-03-16
JP2007-068803 2007-03-16
JP2007-068823 2007-03-16

Publications (2)

Publication Number Publication Date
CN101521068A true CN101521068A (en) 2009-09-02
CN101521068B CN101521068B (en) 2012-07-25

Family

ID=39985407

Family Applications (1)

Application Number Title Priority Date Filing Date
CN2008101799497A Active CN101521068B (en) 2007-03-16 2008-03-14 Rare earth permanent magnet and method of manufacturing the same

Country Status (2)

Country Link
JP (1) JP5093485B2 (en)
CN (1) CN101521068B (en)

Cited By (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2012013086A1 (en) * 2010-07-30 2012-02-02 沈阳中北通磁科技股份有限公司 High performance sintered ndfeb magnet and manufacturing method of the same
CN101707107B (en) * 2009-11-23 2012-05-23 烟台首钢磁性材料股份有限公司 Manufacturing method of high-residual magnetism high-coercive force rare earth permanent magnetic material
CN102640238A (en) * 2009-12-09 2012-08-15 爱知制钢株式会社 Rare earth anisotropic magnet and process for production thereof
CN102768898A (en) * 2011-05-02 2012-11-07 信越化学工业株式会社 Rare earth permanent magnets and their preparation
CN103098155A (en) * 2010-09-15 2013-05-08 丰田自动车株式会社 Method for producing rare-earth magnet
CN103227019A (en) * 2012-01-26 2013-07-31 丰田自动车株式会社 Method for manufacturing rare-earth magnet
CN103918041A (en) * 2011-11-14 2014-07-09 丰田自动车株式会社 Rare-earth magnet and process for producing same
CN104112581A (en) * 2013-04-22 2014-10-22 昭和电工株式会社 R-t-b Rare Earth Sintered Magnet And Method Of Manufacturing The Same
CN104737244A (en) * 2012-10-23 2015-06-24 丰田自动车株式会社 Rare-earth sintered magnet and method for manufacturing same
CN104835641A (en) * 2014-02-12 2015-08-12 丰田自动车株式会社 Method for producing rare-earth magnet
CN105074852A (en) * 2013-03-18 2015-11-18 因太金属株式会社 RFeB-based magnet production method and RFeB-based sintered magnets
CN105321702A (en) * 2015-11-19 2016-02-10 北京科技大学 Method for improving coercivity of sintered NdFeB magnet
CN105312575A (en) * 2014-07-25 2016-02-10 丰田自动车株式会社 Method of manufacturing rare earth magnet
CN105830178A (en) * 2013-12-19 2016-08-03 丰田自动车株式会社 Method of manufacturing rare earth magnet
CN105529123B (en) * 2014-12-17 2017-06-06 比亚迪股份有限公司 Grain boundary decision material and rare earth permanent-magnetic material and preparation method thereof
CN106887321A (en) * 2015-12-16 2017-06-23 北京中科三环高技术股份有限公司 One kind improves the coercitive method of rare-earth magnet
US9859055B2 (en) 2012-10-18 2018-01-02 Toyota Jidosha Kabushiki Kaisha Manufacturing method for rare-earth magnet
CN109275334A (en) * 2016-01-25 2019-01-25 Ut巴特勒有限公司 Neodymium-iron-boron magnet and its manufacturing method with optional surface modification
CN109300640A (en) * 2013-06-05 2019-02-01 丰田自动车株式会社 Rare-earth magnet and its manufacturing method
CN109509630A (en) * 2019-01-15 2019-03-22 内蒙古众恒磁谷新材料有限公司 Sintered NdFeB permanent magnet manufacture craft for magnetic field pulse hoist
CN109564819A (en) * 2016-09-29 2019-04-02 日立金属株式会社 The manufacturing method of R-T-B based sintered magnet
CN109671547A (en) * 2017-10-13 2019-04-23 日立金属株式会社 R-T-B based sintered magnet and its manufacturing method
CN110289161A (en) * 2019-07-16 2019-09-27 宁德市星宇科技有限公司 A kind of preparation method of the neodymium iron boron magnetic body of low content of rare earth
CN110931197A (en) * 2019-11-22 2020-03-27 宁波同创强磁材料有限公司 Diffusion source for high-abundance rare earth permanent magnet

