EP0425469A2 - (Matériau pour) Aimant permanent et procédé de fabrication - Google Patents

(Matériau pour) Aimant permanent et procédé de fabrication Download PDF

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Publication number
EP0425469A2
EP0425469A2 EP90890267A EP90890267A EP0425469A2 EP 0425469 A2 EP0425469 A2 EP 0425469A2 EP 90890267 A EP90890267 A EP 90890267A EP 90890267 A EP90890267 A EP 90890267A EP 0425469 A2 EP0425469 A2 EP 0425469A2
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EP
European Patent Office
Prior art keywords
base material
atom
alloy additives
permanent magnet
nitrides
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
EP90890267A
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German (de)
English (en)
Other versions
EP0425469A3 (en
EP0425469B1 (fr
Inventor
Oskar Dr. Pacher
Siegfried Dr. Heiss
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.)
Vacuumschmelze GmbH and Co KG
Original Assignee
Boehler GmbH
Boehler Ybbstalwerke GmbH
Boehler GmbH Germany
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
Application filed by Boehler GmbH, Boehler Ybbstalwerke GmbH, Boehler GmbH Germany filed Critical Boehler GmbH
Publication of EP0425469A2 publication Critical patent/EP0425469A2/fr
Publication of EP0425469A3 publication Critical patent/EP0425469A3/de
Application granted granted Critical
Publication of EP0425469B1 publication Critical patent/EP0425469B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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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
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
    • H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
    • H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
    • H01F41/0293—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets diffusion of rare earth elements, e.g. Tb, Dy or Ho, into permanent magnets

