EP0258609A2 - Dauermagnet mit guter thermischer Stabilität - Google Patents

Dauermagnet mit guter thermischer Stabilität Download PDF

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Publication number
EP0258609A2
EP0258609A2 EP87110634A EP87110634A EP0258609A2 EP 0258609 A2 EP0258609 A2 EP 0258609A2 EP 87110634 A EP87110634 A EP 87110634A EP 87110634 A EP87110634 A EP 87110634A EP 0258609 A2 EP0258609 A2 EP 0258609A2
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Prior art keywords
thermal stability
magnets
permanent magnet
resulting
coercive force
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EP87110634A
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English (en)
French (fr)
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EP0258609B1 (de
EP0258609A3 (en
Inventor
Masaaki Tokunaga
Minoru Endoh
Hiroshi Kogure
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Proterial Ltd
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Hitachi Metals Ltd
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Priority to EP90121313A priority Critical patent/EP0421488B1/de
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Publication of EP0258609A3 publication Critical patent/EP0258609A3/en
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Publication of EP0258609B1 publication Critical patent/EP0258609B1/de
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
    • H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
    • H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
    • H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered

Definitions

  • the present invention relates to rare earth permanent magnet materials, particularly to R-Fe-B permanent magnet materials having good thermal stability.
  • R-Fe-B permanent magnet materials have been developed as new compositions having higher magnetic properties than R-Co permanent magnet materials (Japanese Patent Laid-Open Nos. 59-46008, 59-64733 and 59-89401, and M. Sagawa et al, "New Material for Permanent Magnets on a Basis of Nd and Fe," J. Appl. Phys. 55 (6) 2083(1984)).
  • an alloy of Nd 15 Fe 77 B 8 [Nd(Fe 0.91 B 0.09)5.67] , for instance, has such magnetic properties as (BH)max of nearly 35MGOe and iHc of nearly l0KOe.
  • the R-Fe-B magnets have low Curie temperatures, so that they are poor in thermal stability.
  • attempts were made to elevate Curie temperature by adding Co (Japanese Patent Laid-Open No. 59-64733).
  • the R-Fe-B permanent magent has Curie temperature of about 300°C and at highest 370°C (Japanese Patent Laid-Open No. 59-46008), while the substitution of Co for part of Fe in the R-Fe-B magnet serves to increase the Curie temperature to 400-800°C (Japanese Patent Laid-Open No. 59-64733).
  • the addition of Co decreases the coercive force iHc of the R-Fe-B magnet.
  • An object of the present invention is, therefore, to provide an R-Fe-B permanent magnet with raised Curie temperature and sufficient coercive force and thus improved thermal stability.
  • the permanent magnet having good thermal stability according to the present invention consists essentially of a composition represented by the general formula: wherein R is Nd alone or one or more rare earth elements mainly composed of Nd, Pr or Ce, 0 ⁇ x ⁇ 0.7, 0.02 ⁇ y ⁇ 0.3, 0.001 ⁇ z ⁇ 0.15, and 4.0 ⁇ A ⁇ 7.5.
  • the amount of Co represented by "x" is 0-0.7. When it exceeds 0.7, the residual magnetic flux density Br of the resulting magnet becomes too low.
  • the lower limit of Co is preferably 0.01, and to have a well-balanced combination of such magnetic properties as iHc and Br and Tc.
  • the upper limit of Co is preferably 0.4.
  • the most preferred amount of Co is 0.05-0.25.
  • the addition of Ga leads to remarkable improvement of coercive force. This improvement appears to be provided by increasing the Curie temperature of a BCC phase in the magnet.
  • the BCC phase is a polycrystalline phase having a body-centered cubic crystal structure surrounding in a width of 100-5000A a main phase of the Nd-Fe-B magnet (Nd 2 Fei 4 B) This BCC phase .is in turn surrounded by a Nd-rich phase (Nd: 70-95 at. % and balance Fe).
  • the Curie temperature of this BCC phase corresponds to a temperature at which the coercive force of the magnet becomes lower than 50 Oe, greatly affecting the temperature characteristics of the magnet.
  • the addition of Ga serves to raise the Curie temperature of the BCC phase, effective for improving the temperature characteristics.
  • the amount of Ga represented by “z” is 0.001-0.15. When it is less than 0.001, substantially no effect is obtained on improving the Curie temperature of the magnet. On the other hand, when “z” exceeds 0.15, extreme decrease in saturation magnetization and Curie temperature ensues, providing undesirable permanent magnet materials.
  • the preferred amount of Ga is 0.002-0.10, and the most preferred amount of Ga is 0.005-0.05.
  • the amount of boron represented by "y" is less than 0.02, Curie temperature is low and high coercive force cannot be obtained.
