EP0249973A1 - Dauermagnet-Material und Verfahren zur Herstellung - Google Patents

Dauermagnet-Material und Verfahren zur Herstellung Download PDF

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EP0249973A1
EP0249973A1 EP87108724A EP87108724A EP0249973A1 EP 0249973 A1 EP0249973 A1 EP 0249973A1 EP 87108724 A EP87108724 A EP 87108724A EP 87108724 A EP87108724 A EP 87108724A EP 0249973 A1 EP0249973 A1 EP 0249973A1
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Prior art keywords
magnetic
powder
cementing
metallic
bulk
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French (fr)
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EP0249973B1 (de
Inventor
Kinya Sasaki
Etsuo Otsuki
Tsutomu Otsuka
Teruhiko Fujiwara
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Tokin Corp
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Tokin Corp
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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
    • H01F1/0578—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 bonded together
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/09—Mixtures of metallic powders
    • 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

  • This invention relates to a permanent magnet material of a bulk shape and, in particular, to an iron-rare earth metal-boron (R-Fe-B) permanent magnet material with a high coercive force.
  • R-Fe-B iron-rare earth metal-boron
  • Permanent magnets have been used in various applications such as electromechanical apparatus.
  • a possible approach has been directed to a novel intermetallic compound of transition metal (T) and rare earth metal (R) instead of the Sm-Co intermetallic compound.
  • J. J. Croat proposed amorphous (Nd and/or Pr)-Fe-B alloy having magnetic properties for a permanent magnet as disclosed in JP-A-60009852. Those magnetic properties was considered to be caused by a microstructure where Nd 2 Fe 14 B particles having a perticle size of 20-30 nm were dispersed within an amorphous Fe phase. Reference is further made to R. K. Mishra: J. Magnetism and Magnetic Materials 54-57 (1986) 450.
  • the amorphous alloy can provide only an isotropic magnet because of its crystallographically isotropy. This means that a high performance permanent magnet cannot be obtained from the amorphous alloy.
  • the R-Fe-B sintered magnet has a problem in considerably low corrosion resistance.
  • a magnetic body with a high coercive force for a permanent magnet which consists essentially of a metallic cementing phase and magnetic crystalline particles uniformly dispersed within the metal cementing phase.
  • the cementing phase is 10% or less by volume of the magnetic body and comprises at least one element selected from a first metallic group of Al, Zn, Sn, Cu, Pb, S, In, Ga, Ge, and Te.
  • the magnetic crystalline particles is substantially balance of the volume of the magnetic body and is a composition represented by a chemical formula R 2 T 14 B, where R is at least one element selected from Y and rare earth metals, T being transition metal and comprising Fe 50-100 at% in the transition metal.
  • Each of the magnetic particles is embedded in the cementing phase to form an interface therebetween.
  • the cementing phase is inert to oxygen in comparison with Nd and has, therefore, a good corrosion resistance.
  • the cementing phase may comprise an intermetallic compound of at least one of the first metallic group and at least one selected from a second netallic group of R, T, and B.
  • the present invention further provides a method Eor producing a magnetic body with a high coercive force for a permanent magnet.
  • the method comprises steps of: preparing an ingot of R-T-B magnetic alloy comprising a magnetic intermetallic compound represented by a chemical formula of R 2 T 14 B, where R is at least one element selected from Y and rare earth metals, T being transition metal but comprising Fe 50-100 at% in the transition metal; pulverizing and milling the ingot to thereby prepare a magnetic powder; preparing a metallic cementing powder comprising at least one element selected from a first metallic group of Al, Zn, Sn, Cu, Pb, S, In, Ga, Ge, and Te; mixing the metallic cementing powder of 10% or less by volume and the magnetic powder of substantially balance to prepare a mixed powder; and forming a bulk-shape body of the mixed powder at an elevated temperature.
  • the bulk-shape body forming step comprises steps of; compacting the mixed powder under influence of a grain aligning magnetic field into a compact body of a predetermined shape; and sintering the compact body at a temperature lower than a peritectic reaction temperature of the magnetic powder but higher than a melting temperature of the metallic cementing powder to thereby produce, as the bulk-shape body, a sintered body.
