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WO2018181592A1 - Aimant permanent et machine rotative - Google Patents

Aimant permanent et machine rotative Download PDF

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Publication number
WO2018181592A1
WO2018181592A1 PCT/JP2018/012997 JP2018012997W WO2018181592A1 WO 2018181592 A1 WO2018181592 A1 WO 2018181592A1 JP 2018012997 W JP2018012997 W JP 2018012997W WO 2018181592 A1 WO2018181592 A1 WO 2018181592A1
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WIPO (PCT)
Prior art keywords
permanent magnet
phase
content
atomic
squareness ratio
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PCT/JP2018/012997
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English (en)
Japanese (ja)
Inventor
敦 古田
孝裕 諏訪
信宏 神宮
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Tdk株式会社
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Publication of WO2018181592A1 publication Critical patent/WO2018181592A1/fr

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    • 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
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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

Definitions

  • the present invention relates to a permanent magnet and a rotating machine.
  • An RTB-based permanent magnet containing a rare earth element R, a transition metal element T such as iron (Fe) or cobalt (Co), and boron B has excellent magnetic properties.
  • the main phase of the RTB system permanent magnet contains, for example, a tetragonal R 2 T 14 B compound.
  • the RTB permanent magnet is a high-performance permanent magnet.
  • An RTB-based permanent magnet containing Nd, Pr, Dy, Tb, or Ho as the rare earth element R has a large anisotropic magnetic field Ha and is suitable for a permanent magnet.
  • an Nd—Fe—B permanent magnet containing Nd as the rare earth element R has a good balance between the saturation magnetization Is, the Curie temperature Tc, and the anisotropic magnetic field Ha.
  • the resource amount of Nd—Fe—B permanent magnets is large. Therefore, Nd—Fe—B permanent magnets are widely used in consumer equipment, industrial equipment, transportation equipment, and the like.
  • the RTB permanent magnet described in Patent Document 1 has a grain boundary phase containing Ce. This grain boundary phase is formed by a two-alloy method.
  • the present invention has been made in view of the above circumstances, and among permanent magnets containing Ce as a substitute element for Nd, a permanent magnet having both a high coercive force and a high squareness ratio, and a rotating machine including the permanent magnet are provided.
  • the purpose is to provide.
  • a permanent magnet according to one aspect of the present invention is a permanent magnet containing a rare earth element R, a transition metal element T, and boron B, and the rare earth element R contains at least Nd, Y, and Ce, and the transition metal element T Includes at least Fe, the total content of rare earth elements R in the permanent magnet is [R] atomic%, and the total content of the transition metal elements T in the permanent magnet is [T] atomic%.
  • the content of B in [B] is [B] atomic%
  • the content of Y in the permanent magnet is [Y] atomic%
  • the content of Ce in the permanent magnet is [Ce] atomic%
  • [Y] / [R] is 0.05 to 0.25
  • [Ce] / [R] is 0.10 to 0.55
  • [T] / [B] is 14 to 18.
  • the C content in the permanent magnet may be 0.00 to 0.25% by mass
  • the N content in the permanent magnet is 0.00 to 0.25% by mass
  • the content of O in the permanent magnet may be 0.00 to 0.25% by mass.
  • a rotating machine includes the permanent magnet.
  • a permanent magnet having a high coercive force and a high squareness ratio among permanent magnets containing Ce as an alternative element of Nd, and a rotating machine including the permanent magnet are provided.
  • FIG. 10 is a schematic diagram of a cross section 10cs of FIG.
  • FIG. 2 is an enlarged view of a part II of the cross section 10cs of the permanent magnet 10 shown in FIG.
  • FIG. 3 is a schematic perspective view of a rotating machine according to an embodiment of the present invention.
  • FIG. 4 is a diagram showing the relationship between [T] / [B] and HcJ in Experiment Group 1.
  • FIG. 5 is a diagram illustrating the relationship between [T] / [B] and the squareness ratio of the experimental group 1.
  • FIG. 6 is a diagram showing the relationship between [Y] / [R] and HcJ for each of the experimental groups 2-1 to 2-4.