Definitions

  • the invention relates to a sintered SE-Fe-B permanent magnet (material).
  • the invention further relates to a method for producing SE-Fe-B permanent magnet (s) (materials), the constituents of the base (magnet) material being produced by melt metallurgy, then pulverized and pressed in a magnetic field and then sintered.
  • Permanent magnets are known from EP-PS 126 802, which contain rare earths as well as boron and possibly cobalt as materials. These elements are homogeneously distributed in the magnetic phase due to the process parameters used.
  • the manufacture of the magnets is carried out in such a way that a starting alloy made by melt metallurgy is ground, whereupon the powder is pressed in a magnetic field, followed by a sintering process and a heat treatment.
  • EP-PS 101 552 which contain rare earths as well as iron and boron and optionally further additional elements.
  • the main magnetic phase must be an intermetallic compound of constant composition, which requires a homogeneous distribution of all elements.
  • the aim of the invention is to eliminate the disadvantages of the known magnets and their manufacturing processes and to create permanent magnets which contain rare earths and which have good temperature stability. Furthermore, the scatter of the magnetic parameters should be reduced by a new and improved manufacturing process.
  • a permanent magnet material of the type mentioned in that in or at the grain boundaries and / or in the grain boundary region of the magnetic phase, preferably SE2Fe14 B, with SE at least one element from the group of rare earths, preferably Neodymium and / or dysprosium and / or praseodymium and / or holmium is, as an alloy additive, at least one further element from the group of heavy rare earths, preferably gadolinium, holmium, dysprosium and / or terbium, and / or at least one oxide and / or Nitride and / or carbide of at least one element from the group of rare earths, preferably heavy rare earths, optionally together with grain boundary alloy additives, including oxides and / or nitrides and / or borides, at least one of the elements cobalt, chromium, aluminum, titanium and / or tantalum.
  • a method of the type mentioned at the outset is characterized in that the melt metallurgically produced, powdered base material with solid powdered and / or in liquid form alloy additives, namely at least one element from the group of heavy rare earths, preferably gadolinium and / or holmium and / or dysprosium and / or terbium and / or at least one containing at least one preferably heavy rare earth metal, which is present as oxide and / or nitride and / or carbide of this metal (these metals) or oxides and / or nitrides and / or carbides thereof Metal (these metals), in particular when forming a chemical, preferably organometallic, compound, optionally together with powdered grain boundary alloy additives, consisting of oxides and / or nitrides and / or borides, at least one of the elements cobalt, chromium, aluminum, titanium or tantalum and then mixed together Magnetic field alignment with the alloy additives and optionally the grain
  • a special feature of the new permanent magnet (material) according to the invention is the specific element enrichment in the grain boundary or in the grain boundary area and a concentration gradient at the grain edge of the magnetic phase.
  • the temperature dependence of the coercive force is influenced extremely favorably and shows favorable values at room temperature and in particular also at elevated temperatures with a high remanence.
  • alloy additives ie the elements or compounds added to the base material
  • the alloy additives are selected from the group of heavy rare earths and are present in the magnet in the form of thermodynamically stable oxides, nitrides or carbides of rare earth metals, whereby concentration gradients which are advantageously formed by microdiffusion are formed below 5 ⁇ m, preferably below 0 5 / ⁇ m.
  • the grain boundary alloy additives are also said to be thermodynamically stable compounds.
  • the effect of the grain boundary enrichment according to the invention is likely to be due to partial dissolution and re-excretion processes, which surprisingly also reduce the average grain size of the magnetic phases.
  • the base material 15 atom% ( ⁇ 5 atom%) SE, 77 atom% ( ⁇ 10 atom%) Fe and 8 atom% ( ⁇ 5 atom%) B having.
  • Certain variations in the composition of the base material are therefore possible; it is also possible to use various rare earths in the base material or in the alloy additives, alone or in combination.
  • alloy additions 0.2 to 2.5% by weight, preferably 0.8 to 2% by weight, in particular 1 to 1.5% by weight. make up% of the base material. Larger amounts of alloy additives have an undesirable effect on the characteristics of the material.
  • alloy additives present in solid form are milled with dimensions of less than 5 ⁇ m, preferably less than 1 ⁇ m, in particular less than 0.5 ⁇ m, and that the melt metallurgy produced base material to particles with dimensions less than 200 microns, preferably less than 100 microns, in particular less than 50 microns, in particular by high-energy comminution.
  • the powdered alloy additives and the comminuted base material are ground together for mixing are, preferably until the particles of the base material have dimensions of less than 30 ⁇ m, preferably less than 20 ⁇ m, in particular less than 15 ⁇ m.
  • the fine alloy additives accumulate on the comminuted particles of the base material, which has a very good influence on the subsequent sintering process.
  • the base material can essentially be completely surrounded by the finer powder.
  • Another advantageous way of intimately contacting the base material with the alloy additives is that the compounds are in liquid, in particular dissolved, form and are mixed with the powdery base material, so that the surface of the individual grains is largely wetted or contacted.
  • the base material contacted with the compounds present in liquid form is dried in particular by evaporating off the solvent for the compounds and then subjected to a heat treatment to form oxides, nitrides, carbides of the rare earth metals contained in the compound.
  • the compound can already be in the form of dissolved oxides, nitrides or carbides of RE metals or these oxides, nitrides or carbides are formed by thermal decomposition of the liquid. It is advantageous if the thermal decomposition of the connections takes place between 100 ° C. to 1000 ° C., preferably between 350 ° C. to 800 ° C.
  • soluble, in particular organometallic, compounds of preferably heavy RE metals are used as chemical compounds or that soluble salts of inorganic and / or organic acids are preferably used as chemical compounds or that acetates and / or oxalates and / or carbonates and / or halides and / or acetylacetates of the RE metals are used.
  • soluble salts of inorganic and / or organic acids are preferably used as chemical compounds or that acetates and / or oxalates and / or carbonates and / or halides and / or acetylacetates of the RE metals are used.
  • the chemical compounds admixed to the base material are broken down into the oxides, nitrides or carbides in the course of a temperature treatment and / or in the course of the temperature increase during the sintering process.