  • the sintered body may be subjected to a heat treatment at a temperature, preferably, 300-900 C for improving the magnetic properties of the sintered body.
  • the bulk-shape body forming step may be hot compaction process for hot compacting the mixed powder into the bulk-shape body at an elevated temperature lower than 1,100 °C but higher than a melting temperature of the metallic cementing powder.
  • the hot compaction process is a hot-pressing process and alternatively a hot-extrusion process.
  • the present invention attempts to provide a permanent magnet material with a high coercive force and a corrosion resistance by making the material to have a microstructure as shown in Fig. 1 where magnetic particles of stoichiometric intermetallic compound of Nd 2 Fe 14 B are dispersed within a metallic cementing phase.
  • the metallic cementing phase is composed of metallic elements and/or an intermetallic compound or compounds, which are inert to oxygen in comparison with Nd.
  • Nd 2 Fe 14 B powder and metallic cementing powder are separately prepared and those powder are mixed.
  • the mixed powder is sintered or hot-formed at an elevated temperature into a bulk-shape body so that the cementing powder forms a cementing phase to cement the magnetic particles together.
  • the metallic element or elements are selected to be ones each having a melting point lower than a peritectic temperature of the intermetallic compound of Nd 2 Fe 14 B, and the elevated temperature is also selected lower than the peritectic temperature but higher than the melting point of the cementing powder. Therefore, only the cementing powder melts to form the cementing phase by the sintering process or hot compaction process while the intermetallic compound of the magnetic powder is not melted but dispersed within the cementing phase.
  • Nd is active to oxygen if they do not form any intermetallic compound together or with other metallic element or elements. Therefore, it is desired that the cementing phase includes no Nd.
  • Nd and Fe are included in the cementing powder in the form of an intermetallic compound or compounds with other metallic element or elements.
  • the magnetic powder is prepared as an alloy powder including Nd and Fe in addition to the intermetallic compound of Nd 2 Fe 14 B '
  • Nd and Fe are present in the cementing phase of the produced body.
  • Nd forms an intermetallic compound with the other metallic element or elements. Accordingly, the cementing phase is also excellent in corrosion resistance.
  • both of the former and the latter can be employed.
  • a comparatively low temperature is used in the hot compaction process, the latter is employed because intermetallic compound of Nd and Fe with the other metallic element is apt to have a melting temperature higher than the temperature for hot compaction.
  • the amount of the cementing powder is limited at maximum 10 % by volume of the mixed powder, because when the cementing powder exceeds 10 vol%, the amount of the magnetic powder is insufficient to obtain a high remanence.
  • the intermetallic compound of Nd2Fel4B has a high residual magnetic flux density but has not a coercive force sufficient for a permanent magnet.
  • An-ingot of an intermetallic magnetic alloy represented by Nd 13 Fe 81 B 6 was prepared by the induction melting in argon gas atmosphere. Purity factors of used start materials of Nd, Fe (electrolytic iron), and B were 98%, 99.9%, and 99.5% or more, respectively.
  • the ingot was pulverized by a crusher to have a particle size below 24 mesh (Tyler) and, thereafter, finely divided by a ball mill into a fine magnetic powder having an average particle size of 3 pm.
  • Each metallic powder was mixed with the fine magnetic powder to form mixed powder.
  • Each metal was adjusted at 5% by volume of the mixed powder.
  • Zn, Al, S, In, Ga, Ge, Sn, Te, Cu, and Pb were, by weight, 5%, 2%, 2%, 5%, 4%, 4%, 5%, 4%, 6%, and 7% in the mixed powders, respectively.
  • each mixed powder was hot-pressed into a desired bulk-shape body under a pressing stress of 1,000 Kg.f/cm 2 at a temperature of 600 0 C within argon gas atmosphere for 15 minutes.
  • Table 1 teaches that the samples Nos. 1-10 according to an embodiment of this invention are superior to comparing samples Nos. 11 and 12 according to the known production method in the magnetic properties, especially, the maximum energy product (BH)max.