  • FIG. 7 is a diagram showing the relationship between [Y] / [R] and the squareness ratio of each of the experimental groups 2-1 to 2-4.
  • FIG. 8 is a diagram showing the relationship between [Ce] / [R] and HcJ in the experimental group 3.
  • FIG. 9 is a diagram showing the relationship between [Ce] / [R] and the squareness ratio in the experimental group 3.
  • FIG. 10 is a diagram showing the relationship between [Y] / [R] and HcJ for each of the experimental groups 4-1 and 4-2.
  • FIG. 11 is a diagram showing the relationship between [Y] / [R] and the squareness ratio of each of the experimental groups 4-1 and 4-2.
  • the permanent magnet according to the present invention may be a sintered magnet or a hot-worked magnet.
  • the permanent magnet according to the present invention may be a rare earth magnet.
  • the whole permanent magnet 10 according to the present embodiment is shown in (a) of FIG.
  • a cross section 10cs of the permanent magnet 10 is shown in FIG.
  • FIG. 2 is an enlarged view of a part II of the cross section 10 cs of the permanent magnet 10.
  • the permanent magnet 10 may include a plurality of main phase particles 11 (main phase) and a grain boundary phase 9 located between the plurality of main phase particles 11.
  • the permanent magnet 10 may be a sintered body composed of a large number of main phase particles 11 via the grain boundary phase 9.
  • the permanent magnet 10 contains a rare earth element R, a transition metal element T, and boron B.
  • the main phase particle 11 may contain a rare earth element R, a transition metal element T, and B.
  • the rare earth element R contains at least Nd (neodymium), Y (yttrium), and Ce (cerium).
  • the transition metal element T contains at least Fe (iron).
  • the total content of rare earth elements R in the permanent magnet 10 is expressed as [R] atomic%.
  • the total content of the transition metal element T in the permanent magnet 10 is expressed as [T] atomic%.
  • the B content in the permanent magnet 10 is expressed as [B] atomic%.
  • the Y content in the permanent magnet 10 is expressed as [Y] atomic%.
  • the Ce content in the permanent magnet 10 is expressed as [Ce] atomic%.
  • [Y] / [R] is 0.05 to 0.25.
  • [Ce] / [R] is 0.10 to 0.55.
  • the present inventors examined a method for increasing the coercive force of a permanent magnet in which a part of the rare earth element R is replaced with Ce.
  • the main phase particles in the permanent magnet are, for example, tetragonal R 2 T 14 B compounds.
  • the stoichiometric ratio of T to B in R 2 T 14 B is 14.
  • the present inventors have found that a high coercive force can be obtained when [T] / [B] is 14 or more and 18 or less, which is the stoichiometric ratio.
  • the squareness ratio of the permanent magnet is likely to be lowered only when [T] / [B] is within the above range.
  • the R 2 T 17 phase is likely to be precipitated in the grain boundary phase, so that the squareness ratio of the permanent magnet is likely to be lowered.
  • the R 2 T 17 phase can be modified into the main phase by performing liquid phase sintering at a sufficiently high temperature.
  • the liquidus temperature of the main phase is lowered, so that the main phase becomes coarse due to abnormal grain growth even when the temperature of the liquid phase sintering is relatively low. Magnetic properties such as magnetic force are reduced.
  • [Y] / [R] is 0.05 to 0.25, and a part of R in the main phase is replaced with Y, so that the liquidus temperature of the main phase increases, The coarsening of the phase particles 11 is suppressed, and liquid phase sintering becomes possible at a relatively high temperature. As a result, the R 2 T 17 phase can be reformed to the main phase, and the squareness ratio of the permanent magnet 10 is increased.
  • [Ce] / [R] is 0.10 to 0.55, and the substitution amount of Ce in the main phase is not too large, so that the liquidus temperature of the main phase is unlikely to decrease.
  • the sintering can be performed at a sufficiently high temperature to modify the R 2 T 17 phase, the squareness ratio of the permanent magnet 10 is unlikely to decrease. From the above, even if a part of the rare earth element R is replaced with Ce, both a high coercive force and a high squareness ratio can be achieved.
