EP0517179B1 - Verfahren zur Herstellung von zweiphasigen Dauermagneten auf der Basis von Seltenen Erden - Google Patents

Verfahren zur Herstellung von zweiphasigen Dauermagneten auf der Basis von Seltenen Erden Download PDF

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EP0517179B1
EP0517179B1 EP92109366A EP92109366A EP0517179B1 EP 0517179 B1 EP0517179 B1 EP 0517179B1 EP 92109366 A EP92109366 A EP 92109366A EP 92109366 A EP92109366 A EP 92109366A EP 0517179 B1 EP0517179 B1 EP 0517179B1
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Prior art keywords
alloy
rare earth
positive number
range
powder
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French (fr)
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EP0517179A1 (de
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Matou Kusunoki
Takehisa Monowa
Masao Yoshikawa
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Shin Etsu Chemical Co Ltd
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Shin Etsu Chemical Co Ltd
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Priority claimed from JP3159766A external-priority patent/JP2853839B2/ja
Priority claimed from JP3159765A external-priority patent/JP2853838B2/ja
Priority claimed from JP03198476A external-priority patent/JP3143156B2/ja
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0433—Nickel- or cobalt-based alloys
    • C22C1/0441—Alloys based on intermetallic compounds of the type rare earth - Co, Ni
    • 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 a method of preparing a rare earth-based permanent magnet or, more particularly, to a method of preparing a rare earth-based permanent magnet having remarkably improved magnetic properties such as the residual magnetic flux density, coercive force, maximum energy product and the like.
  • rare earth-based permament magnets are known in the prior art and widely used in practical applications by virtue of their very excellent magnetic properties as compared with other non- rare earth permanent magnets.
  • various methods of preparing the rare earth-based permanent magnets those preparing rare earth-based permanent magnets from a ternary alloy of neodymium, iron and boron are highlighted.
  • an excellent neodymium-iron-boron permanent magnet can be produced by the so-called two-alloy method in which, instead of the conventional powder-metallurgical method using a powder of the single alloy having the same composition as the magnet, two alloys having different compositions are prepared and the fine powders obtained by pulverizing the two alloys are mixed together in a specified proportion to give a powder mixture which is molded into a shape of the desired magnet in a magnetic field followed by sintering.
  • the permanent magnet prepared by this two-alloy method sometimes has much better magnetic properties than the magnets prepared by the single-alloy method even when the overall chemical compositions of the magnets are the same.
  • the above mentioned two-alloy method can be classified into three types depending on the procedure by which the alloy powders before blending are prepared.
  • the method of the first type disclosed for example, in Japanese Patent Kokai 63-93841, 63-252403, 63-278308, 1-108707, 1-146310, 1-146309 and 1-155603, either one or both of the two alloys are prepared by the so-called liquid-quenching method so that the alloy thus produced can be an amorphous or microcrystalline alloy. It is recently reported by E. Otuki, et al. in Eleventh International Workshop on Rare Earth Magnets, Pittsuburgh, Penn., October 1990, page 328 that the rare earth-based permanent magnet prepared by using this liquid-quenching method may have an extremely high maximum energy product of 50 MGOe or even larger.
  • two different alloys of a rare earth element R each having a chemical composition of the formula R 2 Fe 14 B as an intermetallic compound are prepared by modifying the kind and content of the rare earth element or elements, one being rich and the other being lean in the content of neodymium.
  • one of the alloy powders having a chemical composition of the formula R 2 Fe 14 B, in which R is mainly neodymium, is mixed with a second powder prepared from a certain element or alloy of a low melting point or carbide, boride, hydride and the like of a rare earth element followed by the powder metallurgical process for the preparation of a magnet.
  • a magnet which is produced by this third-type method is also disclosed in WO-A-9 106 107.
  • a R 2 T 14 B phase in which Tone or more of Fe, Co or Ni and which has a high residual flux densitiy, and a low-melting RT- and/or RTB phase are used as starting makrials.