  • a fine magnetic powder of Nd 13 Fe 81 B 6 was prepared and was mixed with metal powders (each having an average particle size of 20-30 um ) of Zn 5wt%, Al 2wt%, S 2wt%, In 5wt%, Ga 4wt%, Ge 4wt%, Sn 5wt%, Te 4wt%, Cu 6wt%, and Pb 7wt%, respectively, in the similar manner as described in Example 1.
  • Each mixed powder was compacted into a compact body of a desired bulk-shape by application of a pressing force of 1.5 ton.f/cm 2 under influence of a grain aligning magnetic field of 25 KOe.
  • the compact body was hot-pressed at 600°C by pressing stress of 1,000 Kg.f/cm 2 within vacuum for 15 minutes.
  • Each hot-pressed body was subjected to measurement of density and magnetic properties. The measured data are shown as sample Nos. 13-22 in Table 2.
  • alloy ingots of (Nd 15 Fe 77 B 7 ) 95 Al 5 andNd 14 Fe 81 B 6 were produced and were finely ground into powders. Those powders were compacted into compact bodies of a desired bulk shape and were hot-pressed in the similar manner. Densities and magnetic properties of those hot-pressed bodies are shown as sample Nos. 23 and 24 in Table 2.
  • sample Nos. 13-22 according to embodiments of the present invention are superior in the magnetic properties to not only comparing samples of Nos 23 and 24 according to the known producing method but also samples of Nos. 1-10 in Table 1 according to embodiments of the present invention.
  • Nd 2 Fe 14 B magnetic alloy ingot was prepared and was pulverized to have a particle size below 24 mesh (Tyler).
  • start materials of Nd having a purity factor of 98% or more
  • Fe having a purity factor of 99.9% or more
  • Al having a purity factor of 99.9%
  • Both of the powders were blended with each other at various mixing ratios so that Nd 30 Fe 40 A1 30 powder is 0-15% by volume of the blended powder.
  • Each blended powder was finely ground into a powder of an average particle size of about 4 ⁇ m.
  • the finely ground powder was compacted into a compact body of a desired bulk-shape by application compacting stress of 1.5 ton.f/cm 2 under influence of a grain aligning magnetic field of 20 KOe.
  • the compact body was sintered in vacuum at 1,000-1,150 °C for 2 hours.
  • the sintered body was heat treated at 500-900 °C for one hour.
  • Density d, residual magnetic flux density Br, coercive force I H C , and (BH)max of the sintered body after heat treatment were measured and are illustrated in Fig. 2 for various volume percents of Nd 30 Fe 40 Al 30 in the sintered body.
  • Fig. 2 the maximum magnetic properties are obtained at 5 vol% of Nd 30 Fe 40 Al 30 content.
  • the magnetic properties are shown as a sample No. 25 in Table 3.
  • the table also has properties of a comparing sample No. 26 which was a sintered Nd 14 Fe 80 B 6 alloy produced from the alloy ingot through milling, compacting in the aligning magnetic field, sintering, and heat treating steps according to a conventional powder metallurgy.
  • sample No.25 according to the present invention has a considerably excellent magnetic properties in comparison with sample No. 26 according to the conventional process.
  • the sintered body of sample No. 25 was cross-sectioned and polished.
  • the microstructure in the polished surface was observed by a Scanning Electron Microscope (SEM).
  • SEM Scanning Electron Microscope
  • the magnetic crystalline particles (being black) of Nd 2 Fe 14 B are covered with, or embedded in, a cementing phase (being white) of Nd 30 Fe 40 Al 30 .
  • This example teaches us that magnetic properties of sintered Nd 2 Fe 14 B magnet can be considerably improved by covering and cementing the Nd 2 Fe 14 B particles with the Nd(Fe, Al) 3 matrix or the cementing phase.
  • Fig. 2 shows that the magnetic properties gradually decrease along increase of the cementing phase from 5 vol% through 8 vol%. It is considered that this is because of decrease of the amount of the magnetic particles.