  • the reason why the permanent magnet 10 has a high coercive force and a high squareness ratio is not limited to the above reason.
  • the rare earth element R may further contain other rare earth elements in addition to Nd, Y, and Ce.
  • Other rare earth elements include, for example, Sc (scandium), La (lanthanum), Pr (praseodymium), Sm (samarium), Eu (europium), Gd (gadolinium), Ho (holmium), Dy (dysprosium) and Tb ( May be at least one selected from the group consisting of terbium).
  • the rare earth element R may consist only of Nd, Y, and Ce.
  • [R] may be 11-18 atomic%.
  • the Nd content [Nd] in the permanent magnet 10 may be 2.2 to 14.4 atomic%.
  • [Y] may be 0.55 to 4.5 atomic%.
  • [Ce] may be 1.1 to 9.9 atomic%.
  • the transition metal element T may further contain Co (cobalt) in addition to Fe, and may further contain other transition metal elements.
  • the other transition metal element may be, for example, Ni (nickel).
  • the transition metal element T may consist only of Fe and Co. [T] may be 76.5 to 84.3 atomic%.
  • the Fe content [Fe] in the permanent magnet 10 may be 71.5 to 84.3 atomic%.
  • the Co content [Co] in the permanent magnet 10 may be 0 to 5 atomic%.
  • [B] may be 4.32 to 5.93 atomic%, or 4.65 to 5.41 atomic%.
  • [Y] / [R] may be 0.05 to 0.25, or 0.05 to 0.15. When [Y] / [R] is within the above range, the squareness ratio of the permanent magnet 10 tends to be high.
  • [Ce] / [R] may be 0.10 to 0.55, or 0.1 to 0.4.
  • [Ce] / [R] is within the above range, even if R in the main phase is replaced with Ce, the coercive force of the permanent magnet 10 is hardly reduced.
  • [T] / [B] may be 14.0 to 18.0, or 15.5 to 18.0.
  • [T] / [B] is within the above range, the coercive force of the permanent magnet 10 tends to be high.
  • the permanent magnet 10 includes Cu (copper), Al (aluminum), Mn (manganese), Nb (niobium), Ta (tantalum), Zr (zirconium), Ti (titanium), W (tungsten), Mo (molybdenum), You may further contain elements, such as V (vanadium), Ag (silver), Ge (germanium), Zn (zinc), Ga (gallium), Si (silicon), Sn (tin), and Bi (bismuth).
  • the C (carbon) content in the permanent magnet 10 may be 0.00 to 0.25% by mass, or 0.00 to 0.10% by mass.
  • the content of N (nitrogen) in the permanent magnet 10 may be 0.00 to 0.25% by mass, or 0.00 to 0.10% by mass.
  • the content of O (oxygen) in the permanent magnet 10 may be 0.00 to 0.25% by mass, or 0.00 to 0.10% by mass.
  • the Y-OCN phase may include at least one selected from the group consisting of yttrium oxide, yttrium carbide, and yttrium nitride, for example.
  • the composition of the permanent magnet 10 is X-ray fluorescence analysis, ICP (Inductively Coupled Plasma) emission analysis, inert gas melting-non-dispersive infrared absorption method, combustion in oxygen stream-infrared absorption method, inert gas melting- It may be specified by a thermal conductivity method or the like.
  • Each main phase particle 11 may include at least a rare earth element R, a transition metal element T, and boron (B).
  • the rare earth element R contains at least Nd (neodymium), Y (yttrium), and Ce (cerium). That is, a part of Nd is substituted with Y and Ce.
  • the transition metal element T contains at least Fe (iron).
  • the transition metal element T may contain Fe and Co (cobalt). That is, a part of the Fe may be replaced with Co.
  • Each main phase particle 11 may contain carbon (C) in addition to boron (B). That is, a part of the above B may be replaced with C.
  • the main phase particle 11 may contain R 2 T 14 M as a main phase.
  • the element M may be only B.