  • the actual sintering is carried out in such a way that sintering takes place in a vacuum until the alloy additives are enriched at or in the grain boundaries or until concentration gradients are formed at the grain boundaries by microdiffusion in the magnetic phase, which gradients are 5 ⁇ m, preferably 1 ⁇ m; in particular 0.5 ⁇ m, not significantly exceed. It is advantageous if the sintering is not longer than 20 minutes, preferably 10 to 20 minutes, in particular about 15 minutes, or the sintering is optionally carried out only so long that no decomposition or complete diffusion of the oxides, nitrides or carbides of RE metals or any grain boundary alloy additives. Too large deposits of the alloy additives would impair the magnetic properties of the material; an undesired decomposition (e.g. oxide decomposition) of an added rare earth metal compound could e.g. cause the dissolution of this metal in the magnetic phase.
  • an undesired decomposition e.g. oxide decomposition
  • FIG. 1 a flow chart which schematically reproduces the method steps according to the invention.
  • 2 shows a deposition or concentration curve.
  • this alloy is comminuted to a powder with dimensions of advantageously less than 50 ⁇ m.
  • the selected solid alloy additives can also be pulverized or ground, advantageously on particles with dimensions of less than 5 ⁇ m. These two powders are then ground together until the particles of the base material produced by melt metallurgy preferably have dimensions of less than 10 ⁇ m or 15 ⁇ m.
  • This powder with an essentially homogeneous particle distribution which is optionally achieved after a homogenization step, is then pressed into the desired shape in the magnetic field and then sintered at temperatures of 900 ° to 1200 ° C.
  • the alloy additives can be present as compounds in the form of solutions or in liquid form and mixed with the powder of the base material, e.g. be stirred.
  • These compounds are oxides and / or nitrides and / or carbides of RE metals or can be converted into them by heat treatment. As shown in FIG. 1, this heat treatment can take place before or after the pressing, at most in the course of the sintering. It is advisable to mix excess solvents e.g. to be removed by evaporation or to heat or, if necessary, to compress the moist or wetted base material and then to undergo the sintering in dried form.
  • the solvent of the compound can be dried in vacuo or under a protective gas.
  • a first phase which contains about 90 to 95 vol. .%, with a composition of 1.8 atom% neodymium, 82.4 atom% iron and 5.8 atom% boron, which phase is the magnetic phase.
  • a phase with about 11.1 atom-u neodymium, 4414 atom% iron and 44.4 atom% boron is obtained, the ratio of 1: 4 of Rare earths to iron can vary somewhat (e.g. (1+): 4).
  • a neodymium-rich phase is obtained in an amount of up to 5% by volume, the last (s) being (are) paramagnetic.
  • the base material is pulverized or ground.
  • this homogenization or comminution has the purpose that since the magnetic first phase is not melted during the sintering process, the metallic binding of the sintered workpiece takes place by melting or melting on the further phase.
  • This further melting phase also represents the carrier for the added alloy additives and diffuses with them into the grain boundary regions of the magnetic phase or accumulates there.
  • This deposition is shown schematically in FIG. 2, in which the concentration curve of the alloy additives over the boundary curve of two grains is shown. The alloy additives deposited on the boundary between the grains are recognized, which prevent migration of the domain walls and thus increase the coercive force of the magnetic phase.
  • the additives C 1, C 2 and C 3 give even better BHmax values than the additives A 1, A 2 and A 3. Also the addition of DyBr3 or Dy2 (CH3COO) 3 dehydrated proved to be favorable.
  • An alloy with the composition Nd (33% by weight), Fe (53% by weight), Co (15% by weight) and B (1% by weight) is pre-comminuted to a grain size of ⁇ 100 ⁇ m and continue to grind together with finely ground Dy2O3 ( ⁇ 5 ⁇ m).
  • the joint grinding creates an intimate, homogeneous mixture between the two powders.
  • the homogeneous mixture of the fine powders is magnetized, aligned and pressed in a magnetic field.
  • the green body is sintered at a temperature between 1000 ° C and 1100 ° C and then heat-treated between 600 ° C and 900 ° C.
  • the remanence of the magnets at room temperature is 1.2T and is reduced to around 1.1T at 160 ° C.
  • the coercive force is reduced from L400kA / m at room temperature to 650kA / m at 100 ° C.
  • the maximum energy product varies between 280kJ / m3 and 240kJ / m3 in the temperature range between 20 ° C and 160 ° C.
  • the granular base material for a sintered magnet with the composition Nd15Fe77B8 has an initial grain size between 0.5 and 2 mm.
  • the raw material is ground to a grain size of ⁇ 10 ⁇ m over a period of 60 min.
  • One kg of the powder is then mixed with 5 g of a mixture of dysprosium oxalate and terbium oxalate (dry powder) in a ratio of 50:50 and homogenized over a period of 20 minutes.
  • the powder is then removed from the grinding device and aligned, compressed and sintered under a protective gas in a magnetic field for the production of anisotropic magnets.
  • the Dy compounds are converted into Dy2O3, which compound is present at the grain boundaries.
  • the starting powder for a magnet with the composition Nd15Fe72Co5B8 is ground to a grain size of ⁇ 10 ⁇ m. Then the powder is mixed with a solution of 50 g / l of dysprosium acetylacetonate in acetone, 1-2 g of solution per kg of powder being used, and the solvent is evaporated to a small extent in a rotary evaporator (vacuum). By introducing the Dy compound in a dissolved form, the powder particles are provided with a very thin coating. The powder is then magnetically aligned, compacted and sintered (as in Example 1).
  • the granular base material for a sintered magnet with the composition Nd13Dy2Fe72Co5B8 has an initial grain size between 0.5 and 2 mm.
  • the raw material is ground to a grain size of ⁇ 10 ⁇ m over a period of 60 min.
  • 1 kg of the powder is then mixed with 5 g of dysprosium bromide (powder) and homogenized over a period of 20 minutes.
  • the powder coated with dysprosium bromide is then the grinding device removed and aligned for the production of anisotropic magnets under protective gas in a magnetic field, pressed and sintered. When the temperature rises, the bromide escapes and Dy2O3 is formed. The actual sintering takes place in a vacuum.
  • the starting powder for a magnet of the composition Nd13Dy2Fe72Co5B8 is ground to a particle size (10 .mu.m. Then the powder is mixed with an addition of 3 g of dysprosium acetate (powder) per kg of magnetic powder. After homogenization during a The surface of the magnetic powder is coated uniformly with dysprosium acetate for a period of 15 minutes, after which the powder is magnetically aligned, compacted and sintered (analogously to example 1). The dysprosium acetate is converted into Dy2O3 by heating.
  • the starting powder for a magnet with the composition Nd15Fe77B8 is ground to a grain size of ⁇ 10 ⁇ m. Then the powder is mixed several times with a solution of dysprosium acetylacetonate in acetone and the solvent is always evaporated down to a small amount. This is carried out until 3 g of dysprosium acetylacetonate per / kg of magnetic powder have been used up.
  • the Dy compound in dissolved form and by evaporating the solvent several times, the powder particles are provided with a very thin and even coating. The powder is then magnetically aligned, compacted and sintered analogously to Example 1, the formation of Dy2O3 taking place, which remains attached to the grain boundaries.