Families Citing this family (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5057111B2 (en) 2009-07-01 2012-10-24 信越化学工業株式会社 Rare earth magnet manufacturing method
JP5880448B2 (en) 2011-01-19 2016-03-09 日立金属株式会社 Method for producing RTB-based sintered magnet
JP2012174920A (en) * 2011-02-22 2012-09-10 Toyota Motor Corp Neodymium magnet and production method therefor
JP5742776B2 (en) * 2011-05-02 2015-07-01 信越化学工業株式会社 Rare earth permanent magnet and manufacturing method thereof
JP5754232B2 (en) * 2011-05-02 2015-07-29 トヨタ自動車株式会社 Manufacturing method of high coercive force NdFeB magnet
JP5874951B2 (en) * 2011-05-02 2016-03-02 日立金属株式会社 Method for producing RTB-based sintered magnet
MY168281A (en) 2012-04-11 2018-10-19 Shinetsu Chemical Co Rare earth sintered magnet and making method
JP6003452B2 (en) * 2012-09-20 2016-10-05 トヨタ自動車株式会社 Rare earth magnet manufacturing method
JP6221246B2 (en) * 2012-10-31 2017-11-01 日立金属株式会社 R-T-B system sintered magnet and manufacturing method thereof
JP6221233B2 (en) * 2012-12-28 2017-11-01 日立金属株式会社 R-T-B system sintered magnet and manufacturing method thereof
JP6051892B2 (en) * 2013-01-31 2016-12-27 日立金属株式会社 Method for producing RTB-based sintered magnet
JP6051922B2 (en) * 2013-02-20 2016-12-27 日立金属株式会社 Method for producing RTB-based sintered magnet
CN103646772B (en) * 2013-11-21 2017-01-04 烟台正海磁性材料股份有限公司 A kind of preparation method of R-Fe-B based sintered magnet
KR101719871B1 (en) * 2014-07-14 2017-03-24 한양대학교 산학협력단 HREE free sintered R-Fe-B magnets and manufacturing method thereof
CN105185498B (en) * 2015-08-28 2017-09-01 包头天和磁材技术有限责任公司 Rare earth permanent-magnet material and its preparation method
JP2017098456A (en) * 2015-11-26 2017-06-01 国立大学法人大阪大学 Method for manufacturing grain boundary diffusion treatment agent, and method for manufacturing rare earth-iron-boron based magnet
CN109478459B (en) 2016-08-08 2021-03-05 日立金属株式会社 Method for producing R-T-B sintered magnet
JP6610957B2 (en) * 2016-08-17 2019-11-27 日立金属株式会社 Method for producing RTB-based sintered magnet
CN107699739A (en) * 2017-10-16 2018-02-16 中国核动力研究设计院 A kind of zircaloy of resistance to nodular corrosion and preparation method thereof
JP7228096B2 (en) * 2019-03-22 2023-02-24 株式会社プロテリアル Method for producing RTB based sintered magnet
JP2021034583A (en) * 2019-08-26 2021-03-01 日本電産株式会社 Neodymium magnet, and manufacturing method thereof
JP7476601B2 (en) 2019-09-24 2024-05-01 株式会社プロテリアル Manufacturing method of RTB based sintered magnet
JP7380369B2 (en) 2020-03-24 2023-11-15 株式会社プロテリアル Manufacturing method of RTB sintered magnet and alloy for diffusion

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0742553B2 (en) * 1986-02-18 1995-05-10 住友特殊金属株式会社 Permanent magnet material and manufacturing method thereof
JP3143156B2 (en) * 1991-07-12 2001-03-07 信越化学工業株式会社 Manufacturing method of rare earth permanent magnet
JP2001196215A (en) * 2000-01-07 2001-07-19 Tokin Corp Rare earth permanent magnet having good corrosion resistance and method of manufacturing the same
TWI302712B (en) * 2004-12-16 2008-11-01 Japan Science & Tech Agency Nd-fe-b base magnet including modified grain boundaries and method for manufacturing the same
JP4702546B2 (en) * 2005-03-23 2011-06-15 信越化学工業株式会社 Rare earth permanent magnet
EP1879201B1 (en) * 2005-04-15 2016-11-30 Hitachi Metals, Ltd. Rare earth sintered magnet and process for producing the same