  • Nd 2 Fe 14 B alloy powder and Nd 30 Fe 40 Al 30 alloy powder produced through the similar steps as described in Example 3 were blended with each other so that Nd 30 Fe 40 Al 30 powder was 5% of volume of the blended powder.
  • the blended powder was compacted to a desired bulk shape in the grain aligning magnetic field of 20 KOe by application of compacting force of 1.5 ton.f/cm 2 and produced a green compact body.
  • the green compact body was subjected to a hot compaction by hot-pressing the green compact at 800 C in argon gas atmosphere by 1,000 Kg.f/cm 2 for 15 minutes.
  • Density and magnetic properties of the hot-pressed body were measured and are described with sample number of No. 27 in Table 5.
  • sample No. 28 is a sample produced from a Nd 14 Fe 80 B 6 powder through the similar compacting and hot-pressing steps.
  • Nd 2 Fe 14 B magnetic alloy powder with an average particle size of 3 ⁇ m was prepared in the similar manner as described in Example 1. While, NdCu 2 powder for the cementing phase material having similar particle size was also produced in a similar producing method. Both powders were mixed with each other so that the amount of NdCu 2 powder was about 10% by volume in the mixture, and the mixture was uniformly mixed in a ball mill. The mixture was compacted into a bulk shape by application of compacting stress of 1.5 ton.f/cm 2 in the grain aligning magnetic field of 20 KOe. The compacted body was sintered in vacuum at 1,100-1,130 °C for 2 hours. The sintered body was heat-treated in argon gas atmosphere at 600-800 °C for one hour.
  • the magnetic properties of the sintered body as sample No. 29 are shown in Table 6 together with its density.
  • No. 29 sample was then cross-sectioned and polished.
  • the microstructure of the cross-section was observed by use of an optical microscope.
  • the observed microstructure is illustrated in Fig. 4.
  • Nd 2 Fe 14 B magnetic particle is shown in white and the NdCu 2 cementing phase is shown in black.
  • the cementing phase comprises two intermetallic compounds I and II.
  • Compound I is represented by NdCu
  • Compound II is represented by Nd(Cu, Fe ) 2 .
  • each magnetic particle (shown in white in Fig. 4) is cemented and covered with the cementing phase (black in Fig. 4).
  • the mixture was hot-pressed in argon gas atmosphere at 900 °C by application of pressing stress of 1,000 K g.f/cm 2 for 15 minutes.
  • Table 8 shows density and magnetic properties of the hot-pressed body as sample No. 30. Table 8 teaches us that excellent magnetic properties are obtained.
  • N d 2 Fe 14 B magnetic powder similar to Example 5 was prepared. While, Nd 25.4 Cu 52.2 Zn 22.4 powder for the cementing phase was prepared in the similar manner as the magnetic powder. Both of the powders were blended with each other so that the amount of the Nd 25.4 Cu 52.2 Zn 22.4 powder was about 10% by volume of the blended powder. The blended powder was uniformly mixed in ball mill. The mixture was hot-pressed into a body of a desired shape in argon gas at 600 °C by pressing stress of 1,000 Kg.f/cm 2 for 15 minutes.
  • a molten alloy of Nd 34 Fe 65 B was prepared in the similar way as in Example 1.
  • a powder less than.250 (Tyler) mesh was prepared from each of the molten alloys by atomization. Then, Nd 16 Fe 18 B 6 magnetic powder was divided by ball mill into average particle size of about 3 pm. Each powder of Pb-Sn alloys A and B was blended with the magnetic powder and was mixed in ball mill. The amount of each of alloy A and B was 5% by volume of each mixture.
  • Each powder mixture was compacted into a compact body of a bulk shape in the aligning magnetic field of 20 KOe by compacting stress of 1.5 ton.f/cm 2 .
  • the compact body was sintered in vacuum at 1,000-1,150 °C for 2 hours.
  • the sintered body was heat-treated at 500-900 °C for one hour and was thereafter.subjected to measurement of density and magnetic properties.
  • Fig. 5 shows the microstructure of No. 32 sample.