  • the amount of B "y” is higher than 0.3. the saturation magnetization are decreased, forming phases undesirable to magnetic properties. Accordingly, the amount of B should be 0.02-0.3.
  • the preferred range of "y” is 0.03-0.20.
  • the most preferred amount of B is 0.04-0.15.
  • the permanent magnet of the present invention may further contain an additional element generally represented by "M" in the following formula: wherein R is Nd alone or one or more rare earth elements mainly composed of Nd, Pr or Ce, part of which may be substituted by Dy, Tb or Ho, M is one or more elements selected from Nb, W, V, Ta and Mo, 0 ⁇ x ⁇ 0.7, 0.02 ⁇ y ⁇ 0.3, 0.001 ⁇ z ⁇ 0.15, 0.001 ⁇ u ⁇ 0.1, and 4.0 ⁇ A ⁇ 7.5.
  • R is Nd alone or one or more rare earth elements mainly composed of Nd, Pr or Ce, part of which may be substituted by Dy, Tb or Ho
  • M is one or more elements selected from Nb, W, V, Ta and Mo, 0 ⁇ x ⁇ 0.7, 0.02 ⁇ y ⁇ 0.3, 0.001 ⁇ z ⁇ 0.15, 0.001 ⁇ u ⁇ 0.1, and 4.0 ⁇ A ⁇ 7.5.
  • Nb, W, V, Ta or Mo is added to prevent the grain growth.
  • the amount of these elements represented by "u" is 0.001-0.1. When it is less than 0.001, sufficient effects cannot be obtained, and when it exceeds 0.1, the saturation magnetization is extremely decreased, providing undesirable permanent magnets.
  • Nb does not decrease Br as much as the addition of Ga does, while it slightly increases iHc.
  • Nb is effective for increasing corrosion resistance, and so in the case of highly heat-resistant alloys likely to be exposed to relatively high temperatures, it is a highly effective additive.
  • u the amount of Nb represented by "u"
  • u the amount of Nb represented by "u"
  • u the amount of Nb represented by "u"
  • u the amount of Nb represented by "u"
  • u When the amount of Nb represented by "u" is less than 0.001, sufficient effects of increasing iHc cannot be achieved, neither does the magnet alloy have sufficiently high corrosion resistance.
  • the amount of Nb exceeds 0.1, undesirably large decrease in Br and Curie temperature ensues.
  • the preferred range of Nb is 0.002 ⁇ z ⁇ 0.04.
  • tungsten serves to extremely improve the temperature characteristics.
  • W tungsten
  • the preferred amount of W is 0.002-0.04.
  • the rare earth element "R” it may be Nd alone, or a combination of Nd and a light rare earth element such as Pr or Ce, or Pr plus Ce.
  • a light rare earth element such as Pr or Ce, or Pr plus Ce.
  • Pr and/or Ce are contained, the proportion of Pr to Nd may be 0:1 - 1:0, and that of Ce to Nd may be 0:1 - 0.3:0.7.
  • Nd may also be substituted by Dy which acts to somewhat raise Curie temperature and enhance coercive force iHc.
  • Dy acts to somewhat raise Curie temperature and enhance coercive force iHc.
  • the addition of Dy is effective to improve the thermal stability of the permanent magnet of the present invention.
  • an excess amount of Dy leads to the decrease in residual magnetic flux density Br.
  • the proportion of Dy to Nd should be 0.03:0.97-0.4:0.6 by atomic ratio.
  • the preferred atomic ratio of Dy is 0.05-0.25 .
  • the permanent magnet of the present invention can be produced by a powder metallurgy method, a rapid quenching method or a resin bonding method. These methods will be explained below.
  • a magnet alloy is obtained by arc melting or high-frequency melting.
  • the purity of starting materials may be 90% or more for R, 95% or more for Fe, 95% or more for Co, 90% or more for B, 95% or more for Ga and 95% or more for M(Nb, W, V, Ta, Mo), if any.
  • a starting material for B may be ferroboron and a starting material for Ga may be ferrogallium.
  • a starting material for M(Nb, W, V, Ta, Mo) may be ferroniobium, ferrotungsten, ferrovanadium, ferrotantalum or ferromolybdenum. Since the ferroboron and the ferrogallium contain inevitable impurities such as At and Si, high coercive force can be obtained by synergistic effect of such elements as Ga, At and Si.
  • Pulverization may be composed of the steps of pulverization and milling.
  • the pulverization may be carried out by a stamp mill, a jaw crusher, a brown mill, a disc mill, etc., and the milling may be carried out by a jet mill, a vibration mill, a ball mill, etc.
  • the pulverization is preferably carried out in a non- oxidizing atmosphere to prevent the oxidation of the alloy.
  • the final particle size is desirably 2-5 L Lm (FSSS).
  • the resulting fine powders are pressed in a magnetic field by a die. This is indispensable for providing the alloy with anisotropy that the magnet powders to be pressed have C axes aligned in the same direction.
  • Sintering is carried out in an inert gas such as Ar, He, etc., or in vacuum, or in hydrogen at 1050°C-1I50°C.
  • Heat treatment is carried out on the sintered magnet alloy at 400°C-1000°C.
  • a magnet alloy is prepared in the same manner as in the powder metallurgy method (I).
  • a melt of the resulting alloy is rapidly quenched by a single-roll or double-roll quenching apparatus. That is, the alloy melted, for instance, by high frequency is ejected through a nozzle onto a roll rotating at a high speed, thereby rapidly quenching it.