  • JP-63 127 505. The two alloys selected have different sintering temperatures. Therefore in the sintering step a crystal grows. This crystal consists of one alloy being the kernel and the second forming the peripheral part. The resulting permament magnet has a large maximum energy product and causes no substantial reduction of the maximum energy product.
  • the first-type method disclosed by Otuki has a problem that the coercive force of the permanent magnet obtained thereby cannot be high enough to rarely exceed 9 kOe, which is subject to a decrease as the temperature is increased, although a considerably large value of the maximum energy product can be obtained by the method.
  • the third-type method using a low melting-point powder is based on an idea that the particles of the low melting-point phase in the powder mixture may have an effect of removing the nucleation sites, such as the lattice defects and the oxide phase, found on the grain boundary of the R 2 Fe 14 B compound during sintering to have an effect of cleaning of the grain boundaries leading to an increase in the coercive force. Presence of such a low melting-point phase in the powder mixture, however, is an adverse condition for the improvement of the magnetic properties of the permanent magnets to cancel the advantage.
  • the melt of this phase would have a considerably decreased viscosity at the temperature of sintering which is usually at about 1100 °C so that the magnetic particles which have been oriented in the molding process in a magnetic field may float in the low-viscosity melt to cause random rotation resulting in shuffling of once magnetically oriented particles in the course of sintering which proceeds by the liquid-phase sintering to effect shrinkage of the molded body.
  • the melt of the low melting-point phase in the sintering process has a viscosity high enough not to allow free rotation of the magnetic particles but low enough to give a fully densified structure of the sintered body with a full cleaning effect of the grain boundaries.
  • the present invention accordingly has an object to provide a two-alloy method of preparing a rare earth-based permanent magnet having well-balanced magnetic properties.
  • the two-alloy methods however have been established after a fundamental reconsideration of the above discussed problems in the prior art two-alloy methods relative to the composition of each of the alloy powders.
  • the method of preparing a rare earth-based permanent magnet comprises the steps of:
  • the second alloy powder is characterized by the unique metallographic structure including, besides the R 2 T 14 B phase, at least one of the phases having a chemical composition of the formulas RT 4 L, RT 3 , RT 2 , R 2 T 7 and RT 5 , in which R and T each have the same meaning as defined above and L is boron or a combination of boron and the element M, e.g., gallium.
  • the method of preparing a rare earth-based permanent magnet of the invention is a so-called two-alloy method in which powders of two kinds of magnetic alloys having a specified but different compositions are mixted together in a specified weight proportion and the powder mixture is subjected to shaping by molding in a magnetic field to give a green body which is sintered by heating in vacuum or in an atmos- pere of an inert gas such as argon followed, usually, by an aging treatment at a temperature substantially lower than the sintering temperature.
  • an inert gas such as argon
  • the first of two magnetic alloys is basically a ternary alloy mainly consisting of the metallographic phase expressed by the formula R 2 T l4 B.
  • R is a rare earth element including yttrium but preferably selected from the group consisting of neodymium, praseodymium, dysprosium and terbium although a limited portion thereof can be replaced with other rare earth elements including yttrium and the elements having an atomic number in the range from 57 to 71 inclusive.
  • T in the formula is iron or a combination of at least 60% by weight of iron and 40% by weight or less of cobalt.
  • cobalt is an optimal ingredient
  • the amount thereof in the combination of iron and cobalt, when added should be at least 0,1% by weight or, preferably, at least 1% by weight in order that the advantage obtained by the combined use of cobalt can be fully exhibited.
  • addition of cobalt to the Alloy I is effective in increasing the Curie point of the alloy and also increasing the corrosion resistance of the magnet.
  • the Alloy I is prepared by melting together each a specified and weighed amount of the respective ingredients R, i.e. one or more of the rare earth elements, T, i.e. iron or iron and cobalt, and boron each in a metallic or elementary form in vacuum or in an atmosphere of an inert gas which is preferably argon. It is optional to use a ferroboron as the source material of boron and a part of the iron source in combination with an appropriate amount of elementary iron or boron to adjust the iron to boron ratio depending on the composition of the ferroboron.
  • the above mentioned source materials of the respective ingredients shoud have a purity as high as possible, small amounts of impurities usually unavoidable in industrial production of the materials may have no particular adverse influences.