  • the magnetic particles are illustrated in white and the cementing phase is black.
  • the magnetic particle phase consists of the intermetallic compound of Nd 2 Fe 14 B. While, Nd and Fe is present in both of the cementing phase. I and II are analysed data at different portions of the cementing phase of the sintered body.
  • the cementing phase is constituted of an intermetallic compound of Nd(Pb, Fe, Sn) where a part of Pb in NdPb is replaced by Fe and Sn. While, the cementing phase in No. 33 sample is composed of an intermetallic compound of Nd(Sn, Fe, Pb) where a part of Sn in NdSn compound is replaced by Fe and Pb.
  • Nd and Fe diffuse from Nd-Fe-B particles into Pb-Sn phase so that each Nd-Fe-B particle becomes a stoichiometric intermetallic compound R 2 Fe 14 B which has ferromagnetism.
  • each magnetic particle comprises not only the intermetallic compound of Nd 2 Fe 14 B but also non-magnetic phase.
  • the powder mixtures prepared in Example 8 were compacted into green compact bodies in the aligning magnetic field of 20 KOe by compacting stress of 1.5 ton.f/cm 2 .
  • Each green compact body was hot-pressed in argon gas at 750 °C under application of a pressure 1,000 Kg.f/cm 2 for 20 minutes. Thereafter, the hot-pressed body was heat-treated in argon gas at 600 °C for 30 minutes.
  • Nd 2 Fe 14 B magnetic alloy powder similar to Example 3 was prepared.
  • Nd-Fe-Pb-Sn alloy powders C, D, and E in Table 14 were produced from start.materials of Nd (purity of 98 % or more), Fe (purity of 99.9% or more), Pb (purity of 99.9%), and Sn (purity of 99.9%). Each powder of C-E was prepared to have an average particle size of 3 pm.
  • Each powder mixture was compacted into a compact body in the aligning magnetic field of 20 KOe by compacting force of 1.5 ton.f/cm 2 , and the compact body was sintered in vacuum at 1,000-1,150 °C for 2 hours. The sintered body was further heat-treated at 500-900 °C.
  • Table 15 indicates density and magnetic properties of each sintered and heat-treated body as samples Nos. 36, 37, and 38 which use Nd-Fe-Pb-Sn alloys C, D, and E, respectively.
  • Nos. 36-38 samples are nearly equal to them in the magnetic properties but have a reduced Nd content which is active to oxygen. Accordingly, Nos. 36-38 samples are superior to Nos. 32 and 33 samples in the corrosion resistance and especially during production and storage of powder materials.
  • Example 10 Each mixture obtained in Example 10 was compacted into a green compact in the aligning magnetic field of 25 KOe by pressing stress of 1.5 ton.f/cm 2 .
  • the green compact was hot-pressed in argon gas at 800 °C by pressing stress of 1.0 ton.f/cm 2 for 20 minutes. Then, the hot-pressed body was heat-treated in argon gas atmosphere at 600 °C for 30 minutes.
  • Table 17 shows density and magnetic properties of each hot-pressed body after heat-treated as samples Nos. 39, 40, and 41.
  • Nos. 39 and 40 samples have magnetic properties equally to Nos. 34 and 35 samples but have a reduced amount of Nd.
  • a humidity test was carried out onto the test pieces under a test condition of a temperature of 60°C and a humidity of 90% for 100 hours.
  • Test pieces of each sample were coated with surface coatings by electrolytic Ni plating, phosphate treating, and anti-corrosion resin coating, respectively.
  • the electrolytic Ni plating was carried out after Cu plating coating of 3-5 ⁇ m thickness was previously formed.
  • the phosphate treating was performed using a conventional phosphate solution.
  • epoxy resin was dissolved in an organic solvent and then sprayed onto test pieces. Thereafter, epoxy resin coating was formed by heating at 150 °C.
  • test pieces were subjected to salt spray corrosion test under a condition where salt water solution (5% NaCl) was sprayed onto the test pieces at 35 °C for 48 hours during which surface change of each test piece was observed. When the test completed, magnetic properties of each test were measured.