  • the element M may be B and C.
  • R 2 T 14 M may be represented as Nd 2 -xy Y x Ce y Fe 14 -s Co s B 1 -t C t .
  • x + y is greater than 0 and less than 2.
  • x is greater than 0 and less than 2.
  • y is greater than 0 and less than 2.
  • s is 0 or more and less than 14.
  • t is 0 or more and less than 1.
  • the main phase particles 11 may contain Nd 2 Fe 14 B.
  • the main phase particles 11 may include Y 2 Fe 14 B.
  • the main phase particles 11 may include Ce 2 Fe 14 B.
  • the grain boundary phase 9 may include an RT phase 3 containing an intermetallic compound of a rare earth element R and a transition metal element T.
  • the grain boundary phase 9 may include an R-rich phase 5, a heterogeneous phase 7, an R 6 T 13 E phase, and the like.
  • the element E may be at least one selected from the group consisting of Ga, Si, Sn, and Bi.
  • the definitions of RT phase 3, R rich phase 5, heterogeneous phase 7, and R 6 T 13 E phase may be as follows.
  • the content of C in the RT phase 3 is expressed as [C] L atomic%.
  • the N content in the RT phase 3 is expressed as [N] L atomic%.
  • the content of O in the RT phase 3 is expressed as [O] L atomic%.
  • the total content of rare earth elements R in the RT phase 3 is expressed as [R] L atomic%.
  • the total content of the transition metal element T in the RT phase 3 is expressed as [T] L atomic%.
  • the total content of the element E in the RT phase 3 is expressed as [E] L atomic%.
  • the RT phase 3 may be a phase that satisfies all of the following inequalities (1), (2), and (3).
  • the RT phase 3 may include, for example, an RT 2 phase. That is, the intermetallic compound contained in the RT phase 3 may be, for example, RT 2.
  • RT 2 may be represented as Nd 1- ⁇ Ce ⁇ Fe 2- ⁇ Co ⁇ . ⁇ is 0 or more and 1 or less. ⁇ is 0 or more and 2 or less.
  • RT 2 may be, for example, NdFe 2 or CeFe 2 .
  • the RT phase 3 may be a Laves phase.
  • the crystal structure of RT phase 3 may be C15 type.
  • the RT phase 3 may be specified based on the diffraction angle 2 ⁇ of the diffraction peak derived from the lattice plane (hkl) using an X-ray diffraction (XRD) pattern.
  • XRD X-ray diffraction
  • 2 ⁇ derived from the lattice plane (220) of the RT phase 3 may be 34.0 to 34.73 °.
  • 2 ⁇ derived from the lattice plane (311) of the RT phase 3 may be 40.10 to 40.97 °.
  • the 2 ⁇ may vary within the above range depending on the type of rare earth element R contained in the RT phase 3.
  • the content of C in the R-rich phase 5 is expressed as [C] R atomic%.
  • the N content in the R-rich phase 5 is expressed as [N] R atomic%.
  • the content of O in the R-rich phase 5 is expressed as [O] R atomic%.
  • the total content of rare earth elements R in the R-rich phase 5 is expressed as [R] R atomic%.
  • the total content of the transition metal element T in the R-rich phase 5 is expressed as [T] R atomic%.
  • the R-rich phase 5 may be a phase that satisfies the following inequalities (4) and (5). 0 ⁇ [C] R + [N] R + [O] R ⁇ 30 (4) 0.50 ⁇ [R] R / ([R] R + [T] R ) ⁇ 1.00 (5)
  • the content of C in the heterogeneous phase 7 is expressed as [C] D atomic%.
  • the N content in the different phase 7 is expressed as [N] D atomic%.
  • the content of O in the heterogeneous phase 7 is expressed as [O] D atomic%.
  • the hetero phase 7 may be a phase in which the sum of [C] D , [N] D, and [O] D [C] D + [N] D + [O] D is 30 or more and less than 100. That is, the different phase 7 may be a phase satisfying the following inequality (6).