  • the melt of the alloy is cast in a metal mold and cooled to give an alloy ingot mainly consisting of the phase of R 2 T l4 B. Since this phase is formed by the peritective reaction between the incipient phase of a-iron and a liquid phase rich in the content of the rare earth element, it would be a possible case that the ingot of the Alloy I contains small amounts of the remaining a-iron phase, a phase rich in the content of boron and/or a phase rich in the content of the rare earth element.
  • the alloy ingot is subjected to a solution treatment by heating at 700 to 1200 °C for at least 1 hour in vacuum or in an atmosphere of an inert gas so as to convert these phases into the phase of R 2 T l4 B, the fraction of which should desirably be as large as possible.
  • the ingot of the Alloy I obtained in the above described manner is finely pulverized either by a wet process or dry process using a suitable pulverizing machine. Namely, the ingot is first crushed into coarse particles which are then finely pulverized. It is essential in each method of pulverization that surface oxidation of the alloy particles, which is highly reactive with atmospheric oxygen, should be avoided as far as possible.
  • the wet-process pulverization is performed in a non-reactive organic solvent such as fluorinated hydrocarbon solvents and the dry-process pulverization is performed in an atmosphere of an inert gas such as nitrogen.
  • nitrogen is used as the jet gas.
  • the powder of the Alloy I shoud have an average particle diameter in the range from 0.5 to 20 f..lm or, preferably, in the range from 1 to 10 ⁇ m.
  • the average particle diameter of the particles is too large, the powder mixture of the two magnetic alloys cannot be sintered to effect full densification while the average particle diameter should not be too small because a too fine powder is highly susceptible to the surface oxidation of the particles by the atmospheric oxygen to cause serious degradation of the magnetic properties of the magnets.
  • the second of the two magnetic alloys is basically a five-component alloy having a composition represented by the formula R a F Ob C Oe B d M e , in which R has the same meaning as defined above for the Alloy I and M is an element selected from the group consisting of gallium, aluminum, copper, zinc, indium, silicon, phosphorus, sulfur, titanium, vanadium, chromium, manganese, germanium, zirconium, niobium, molybdenum, palladium, silver, cadmium, tin, antimony, hafnium, tantalum and tungsten or, preferably, gallium.
  • the subscript a in the formula is a positive number in the range from 15 to 40 or, preferably, from 25 to 35
  • b is zero or a positive number not exceeding 80 or, preferably, a positive number in the range from 5 to 45
  • c is a positive number in the range from 5 to 85 or, preferably, in the range from 15 to 65
  • d is zero or a positive number not exceeding 20 or, preferably, a positive number in the range from 1 to 15
  • e is zero or a positive number not exceeding 20 or, preferbly, not exceeding 10 with the proviso that the sum of the subscripts a+b+c+d+e is 100.
  • the atomic fraction of the rare earth element is too small, the deficiency in the content of the rare earth element provides no sufficient amount of the liquid phase in the sintering process so that the sintered body cannot be fully densified.
  • the melting point of the Alloy II would be too low to exhibit the desired effect for the improvement of the magnetic properties of the resulting permanent magnet.
  • the method forthe preparation of an ingot of the Alloy II or a fine powder thereof is not different in principle from that for the preparation of an ingot of the Alloy I or a fine powder thereof described above.
  • the requirement for the average particle diameter of the Alloy II powder is also about the same as for the Alloy I powder.
  • the liquid-quenching method is applicable also in this case. Namely, the thin belt of the alloy formed by quenching, which is crystallographically amorphous or microcrystalline, formed by the liquid-quenching method is subjected to a heat treatment at a temperature higher than the temperature of crystallization for a certain length of time so as to cause crystallization or growth by recrystallization resulting in the appearance of the characteristic phase or phases.