  • salt water solution 5% NaCl
  • Added amounts of Zn, Sn, and Al powders were selected to be 5% by volume of respective powder mixtures.
  • Each powder mixture was compacted in the aligning magnetic field of 25 KOe by pressing stress of 1.5 ton.f/cm 2 and formed a green compact of a desired bulk shape.
  • the green compact was heated at 700 C and then coated with glass coating by depositing glass powder onto the surface of the green compact.
  • the glass coated green compact was inserted in a extrusion mould and was moulded into a desired shape by extrusion.
  • each of Nos. 45 and 46 samples is a hot-pressed body produced from the alloy ingot through pulverizing, compacting, and extruding steps.
  • Magnetic materials according to the present invention can be produced by hot extrusion and has excellent magnetic properties in comparison with one produced from the alloy ingot.
  • Example 12 Each of green compact obtained in Example 12 was hot-pressed in argon gas atmosphere at 700 °C by pressing stress of 1,000 Kg.f/cm 2 for 15 minutes.
  • the hot-pressed body was heat-treated in argon at 600 C for 10 minutes.
  • Fig. 7 illustrates measured coercive force to variation of heat-treating temperature. Fig. 7 shows that the effective temperature is 300-900 0 C.
  • Fig. 8 shows residual magnetic flux density Br and coercive force I H C to variation of heat-treating time period. It will be noted from Fig. 8 that the heat treatment for about 10 minutes is most effective for improvement of the magnetic properties.
  • Al 11 Zn 89 powder and Al 83 Cu 17 powder were produced from starting materials having purity of 98% or more. Each powder has an averaged particle size of 1-10 ⁇ m.
  • Example 2 Each powder and the Nd 13 Fe 81 B 6 magnetic powder obtained in Example 2 were mixed with each other at a mixing ratio of 5 to 95 by volume (which means 4.4 wt% for Al 11 Zn 89 and 2.4 wt% for Nd 13 Fe 81 B 6 ) in a ball mill.
  • the mixture was compacted to a green compact in the aligning magnetic field of 25 KOe by pressing stress of 1.5 ton.f/cm 2 .
  • the green compact was hot-pressed in argon gas atmosphere at 600 °C by pressing stress of 1,000 Kg.f/cm 2 for 15 minutes.
  • the magnetic properties of hot-pressed body of sample Nos. 50 and 51 are described in Table 23.
  • Al 66 Fe 34 powder, Al 25 Ni 75 powder, Al 20 Co 80 powder, and Al 75 Cr 25 powder were used in place of Al 11 Zn 89 powder and Al 83 Cu 17 powder in Example 14, and a green compact was produced from a mixture of each powder and Nd 13 Fe 81 B 6 magnetic powder in similar manner as described in Example 14. The green compact was hot-pressed similarly, but for 10 minutes.
  • Magnetic properties of the hot-pressed body was excellent similarly as in Example 14 and is shown in Table 24 with sample numbers Nos. 52-55 for alloy powders used.