  • the resulting flaky products are heat-treated at 500-800°C. Materials provided by this rapid quenching method may be used for three kinds of permanent magnets.
  • the starting material may be an R-Fe-Co-B-Ga alloy obtained in the above (I), sintered bodies obtained by pulverization and sintering of the above alloy, rapidly quenched flakes obtained in the above (2), or bulky products obtained by hot-pressing or upsetting the flakes. These bulky products are pulverized to 30-500 ⁇ m in particle size by a jaw crusher, a brown mill, a disc mill, etc. The resulting fine powders are mixed with resins and formed by die molding or injection molding. The application of a magnetic field during the molding operation provides anisotropic magnets in which their C axes are aligned in the same direction.
  • starting materials used were 99.9%-pure Nd, 99.9%-pure Fe, 99.9%-pure Co, 99.5%- pure B, 99.9999%-pure Ga, 99.9%-pure Nb and 99.9%-pure W, and all other elements used were as pure as 99.9% or more.
  • An alloy having the composition of (Nd 0.8 Dy 0.2 )(Fe 0.835 Co 0.06 B 0.08 Nb 0.015 Ga 0.01 ) 5 . 5 was formed into an ingot by high-frequency melting.
  • the resulting alloy ingot was coarsely pulverized by a stamp mill and a disc mill, and then finely pulverized in a nitrogen gas as a pulverization medium to provide fine powders of 3.5- ⁇ m particle size (FSSS).
  • the fine powders were pressed in a magnetic field of 15KOe perpendicular to the compressing direction.
  • the compression pressure was 2 tons/cm 2 .
  • the resulting green bodies were sintered at II00°C for 2 hours in vacuo, and then cooled to room temperature in a furnace. A number of the resulting sintered alloys were heated at 900°C for 2 hours and then slowly cooled at 1.5°C/min. to room temperature.
  • an alloy of Nd 0.8 Dy 0.2 )(Fe 0.86 Co 0.06 B 0.08 ) 5.5 was prepared in the same manner as above.
  • the annealing temperature was 600°C.
  • the magnetic properties of the resulting magnet were as follows: Br of nearly 11200G, bHc of nearly 10700 Oe, iHc of nearly 24000 Oe and (BH)max of nearly 29.8 MGOe.
  • the irreversible loss of flux by heating is also shown in Tables 12(a)-(c).
  • the increase in the Co content leads to the decrease in iHc without substantially changing (BH)max.
  • the irreversible loss of flux becomes larger with the increase in the Co content.
  • the amount of Co is 0.06, the highest heat resistance can be provided.
  • the comparison of these three types of alloys shows that those containing both Ga and Nb have the highest heat resistance.
  • Alloys represented by the compositions of Nd(Feo.ss Co 0.06 B 0.08 ) 5.6 , Nd(Fe 0.84 Co 0.06 B 0.02 ) 5.6 , and Nd-(Fe 0.0825 CO 0.06 B 0.08 Ga 0.02 W 0.015 ) 5.6 were prepared by arc melting.
  • the resulting ingots were coarsely pulverized by a stamp mill and a disc mill, and after sieving to finer than 32 mesh milling was carried out by a jet mill.
  • a pulverization medium was an N 2 gas, and fine powders of 3.5 ⁇ m in particle size (FSSS) were obtained.
  • the resulting powders were formed in a magnetic field of 15KOe whose direction was perpendicular to the pressing direction. Press pressure was 2t/cm 2.
  • the resulting green bodies were sintered in vacuum at 1080°C for two hours. Heat treatment was carried out at 500-900°C for one hour, followed by quenching. The results are shown in Table 19.
  • the resulting ingots were coarsely pulverized by a stamp mill and a disc mill, and after sieving to finer than 32 mesh milling was carried out by a jet mill.
  • a pulverization medium was an N 2 gas, and fine powders of 3.5 ⁇ m in particle size (FSSS) were obtained.
  • the resulting powders were formed in a magnetic field of 15KOe whose direction was perpendicular to the pressing direction. Press pressure was 1.5t/cm 2 .
  • the resulting green bodies were sintered in vacuum at 1040°C for two hours. Heat treatment was carried out at 600-700°C for one hour, followed by quenching. The results are shown in Fig. 6.
  • the magnets containing Ga had higher coercive force and smaller decrease in 4 7 rlr and (BH)max than those containing Dy or At.
  • the variation of magnetic flux with temperature has two inflection points: one on the side of lower temperature corresponding to the Curie temperature of the BCC phase, and the other on the side of higher temperature corresponding to the Curie temperature of the main phase.
  • the magnets with Ga have lower Curie temperatures in their main phases than those containing no additive.
  • the former is higher than the latter.
  • the addition of At greatly decreases the Curie temperatures of the main phase and of the BCC phase, providing undesirable thermal stability.
  • the addition of Ga or Co and Ga together to Nd-Fe-B magnets increases Curie temperature and coercive force of the magnets, thereby providing magnets with better thermal stability.
  • M one or more of Nb. W, V, Ta, Mo