Cited By (46)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101707107B (en) * 2009-11-23 2012-05-23 烟台首钢磁性材料股份有限公司 Manufacturing method of high-residual magnetism high-coercive force rare earth permanent magnetic material
CN102640238A (en) * 2009-12-09 2012-08-15 爱知制钢株式会社 Rare earth anisotropic magnet and process for production thereof
WO2012013086A1 (en) * 2010-07-30 2012-02-02 沈阳中北通磁科技股份有限公司 High performance sintered ndfeb magnet and manufacturing method of the same
CN102347126A (en) * 2010-07-30 2012-02-08 沈阳中北通磁科技股份有限公司 High-performance sintered neodymium-iron-boron (Nd-Fe-B) rare-earth permanent magnet material and manufacturing method thereof
CN102347126B (en) * 2010-07-30 2014-07-23 沈阳中北通磁科技股份有限公司 High-performance sintered neodymium-iron-boron (Nd-Fe-B) rare-earth permanent magnet material and manufacturing method thereof
CN103098155A (en) * 2010-09-15 2013-05-08 丰田自动车株式会社 Method for producing rare-earth magnet
CN103098155B (en) * 2010-09-15 2016-01-06 丰田自动车株式会社 The manufacture method of rare earth element magnet
CN102768898A (en) * 2011-05-02 2012-11-07 信越化学工业株式会社 Rare earth permanent magnets and their preparation
CN102768898B (en) * 2011-05-02 2016-08-03 信越化学工业株式会社 Rare-earth permanent magnet and preparation method thereof
CN103918041A (en) * 2011-11-14 2014-07-09 丰田自动车株式会社 Rare-earth magnet and process for producing same
US10199145B2 (en) 2011-11-14 2019-02-05 Toyota Jidosha Kabushiki Kaisha Rare-earth magnet and method for producing the same
CN103918041B (en) * 2011-11-14 2017-02-22 丰田自动车株式会社 Rare-earth magnet and process for producing same
CN103227019B (en) * 2012-01-26 2015-12-09 丰田自动车株式会社 The manufacture method of rare earth element magnet
US9257227B2 (en) 2012-01-26 2016-02-09 Toyota Jidosha Kabushiki Kaisha Method for manufacturing rare-earth magnet
CN103227019A (en) * 2012-01-26 2013-07-31 丰田自动车株式会社 Method for manufacturing rare-earth magnet
US9859055B2 (en) 2012-10-18 2018-01-02 Toyota Jidosha Kabushiki Kaisha Manufacturing method for rare-earth magnet
CN104737244A (en) * 2012-10-23 2015-06-24 丰田自动车株式会社 Rare-earth sintered magnet and method for manufacturing same
CN105074852A (en) * 2013-03-18 2015-11-18 因太金属株式会社 RFeB-based magnet production method and RFeB-based sintered magnets
CN105074852B (en) * 2013-03-18 2017-09-22 因太金属株式会社 RFeB systems method of manufacturing sintered magnet and RFeB systems sintered magnet
US20160273091A1 (en) 2013-03-18 2016-09-22 Intermetallics Co., Ltd. RFeB SYSTEM SINTERED MAGNET PRODUCTION METHOD AND RFeB SYSTEM SINTERED MAGNET
CN104112581A (en) * 2013-04-22 2014-10-22 昭和电工株式会社 R-t-b Rare Earth Sintered Magnet And Method Of Manufacturing The Same
US10020097B2 (en) 2013-04-22 2018-07-10 Showa Denko K.K. R-T-B rare earth sintered magnet and method of manufacturing the same
US10468165B2 (en) 2013-06-05 2019-11-05 Toyota Jidosha Kabushiki Kaisha Rare-earth magnet and method for manufacturing same
CN109300640A (en) * 2013-06-05 2019-02-01 丰田自动车株式会社 Rare-earth magnet and its manufacturing method
US10748684B2 (en) 2013-06-05 2020-08-18 Toyota Jidosha Kabushiki Kaisha Rare-earth magnet and method for manufacturing same
CN109300640B (en) * 2013-06-05 2021-03-09 丰田自动车株式会社 Rare earth magnet and method for producing same
CN105830178A (en) * 2013-12-19 2016-08-03 丰田自动车株式会社 Method of manufacturing rare earth magnet