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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)
EP87108724A 1986-06-16 1987-06-16 Dauermagnet-Material und Verfahren zur Herstellung Expired EP0249973B1 (de)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP13965086 1986-06-16
JP139650/86 1986-06-16
JP89028/87 1987-04-11
JP8902887A JPS63114939A (ja) 1986-04-11 1987-04-11 Ｒ↓２ｔ↓１↓４ｂ系複合型磁石材料とその製造方法

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EP0249973A1 true EP0249973A1 (de) 1987-12-23
EP0249973B1 EP0249973B1 (de) 1991-11-06

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Cited By (20)

* Cited by examiner, † Cited by third party
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EP0392077A2 (de) * 1989-04-14 1990-10-17 Hitachi Metals, Ltd. Heissverformte anisotrope Magnete und deren Herstellung
US5006045A (en) * 1987-12-24 1991-04-09 Seiko Epson Corporation Scroll compressor with reverse rotation speed limiter
DE4027598A1 (de) * 1990-06-30 1992-01-02 Vacuumschmelze Gmbh Dauermagnet des typs se-fe-b und verfahren zu seiner herstellung
EP0583041A1 (de) * 1992-08-13 1994-02-16 Koninklijke Philips Electronics N.V. Verfahren zum Herstellen eines Dauermagneten auf Basis von NdFeB
US5354354A (en) * 1991-10-22 1994-10-11 Th. Goldschmidt Ag Method for producing single-phase, incongruently melting intermetallic phases
US6027576A (en) * 1996-09-06 2000-02-22 Vacuumschmelze Gmbh Rare earth element-iron-boron permanent magnet and method for the manufacture thereof
US6045751A (en) * 1992-08-13 2000-04-04 Buschow; Kurt H. J. Method of manufacturing a permanent magnet on the basis of NdFeB
WO2001024202A1 (de) * 1999-09-24 2001-04-05 Vacuumschmelze Gmbh Borarme nd-fe-b-legierung und verfahren zu deren herstellung
EP1517149A2 (de) * 2003-09-16 2005-03-23 Ntn Corporation Magnetischer Encoder und Radlager mit einem solchen Encoder
EP1679724A1 (de) * 2003-10-31 2006-07-12 TDK Corporation Verfahren zur herstellung eines gesinterten seltenerdelement-magneten
US7592799B2 (en) 2004-09-10 2009-09-22 Ntn Corporation Magnetic encoder and wheel support bearing assembly using the same
US20110234350A1 (en) * 2008-12-01 2011-09-29 Zhejiang University Modified nd-fe-b permanent magnet with high corrosion resistance
JP2012049492A (ja) * 2010-07-30 2012-03-08 Hitachi Metals Ltd 希土類永久磁石の製造方法
US20130323111A1 (en) * 2011-02-21 2013-12-05 Toyota Jidosha Kabushiki Kaisha Method of production of rare earth magnet
US20140132377A1 (en) * 2011-07-08 2014-05-15 Showa Denko K.K. Alloy for r-t-b-based rare earth sintered magnet, process of producing alloy for r-t-b-based rare earth sintered magnet, alloy material for r-t-b-based rare earth sintered magnet, r-t-b-based rare earth sintered magnet, process of producing r-t-b-based rare earth sintered magnet, and motor
US10695840B2 (en) * 2015-04-29 2020-06-30 Lg Electronics Inc. Sintered magnet based on MnBi having improved heat stability and method of preparing the same
CN112712955A (zh) * 2020-12-23 2021-04-27 安徽大地熊新材料股份有限公司 烧结钕铁硼磁体及其制备方法
CN112820528A (zh) * 2020-05-06 2021-05-18 廊坊京磁精密材料有限公司 提高烧结钕铁硼矫顽力的方法
US20230290546A1 (en) * 2022-01-27 2023-09-14 Ford Global Technologies, Llc Reduction of cracks in additively manufactured nd-fe-b magnet
CN118471675A (zh) * 2023-10-23 2024-08-09 江苏普隆磁电有限公司 一种钕铁硼磁体的制备方法

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Publication number Priority date Publication date Assignee Title
US20160293305A1 (en) * 2013-03-25 2016-10-06 Intermetallics Co., Ltd. Sintered magnet production method

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US5006045A (en) * 1987-12-24 1991-04-09 Seiko Epson Corporation Scroll compressor with reverse rotation speed limiter