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  • Chemical & Material Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Power Engineering (AREA)
  • Hard Magnetic Materials (AREA)
EP87110634A 1986-07-23 1987-07-22 Dauermagnet mit guter thermischer Stabilität Expired - Lifetime EP0258609B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP90121313A EP0421488B1 (de) 1986-07-23 1987-07-22 Dauermagnet mit guter thermischer Stabilität

Applications Claiming Priority (8)

Application Number Priority Date Filing Date Title
JP172987/86 1986-07-23
JP17298786 1986-07-23
JP18590586 1986-08-07
JP185905/86 1986-08-07
JP24349086 1986-10-14
JP243490/86 1986-10-14
JP85787 1987-01-06
JP85787/87 1987-01-06

Related Child Applications (1)

Application Number Title Priority Date Filing Date
EP90121313.2 Division-Into 1987-07-22

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EP0258609A2 true EP0258609A2 (de) 1988-03-09
EP0258609A3 EP0258609A3 (en) 1989-04-26
EP0258609B1 EP0258609B1 (de) 1993-02-03

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EP87110634A Expired - Lifetime EP0258609B1 (de) 1986-07-23 1987-07-22 Dauermagnet mit guter thermischer Stabilität

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EP (2) EP0421488B1 (de)
JP (1) JP2751109B2 (de)
KR (1) KR910001065B1 (de)
CN (1) CN1036554C (de)
DE (2) DE3783975T2 (de)