  • the metallographic phases contained in the Alloy II include, besides the phase of the formula R 2 T l4 B, in which R and T each have the meaning as defined before, and a phase rich in the content of the rare earth element or elements containing at least 35 atomic % of the rare earth element or elements, which were also the constituents of the alloys used in the prior art two-alloy method or the rare earth-boron based magnetic alloys known in the prior art, at least one of the above mentioned five kinds of the unique metallographic phases which appear as an equilibrium phase in the Alloy II as a consequence of the high cobalt content of at least 5 atomic %.
  • these phases each have a melting point in the range from 700 to 1155 °C, which is suitable for the liquid-phase sintering of the neodymium-containing rare earth-based permanent magnet prepared by the method of sintering.
  • the above mentioned melting point is higher than the melting point of the phase rich in the content of neodymium, i.e. 500 to 650 °C, but lower than the melting point of the R 2 Fe 14 B phase which is 1155 °C.
  • the relatively high resistance of the Alloy II against oxidation is a consequence of the content of cobalt therein. While otherwise the Alloy II is more susceptible to oxidation than the Alloy I due to the higher content of the rare earth element or elements than the Alloy I, addition of cobalt to the Alloy II has an effect of compensating for the increase in the oxidation susceptibility so as to contribute to the stabilization of the magnetic properties of the magnet obtained therefrom by preventing degradation due to oxidation. When gallium is contained as the element M in the Alloy II, gallium is concentrated at the grain boundaries even after sintering to exhibit an effect of increasing the coercive force of the sintered magnet.
  • the powders of the Alloys I and II prepared in the above described manner are mixed together in a specified weight proportion as uniformly as possible. This mixing process is also conducted in an atmosphere of an inert gas such as nitrogen in order to minimize oxidation of the particle surface.
  • an inert gas such as nitrogen
  • each of the alloys is first crushed into coarse particles and the coarse particles of the respective alloys are mixed together in a specified weight proportion followed by fine pulverization.
  • the mixing proportion of the powder of the Alloy I to the powder of the Alloy II is in the range from 99:1 to 70:30 by weight or, preferably, in the range from 95:5 to 85:15 by weight.
  • the density of the sintered magnet cannot be fully increased so as not to give a high coercive force while, when the content thereof is too large, the non-magnetic phases would have some predominance in the sintered body so that the saturation magnetic flux density of the magnet would be decreased.
  • the powder mixture of the Alloys I and II is then shaped into a green body of a desired form of the magnet by compression molding in a magnetic field.
  • the direction of the magnetic field is usually perpendicular to the direction of compression but can be parallel. Quite satisfactory results of magnetization molding can be obtained in a magnetic field of 15 kOe and under a compression force of 1000 kgf/cm 2 though not particularly limitative thereto.
  • the green body of the powder mixture as compression-molded is subjected to sintering by heating in vacuum or in an atmosphere of an inert gas such as argon at a temperature in the range from 900 to 1200 °C for a length of time of at least 30 minutes.
  • the sintered body is usually subjected to an aging treatment by heating at a temperature substantially lower than the sintering temperature or, usually, in the range from 400 to 800 °C for 30 minutes or longer.
  • the sinterign process of the green body of the mixed powders is so efficient that the thus sintered body usually has a high density of at least 95% of the true density, i.e. the density of an alloy ingot having the same chemical as the average composition of the mixed powders, so as to exhibit a high residual magnetic flux density.
  • An ingot of an alloy referred to as the Alloy 1-1 hereinbelow, having a composition of the formula 12.5.Nd-6.0B-81.5Fe in the atomic proportion, was prepared in Inventive Example 1 by melting together neodymium metal and iron metal each having a purity of at least 99.9% by weight and a ferroboron containing about 20% by weight of boron, the balance being iron, each in a calculated and weighed amount to give a composition of the above given formula under an atmosphere of argon in a high-frequency induction-furnace followed by casting of the melt.
  • the ingot was subjected to a solution treatment by heating at 1070 °C for 20 hours under an atmosphere of argon.
  • an ingot of another alloy referred to as the Alloy 11-1 hereinbelow, was prepared in substantially the same manner as above from metals of neodymium, dysprosium, iron, gallium and cobalt each having a purity of at least 99.9% by weight and a ferroboron each in a calculated and weighed amount corresponding to the composition of the formula 20.0Nd-10.0Dy-20.0Fe-6.0B-4.0Ga-40.0Co.