EP0392077A3 (de) * 1989-04-14 1991-06-26 Hitachi Metals, Ltd. Heissverformte anisotrope Magnete und deren Herstellung
EP0392077A2 (de) * 1989-04-14 1990-10-17 Hitachi Metals, Ltd. Heissverformte anisotrope Magnete und deren Herstellung
DE4027598A1 (de) * 1990-06-30 1992-01-02 Vacuumschmelze Gmbh Dauermagnet des typs se-fe-b und verfahren zu seiner herstellung
US5354354A (en) * 1991-10-22 1994-10-11 Th. Goldschmidt Ag Method for producing single-phase, incongruently melting intermetallic phases
US6045751A (en) * 1992-08-13 2000-04-04 Buschow; Kurt H. J. Method of manufacturing a permanent magnet on the basis of NdFeB
EP0583041A1 (de) * 1992-08-13 1994-02-16 Koninklijke Philips Electronics N.V. Verfahren zum Herstellen eines Dauermagneten auf Basis von NdFeB
US6027576A (en) * 1996-09-06 2000-02-22 Vacuumschmelze Gmbh Rare earth element-iron-boron permanent magnet and method for the manufacture thereof
WO2001024202A1 (de) * 1999-09-24 2001-04-05 Vacuumschmelze Gmbh Borarme nd-fe-b-legierung und verfahren zu deren herstellung
DE19945943B4 (de) * 1999-09-24 2005-06-02 Vacuumschmelze Gmbh Borarme Nd-Fe-B-Legierung und Verfahren zu deren Herstellung
EP1517149A2 (de) * 2003-09-16 2005-03-23 Ntn Corporation Magnetischer Encoder und Radlager mit einem solchen Encoder
EP1517149A3 (de) * 2003-09-16 2005-04-20 Ntn Corporation Magnetischer Encoder und Radlager mit einem solchen Encoder
US7237960B2 (en) 2003-09-16 2007-07-03 Ntn Corporation Magnetic encoder and wheel support bearing assembly utilizing the same
EP1679724A1 (de) * 2003-10-31 2006-07-12 TDK Corporation Verfahren zur herstellung eines gesinterten seltenerdelement-magneten
EP1679724A4 (de) * 2003-10-31 2010-01-20 Tdk Corp Verfahren zur herstellung eines gesinterten seltenerdelement-magneten
US7592799B2 (en) 2004-09-10 2009-09-22 Ntn Corporation Magnetic encoder and wheel support bearing assembly using the same
US20110234350A1 (en) * 2008-12-01 2011-09-29 Zhejiang University Modified nd-fe-b permanent magnet with high corrosion resistance
US9818515B2 (en) * 2008-12-01 2017-11-14 Zhejiang University Modified Nd—Fe—B permanent magnet with high corrosion resistance
JP2012049492A (ja) * 2010-07-30 2012-03-08 Hitachi Metals Ltd 希土類永久磁石の製造方法
US20130323111A1 (en) * 2011-02-21 2013-12-05 Toyota Jidosha Kabushiki Kaisha Method of production of rare earth magnet
US20140132377A1 (en) * 2011-07-08 2014-05-15 Showa Denko K.K. Alloy for r-t-b-based rare earth sintered magnet, process of producing alloy for r-t-b-based rare earth sintered magnet, alloy material for r-t-b-based rare earth sintered magnet, r-t-b-based rare earth sintered magnet, process of producing r-t-b-based rare earth sintered magnet, and motor
US11024448B2 (en) 2011-07-08 2021-06-01 Tdk Corporation Alloy for R-T-B-based rare earth sintered magnet, process of producing alloy for R-T-B-based rare earth sintered magnet, alloy material for R-T-B-based rare earth sintered magnet, R-T-B-based rare earth sintered magnet, process of producing R-T-B-based rare earth sintered magnet, and motor
US10695840B2 (en) * 2015-04-29 2020-06-30 Lg Electronics Inc. Sintered magnet based on MnBi having improved heat stability and method of preparing the same
CN112820528A (zh) * 2020-05-06 2021-05-18 廊坊京磁精密材料有限公司 提高烧结钕铁硼矫顽力的方法
CN112712955A (zh) * 2020-12-23 2021-04-27 安徽大地熊新材料股份有限公司 烧结钕铁硼磁体及其制备方法
CN112712955B (zh) * 2020-12-23 2023-02-17 安徽大地熊新材料股份有限公司 烧结钕铁硼磁体及其制备方法
US20230290546A1 (en) * 2022-01-27 2023-09-14 Ford Global Technologies, Llc Reduction of cracks in additively manufactured nd-fe-b magnet
CN118471675A (zh) * 2023-10-23 2024-08-09 江苏普隆磁电有限公司 一种钕铁硼磁体的制备方法

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