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EP0274034A3 (en) * 1987-01-06 1989-03-08 Hitachi Metals, Ltd. Anisotropic magnetic powder, magnet thereof and method of producing same
EP0306928A3 (en) * 1987-09-09 1989-10-11 Hitachi Metals, Ltd. Magnet for motor and method of manufacturing same
DE3825358A1 (de) * 1988-07-26 1990-02-01 Siemens Ag Magnetischer werkstoff und verfahren zu seiner herstellung
DE3840414A1 (de) * 1988-11-30 1990-05-31 Siemens Ag Verfahren zur herstellung eines koerpers mit einem hartmagnetischen werkstoff
US5000800A (en) * 1988-06-03 1991-03-19 Masato Sagawa Permanent magnet and method for producing the same
WO1991014271A1 (en) * 1990-03-16 1991-09-19 The Secretary Of State For Defence In Her Britannic Majesty's Government Of The United Kingdom Of Great Britain And Northern Ireland Perromagnetic materials
US5089065A (en) * 1988-08-23 1992-02-18 Mg Company Ltd. Melt-quenched thin-film alloy for bonded magnets
US5143560A (en) * 1990-04-20 1992-09-01 Hitachi Metals, Inc., Ltd. Method for forming Fe-B-R-T alloy powder by hydrogen decrepitation of die-upset billets
US5292380A (en) * 1987-09-11 1994-03-08 Hitachi Metals, Ltd. Permanent magnet for accelerating corpuscular beam
DE4331563A1 (de) * 1992-09-18 1994-03-24 Hitachi Metals Ltd Nd-Fe-B-Sintermagnete
US5472525A (en) * 1993-01-29 1995-12-05 Hitachi Metals, Ltd. Nd-Fe-B system permanent magnet
WO2004003245A1 (ja) * 2002-06-28 2004-01-08 Aichi Steel Corporation ボンド磁石用合金、等方性磁石粉末および異方性磁石粉末とそれらの製造方法並びにボンド磁石
EP3128521A4 (de) * 2014-03-31 2017-12-27 Xiamen Tungsten Co. Ltd. W-haltiger r-fe-b-cu-sintermagnet und abschrecklegierung
CN111627633A (zh) * 2020-06-28 2020-09-04 福建省长汀金龙稀土有限公司 一种r-t-b系磁性材料及其制备方法

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US5405455A (en) * 1991-06-04 1995-04-11 Shin-Etsu Chemical Co. Ltd. Rare earth-based permanent magnet
DE69202515T2 (de) * 1991-06-04 1995-09-21 Shinetsu Chemical Co Verfahren zur Herstellung von zweiphasigen Dauermagneten auf der Basis von Seltenen Erden.
DE19541948A1 (de) * 1995-11-10 1997-05-15 Schramberg Magnetfab Magnetmaterial und Dauermagnet des NdFeB-Typs
WO2002103719A1 (fr) * 2001-06-19 2002-12-27 Mitsubishi Denki Kabushiki Kaisha Materiau magnetique durable en metal du groupe des terres rares
CN101240398B (zh) * 2007-02-07 2010-12-29 罗阳 金属间化合物各向异性磁粉，制备方法及专用设备
KR101378090B1 (ko) 2007-05-02 2014-03-27 히다찌긴조꾸가부시끼가이사 Ｒ－ｔ－ｂ계 소결 자석
CN101657863B (zh) 2007-05-02 2012-11-07 日立金属株式会社 R-t-b系烧结磁体
JP5163630B2 (ja) * 2009-12-18 2013-03-13 トヨタ自動車株式会社 希土類磁石およびその製造方法
US10497497B2 (en) 2012-02-02 2019-12-03 Santoku Corporation R-T-B—Ga-based magnet material alloy and method of producing the same
KR101649433B1 (ko) * 2012-02-23 2016-08-19 제이엑스금속주식회사 네오디뮴계 희토류 영구 자석 및 그 제조 방법
CN103887028B (zh) * 2012-12-24 2017-07-28 北京中科三环高技术股份有限公司 一种烧结钕铁硼磁体及其制造方法
CN104020032A (zh) * 2014-06-17 2014-09-03 攀钢集团攀枝花钢钒有限公司 一种对不易碎钒铁化学分析用试样的制备方法
CN110148506A (zh) * 2019-04-03 2019-08-20 宁波同创强磁材料有限公司 拓宽稀土永磁体烧结温度窗口的方法及稀土永磁体的制备方法
JP2024154865A (ja) * 2023-04-20 2024-10-31 信越化学工業株式会社 希土類焼結磁石及びその製造方法