  • the Alloys 1-1 and 11-1 were separately pulverized in an atmosphere of nitrogen each into a coarse powder having a particle size to pass a 30 mesh screen and these coarse powders of the Alloy 1-1 and Alloy 11-1 were taken and blended in a weight ratio of 90:10 taking 30 minutes in a V-mixer filled with nitrogen gas to replace air.
  • the powder blend was then finely pulverized in a jet mill using high-pressure nitrogen as the jet gas into a fine powder mixture having an average particle diameter of about 5wm.
  • a metal mold was filled with the fine powder mixture obtained above, which was brought in a magnetic field of 15 kOe to effect magnetic orientation of the particles and compression-molded under a compressive pressure of about 1000 kgf/cm 2 into a shaped green body.
  • This green body was subjected to sintering by heating at 1070 °C for 1 hour under an atmosphere of argon in a sintering furnace followed by an aging treatment by keeping for 1 hour at a temperature of 530°C into a sintered permanent magnet, which is referred to as the Magnet 1a a hereinbelow.
  • an ingot of a further alloy referred to as the Alloy III-1
  • the Alloy III-1 was prepared in substantially the same manner as above from the same lots of the metals of neodymium, dysprosium, iron, gallium and cobalt and ferroboron each taken in an amount corresponding to the composition of the formula 13.1 Nd-0.8Dy-3.2Co-6.0B-0.3Ga-76.6Fe in the atomic percentage, which was equivalent to the weighted average of the two formulas 12.5Nd-6.0B-81.5Fe for the Alloy 1-1 and 20.0Nd-1 0.0Dy-20.0Fe-6.0B-4.0Ga-40.0Co for the Alloy 11-1 combined in a weight ratio of 90:10.
  • the ingot of the Alloy III-1 was pulverized into a fine powder in the same manner as in the pulverization of the Alloy 1-1 and 11-1 and the fine powder of the Alloy III-1 was processed singly into a permanent magnet, referred to as the Magnet 1 b hereinbelow, in the same manner as above.
  • the Magnets 1a and 1 b prepared above were subjected to the measurements of the density p in g/cm 3 and the magnetic properties including residual magnetic flux density Br in kG, coercive force iHc in kOe and maximum energy product (BH) max in MGOe to give the results shown in Tables 4 and 5, respectively, given below.
  • the Magnets 2a to 70a and 2b to 70b were each subjected to the measurements of the density and magnetic properties to give the results respectively shown in Table 4 below, which also shows the mixing ratio of the two types of the alloys by weight in Inventive Examples 2 to 70, and in Table 5 below.

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Claims (6)

1. Verfahren zur Herstellung eines Dauermagneten, umfassend die Schritte des:
a) Mischens eines Pulvers aus einer ersten magnetischen Legierung mit einer ternären Zusammensetzung, die im wesentlichen durch die Formel
Figure imgb0020
dargestellt wird, in der R ein Element der seltenen Erden bedeutet und T Eisen oder eine Kombination von Eisen und Cobalt in solch einem Verhältnis, daß die Cobaltmenge 40 Gew.-% der Gesamtmenge von Eisen und Cobalt nicht überschreitet, und eines Pulvers aus einer zweiten magnetischen Legierung mit einer Zusammensetzung, die im wesentlichen durch die Formel
Figure imgb0021
dargestellt wird, in der R die gleiche Bedeutung wie oben definiert aufweist, Mein Element, ausgewählt aus der aus Gallium, Aluminium, Kupfer, Zink, Indium, Silicium, Phosphor, Schwefel, Titan, Vanadium, Chrom, Mangan, Germanium, Zirconium, Niobium, Molybdän, Palladium, Silber, Cadmium, Zinn, Antimon, Hafnium, Tantal und Wolfram bestehenden Gruppe bedeutet, der tiefgestellte Index a eine positive Zahl im Bereich von 15 bis 40 bedeutet, b Null oder eine positive, 80 nicht überschreitende Zahl bedeutet, c eine positive Zahl im Bereich von 5 bis 85 bedeutet, d Null oder eine positive, 20 nicht überschreitende Zahl bedeutet und e Null oder eine eine positive, 20 nicht überschreitende Zahl bedeutet, unter der Bedingung, daß a + b + c + d + e gleich 100 ist, in einem Gewichtsverhältnis des ersten magnetischen Legierungspulvers zu dem zweiten magnetischen Legierungspulver im Bereich von 99:1 bis 70:30, um ein Pulvergemisch zu ergeben,
b) Formens des Pulvergemisches in eine Form eines Magneten durch Kompressionsformen in einem Magnetfeld, und
c) Sinterns der geformten Form des Pulvergemisches durch Erhitzen im Vakuum oder in einer Atmosphäre eines Inertgases.