CN105830178B (en) * 2013-12-19 2018-07-06 丰田自动车株式会社 The method for manufacturing rare-earth magnet
CN104835641A (en) * 2014-02-12 2015-08-12 丰田自动车株式会社 Method for producing rare-earth magnet
US10056177B2 (en) 2014-02-12 2018-08-21 Toyota Jidosha Kabushiki Kaisha Method for producing rare-earth magnet
CN104835641B (en) * 2014-02-12 2017-04-26 丰田自动车株式会社 Method for producing rare-earth magnet
CN105312575B (en) * 2014-07-25 2019-03-08 丰田自动车株式会社 The method for preparing rare earth magnetite
CN105312575A (en) * 2014-07-25 2016-02-10 丰田自动车株式会社 Method of manufacturing rare earth magnet
CN105529123B (en) * 2014-12-17 2017-06-06 比亚迪股份有限公司 Grain boundary decision material and rare earth permanent-magnetic material and preparation method thereof
CN105321702A (en) * 2015-11-19 2016-02-10 北京科技大学 Method for improving coercivity of sintered NdFeB magnet
CN105321702B (en) * 2015-11-19 2017-10-20 北京科技大学 One kind improves the coercitive method of sintered NdFeB magnet
CN106887321B (en) * 2015-12-16 2019-11-19 北京中科三环高技术股份有限公司 A kind of coercitive method of raising rare-earth magnet
CN106887321A (en) * 2015-12-16 2017-06-23 北京中科三环高技术股份有限公司 One kind improves the coercitive method of rare-earth magnet
CN109275334A (en) * 2016-01-25 2019-01-25 Ut巴特勒有限公司 Neodymium-iron-boron magnet and its manufacturing method with optional surface modification
CN109564819A (en) * 2016-09-29 2019-04-02 日立金属株式会社 The manufacturing method of R-T-B based sintered magnet
CN109671547A (en) * 2017-10-13 2019-04-23 日立金属株式会社 R-T-B based sintered magnet and its manufacturing method
CN109671547B (en) * 2017-10-13 2021-06-29 日立金属株式会社 R-T-B sintered magnet and method for producing same
CN109509630A (en) * 2019-01-15 2019-03-22 内蒙古众恒磁谷新材料有限公司 Sintered NdFeB permanent magnet manufacture craft for magnetic field pulse hoist
CN110289161A (en) * 2019-07-16 2019-09-27 宁德市星宇科技有限公司 A kind of preparation method of the neodymium iron boron magnetic body of low content of rare earth
CN110289161B (en) * 2019-07-16 2021-03-30 宁德市星宇科技有限公司 Preparation method of neodymium iron boron magnet with low rare earth content
CN110931197A (en) * 2019-11-22 2020-03-27 宁波同创强磁材料有限公司 Diffusion source for high-abundance rare earth permanent magnet

Also Published As

Publication number Publication date
CN101521068B (en) 2012-07-25
JP5093485B2 (en) 2012-12-12
JP2008263179A (en) 2008-10-30

Similar Documents

Publication Publication Date Title
CN101521068B (en) Rare earth permanent magnet and method of manufacturing the same
US11482377B2 (en) Rare earth permanent magnets and their preparation
EP1970924B1 (en) Rare earth permanent magnets and their preparation
KR101123176B1 (en) Method for producing rare earth permanent magnet material
JP5304907B2 (en) R-Fe-B fine crystal high density magnet
JP5742776B2 (en) Rare earth permanent magnet and manufacturing method thereof
JP4482769B2 (en) Rare earth permanent magnet and manufacturing method thereof
KR20110002441A (en) Rare earth magnet and its preparation
JP2018093202A (en) R-t-b based permanent magnet
CN112119475B (en) Method for producing rare earth sintered permanent magnet
EP4002403A1 (en) Method for manufacturing rare earth sintered magnet
CN110534277A (en) A kind of alloy and its preparation method and application for rare-earth permanent magnet

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
C14 Grant of patent or utility model
GR01 Patent grant