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EP0216254B1 (de) * 1985-09-10 1991-01-02 Kabushiki Kaisha Toshiba Dauermagnet
JPS62136551A (ja) * 1985-12-10 1987-06-19 Daido Steel Co Ltd 永久磁石材料
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JP3084975B2 (ja) * 1992-11-06 2000-09-04 松下電器産業株式会社 液晶表示用セルの製造装置

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Publication number Priority date Publication date Assignee Title
EP0274034A3 (en) * 1987-01-06 1989-03-08 Hitachi Metals, Ltd. Anisotropic magnetic powder, magnet thereof and method of producing same
EP0306928A3 (en) * 1987-09-09 1989-10-11 Hitachi Metals, Ltd. Magnet for motor and method of manufacturing same
US5292380A (en) * 1987-09-11 1994-03-08 Hitachi Metals, Ltd. Permanent magnet for accelerating corpuscular beam
US5000800A (en) * 1988-06-03 1991-03-19 Masato Sagawa Permanent magnet and method for producing the same
DE3825358A1 (de) * 1988-07-26 1990-02-01 Siemens Ag Magnetischer werkstoff und verfahren zu seiner herstellung
US5089065A (en) * 1988-08-23 1992-02-18 Mg Company Ltd. Melt-quenched thin-film alloy for bonded magnets
DE3840414A1 (de) * 1988-11-30 1990-05-31 Siemens Ag Verfahren zur herstellung eines koerpers mit einem hartmagnetischen werkstoff
US5382304A (en) * 1990-03-16 1995-01-17 The Secretary Of State For Defence In Her Britannic Majesty's Government Of The United Kingdom Of Great Britain And Northern Ireland Ferromagnetic materials
WO1991014271A1 (en) * 1990-03-16 1991-09-19 The Secretary Of State For Defence In Her Britannic Majesty's Government Of The United Kingdom Of Great Britain And Northern Ireland Perromagnetic materials
US5143560A (en) * 1990-04-20 1992-09-01 Hitachi Metals, Inc., Ltd. Method for forming Fe-B-R-T alloy powder by hydrogen decrepitation of die-upset billets
DE4331563A1 (de) * 1992-09-18 1994-03-24 Hitachi Metals Ltd Nd-Fe-B-Sintermagnete
US5472525A (en) * 1993-01-29 1995-12-05 Hitachi Metals, Ltd. Nd-Fe-B system permanent magnet
CN1120506C (zh) * 1993-01-29 2003-09-03 日立金属株式会社 钕－铁－硼系永久磁铁
DE4402783B4 (de) * 1993-01-29 2008-06-05 Hitachi Metals, Ltd. Nd-Fe-B-System-Dauermagnet
WO2004003245A1 (ja) * 2002-06-28 2004-01-08 Aichi Steel Corporation ボンド磁石用合金、等方性磁石粉末および異方性磁石粉末とそれらの製造方法並びにボンド磁石
EP3128521A4 (de) * 2014-03-31 2017-12-27 Xiamen Tungsten Co. Ltd. W-haltiger r-fe-b-cu-sintermagnet und abschrecklegierung
US10381139B2 (en) 2014-03-31 2019-08-13 Xiamen Tungsten Co., Ltd. W-containing R—Fe—B—Cu sintered magnet and quenching alloy
CN111627633A (zh) * 2020-06-28 2020-09-04 福建省长汀金龙稀土有限公司 一种r-t-b系磁性材料及其制备方法

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Publication number Publication date
KR880002202A (ko) 1988-04-29
CN1036554C (zh) 1997-11-26
DE3783975D1 (de) 1993-03-18
KR910001065B1 (ko) 1991-02-23
EP0258609B1 (de) 1993-02-03
DE3783975T2 (de) 1993-05-27
JP2751109B2 (ja) 1998-05-18
JPS647503A (en) 1989-01-11
DE3750661D1 (de) 1994-11-17
DE3750661T2 (de) 1995-04-06
EP0258609A3 (en) 1989-04-26
EP0421488A2 (de) 1991-04-10
CN87105186A (zh) 1988-02-03
EP0421488A3 (en) 1991-08-28
EP0421488B1 (de) 1994-10-12

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