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  • Engineering & Computer Science (AREA)
  • Power Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Hard Magnetic Materials (AREA)
  • Powder Metallurgy (AREA)
EP19900890267 1989-10-25 1990-10-05 (Matériau pour) Aimant permanent et procédé de fabrication Expired - Lifetime EP0425469B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
AT245489 1989-10-25
AT2454/89 1989-10-25
AT245489A AT393178B (de) 1989-10-25 1989-10-25 Permanentmagnet(-werkstoff) sowie verfahren zur herstellung desselben

Publications (3)

Publication Number Publication Date
EP0425469A2 true EP0425469A2 (fr) 1991-05-02
EP0425469A3 EP0425469A3 (en) 1991-11-06
EP0425469B1 EP0425469B1 (fr) 2000-04-05

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EP19900890267 Expired - Lifetime EP0425469B1 (fr) 1989-10-25 1990-10-05 (Matériau pour) Aimant permanent et procédé de fabrication

Country Status (6)

Country Link
EP (1) EP0425469B1 (fr)
AT (1) AT393178B (fr)
CZ (1) CZ284167B6 (fr)
DD (1) DD298177A5 (fr)
DE (1) DE59010911D1 (fr)
HU (1) HU215659B (fr)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0505348A1 (fr) * 1991-03-18 1992-09-23 BÖHLER YBBSTALWERKE G.m.b.H. Matériau pour aimant permanant ou aimant permanant fritté et procédé de fabrication
WO2002013209A2 (fr) * 2000-08-03 2002-02-14 Sanei Kasei Co., Limited Aimant permanent nanocomposite a energie elevee
EP2521147A1 (fr) * 2011-05-02 2012-11-07 Shin-Etsu Chemical Co., Ltd. Aimants permanents de terres rares et leur préparation
US10160037B2 (en) 2009-07-01 2018-12-25 Shin-Etsu Chemical Co., Ltd. Rare earth magnet and its preparation

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0208807A1 (fr) * 1985-06-14 1987-01-21 Union Oil Company Of California Aimants permanents terre rare, fer, bore
JPS6227548A (ja) * 1985-07-27 1987-02-05 Sumitomo Special Metals Co Ltd 永久磁石合金
JPS62171102A (ja) * 1986-01-23 1987-07-28 Shin Etsu Chem Co Ltd 希土類永久磁石とその製造方法
JPH01238001A (ja) * 1988-03-18 1989-09-22 Kawasaki Steel Corp 希土類永久磁石の製造方法
EP0389626A1 (fr) * 1988-06-03 1990-10-03 Mitsubishi Materials Corporation AIMANT FRITTE A BASE D'UN ALLIAGE DE B-Fe-ELEMENTS DE TERRES RARES ET PROCEDE DE PRODUCTION
EP0395625A2 (fr) * 1989-04-28 1990-10-31 BÖHLER YBBSTALWERKE Ges.m.b.H. Procédé de fabrication d'un aimant permanent ou un materiau pour aimant permanent