2. Verfahren zur Herstellung eines Dauermagneten auf der Basis von seltenen Erden nach Anspruch 1, bei dem das mit M bezeichnete Element Gallium ist.
3. Verfahren zur Herstellung eines Dauermagneten auf der Basis von seltenen Erden nach Anspruch 1, bei dem das mit R bezeichnete Element ein Element der seltenen Erden, ausgewählt aus der aus Neodymium, Praseodymium, Dysprosium und Terbium bestehenden Gruppe, ist.
4. Verfahren zur Herstellung eines Dauermagneten auf der Basis von seltenen Erden nach Anspruch 3, bei dem das mit R bezeichnete Element Neodymium ist.
5. Verfahren zur Herstellung eines Dauermagneten auf der Basis von seltenen Erden nach Anspruch 1, bei dem der tiefgestellte Index a eine positive Zahl im Bereich von 25 bis 35 bedeutet, b eine positive Zahl im Bereich von 5 bis 45 bedeutet, c eine positive Zahl im Bereich von 15 bis 65 bedeutet, d eine positive Zahl im Bereich von 1 bis 15 bedeutet und e Null oder eine eine positive, 10 nicht überschreitende Zahl bedeutet, unter der Bedingung, daß a + b + c + d + e gleich 100 ist.
6. Verfahren zur Herstellung eines Dauermagneten auf der Basis von seltenen Erden nach Anspruch 1, bei dem die zweite magnetische Legierung eine metallographische Struktur aufweist, die die Phasen von R2T14B und mindestens einer der Formeln RT4L, RT3, RT2, R2T7 und RT5 umfaßt, in denen R und T die gleiche Bedeutung wie oben definiert aufweisen und L Bor oder eine Kombination von Bor und dem die gleiche Bedeutung wie oben definiert aufweisenden Element M bedeutet.
EP92109366A 1991-06-04 1992-06-03 Verfahren zur Herstellung von zweiphasigen Dauermagneten auf der Basis von Seltenen Erden Expired - Lifetime EP0517179B1 (de)

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP3159766A JP2853839B2 (ja) 1991-06-04 1991-06-04 希土類永久磁石の製造方法
JP3159765A JP2853838B2 (ja) 1991-06-04 1991-06-04 希土類永久磁石の製造方法
JP159765/91 1991-06-04
JP159766/91 1991-06-04
JP03198476A JP3143156B2 (ja) 1991-07-12 1991-07-12 希土類永久磁石の製造方法
JP198476/91 1991-07-12

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EP0517179B1 true EP0517179B1 (de) 1995-05-17

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DE19636285A1 (de) * 1996-09-06 1998-03-12 Vakuumschmelze Gmbh Verfahren zur Herstellung eines SE-Fe-B-Dauermagneten
WO2021249159A1 (zh) * 2020-06-11 2021-12-16 厦门钨业股份有限公司 重稀土合金、钕铁硼永磁材料、原料和制备方法

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FR2707421B1 (fr) * 1993-07-07 1995-08-11 Ugimag Sa Poudre additive pour la fabrication d'aimants frittés type Fe-Nd-B, méthode de fabrication et aimants correspondants.
US5482575A (en) * 1992-12-08 1996-01-09 Ugimag Sa Fe-Re-B type magnetic powder, sintered magnets and preparation method thereof
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