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6187825A (ja) * 1984-10-05 1986-05-06 Hitachi Metals Ltd 永久磁石材料の製造方法
AU609669B2 (en) * 1986-10-13 1991-05-02 N.V. Philips Gloeilampenfabrieken Method of manufacturing a permanent magnet
EP0284033B1 (fr) * 1987-03-23 1993-08-11 Tokin Corporation Méthode pour la fabrication d'un aimant anisotrope à liant, à base de terre rare-fer-bore, à partir de copeaux rubanés en alliage terre rare-fer-bore rapidement trempé

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0208807A1 (fr) * 1985-06-14 1987-01-21 Union Oil Company Of California Aimants permanents terre rare, fer, bore
JPS6227548A (ja) * 1985-07-27 1987-02-05 Sumitomo Special Metals Co Ltd 永久磁石合金
JPS62171102A (ja) * 1986-01-23 1987-07-28 Shin Etsu Chem Co Ltd 希土類永久磁石とその製造方法
JPH01238001A (ja) * 1988-03-18 1989-09-22 Kawasaki Steel Corp 希土類永久磁石の製造方法
EP0389626A1 (fr) * 1988-06-03 1990-10-03 Mitsubishi Materials Corporation AIMANT FRITTE A BASE D'UN ALLIAGE DE B-Fe-ELEMENTS DE TERRES RARES ET PROCEDE DE PRODUCTION
EP0395625A2 (fr) * 1989-04-28 1990-10-31 BÖHLER YBBSTALWERKE Ges.m.b.H. Procédé de fabrication d'un aimant permanent ou un materiau pour aimant permanent

Non-Patent Citations (4)

* Cited by examiner, † Cited by third party
Title
IEEE TRANSLATION JOURNAL on MAGNETICS in JAPAN vol. 3, no. 2, Februar 1988, NEW YORK US Seiten 145 - 151; K.OHASHI ET AL.: "Effects of Rare Earth Oxide Addition on Nd Fe B Magnets" *
PATENT ABSTRACTS OF JAPAN vol. 11, no. 206 (C-433)(2653) 3 Juli 1987, & JP-A-62 27548 (SUMITOMO SPECIAL METALS CO LTD) 05 Februar 1987, *
PATENT ABSTRACTS OF JAPAN vol. 12, no. 9 (E-572)(2856) 12 Januar 1988, & JP-A-62 171102 (SHIN ETSU CHEM CO LTD) 28 Juli 1987, *
PATENT ABSTRACTS OF JAPAN vol. 13, no. 568 (E-861)(3916) 15 Dezember 1989, & JP-A-1 238001 (KAWASAKI STEEL CORP.) 22 September 1989, *

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0505348A1 (fr) * 1991-03-18 1992-09-23 BÖHLER YBBSTALWERKE G.m.b.H. Matériau pour aimant permanant ou aimant permanant fritté et procédé de fabrication
WO2002013209A2 (fr) * 2000-08-03 2002-02-14 Sanei Kasei Co., Limited Aimant permanent nanocomposite a energie elevee
WO2002013209A3 (fr) * 2000-08-03 2002-08-22 Sanei Kasei Co Ltd Aimant permanent nanocomposite a energie elevee
US10160037B2 (en) 2009-07-01 2018-12-25 Shin-Etsu Chemical Co., Ltd. Rare earth magnet and its preparation
EP2521147A1 (fr) * 2011-05-02 2012-11-07 Shin-Etsu Chemical Co., Ltd. Aimants permanents de terres rares et leur préparation
US10614952B2 (en) 2011-05-02 2020-04-07 Shin-Etsu Chemical Co., Ltd. Rare earth permanent magnets and their preparation
US11482377B2 (en) 2011-05-02 2022-10-25 Shin-Etsu Chemical Co., Ltd. Rare earth permanent magnets and their preparation
US11791093B2 (en) 2011-05-02 2023-10-17 Shin-Etsu Chemical Co., Ltd. Rare earth permanent magnets and their preparation

Also Published As

Publication number Publication date
EP0425469A3 (en) 1991-11-06
CZ284167B6 (cs) 1998-09-16
HU906544D0 (en) 1991-04-29
CS514190A3 (en) 1992-05-13
EP0425469B1 (fr) 2000-04-05
DD298177A5 (de) 1992-02-06
ATA245489A (de) 1991-01-15
HU215659B (hu) 1999-02-01
DE59010911D1 (de) 2000-09-21
AT393178B (de) 1991-08-26
HUT58948A (en) 1992-03-30

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