  • the hetero phase 7 may include, for example, at least one selected from the group consisting of an oxide of R, a carbide of R, and a nitride of R. 30 ⁇ [C] D + [N] D + [O] D ⁇ 100 (6)
  • the content of C in the R 6 T 13 E phase is expressed as [C] A atomic%.
  • the content of N in the R 6 T 13 E phase is expressed as [N] A atomic%.
  • the content of O in the R 6 T 13 E phase is expressed as [O] A atomic%.
  • the total content of rare earth elements R in the R 6 T 13 E phase is expressed as [R] A atomic%.
  • the total content of the transition metal element T in the R 6 T 13 E phase is expressed as [T] A atomic%.
  • the total content of the element E in the R 6 T 13 E phase is expressed as [E] A atomic%.
  • the R 6 T 13 E phase may be a phase that satisfies all of the following inequalities (7), (8), and (9).
  • the manufacturing method of the permanent magnet 10 may be as follows.
  • the starting materials are weighed to match the desired permanent magnet 10 composition.
  • the starting material can be, for example, a metal, an alloy or an oxide.
  • a reduction process for removing oxygen may be performed at any point in the manufacturing process of the permanent magnet 10.
  • the raw material alloy may be produced from the above starting materials by the following strip casting method, high frequency induction melting method, arc melting method, and other melting methods.
  • a raw material alloy may be produced from a starting material by a reduction diffusion method.
  • a melting method such as a strip casting method may be performed in a non-oxidizing atmosphere.
  • the non-oxidizing atmosphere may be, for example, a vacuum or an inert gas such as Ar (argon).
  • the starting material is melted in a non-oxidizing atmosphere to produce a molten metal (melting material alloy).
  • the molten metal is poured onto the surface of a rotating roll in a non-oxidizing atmosphere. Since the metal roll is cooled by water cooling or the like, the molten metal is rapidly cooled on the surface of the roll and solidifies. By crushing the alloy peeled from the roll, a raw material alloy in the form of a thin plate or flakes (scales) is obtained.
  • the roll may be made of copper, for example.
  • the raw material alloy may be pulverized by, for example, hydrogen pulverization.
  • hydrogen pulverization the raw material alloy is placed in a hydrogen atmosphere, and the raw material alloy is made to store hydrogen.
  • the raw material alloy occludes hydrogen, the volume of the raw material alloy expands.
  • the hydrogenation reaction of the metal contained in the raw material alloy occurs, and the raw material alloy becomes brittle.
  • cracks occur in the raw material alloy, and the raw material alloy is pulverized.
  • the particle size of the coarse powder may be, for example, 10 to 1000 ⁇ m.
  • the coarse powder may be dehydrogenated by heating the coarse powder.
  • the dehydrogenation temperature may be 300-400 ° C.
  • the dehydrogenation time may be 0.5 to 20 hours.
  • a lubricant may be added to the coarse powder.
  • the lubricant may be, for example, an ester organic material or an amide organic material.
  • the amide-based organic substance may be, for example, oleic acid amide.
  • the coarse powder may be pulverized by an airflow pulverizer (jet mill) or the like.
  • fine powder is accelerated by an inert gas stream and then pulverized by colliding with a hard ceramic plate.
  • the obtained fine powder is recovered from the particle collecting part (cyclone) of the jet mill.
  • the inert gas may be nitrogen gas, argon gas or the like.
  • the particle size of the fine powder may be, for example, 0.5 to 10 ⁇ m.
  • the pressing direction may be a direction perpendicular to the magnetic field direction.
  • the strength of the magnetic field may be, for example, 960-1600 kA / m.
  • the pressure applied to the fine powder may be, for example, 10 to 500 MPa.
  • the sintering temperature may be 1000 to 1200 ° C., for example.
  • the sintering time may be, for example, 0.1 to 100 hours.
  • the green body may be sintered in a reduced pressure atmosphere, an inert atmosphere, or the like.
  • the permanent magnet 10 is obtained by subjecting the sintered body to an aging treatment.
  • the aging treatment the sintered body is heated.
  • the temperature of the aging treatment may be 450 to 950 ° C., for example.
  • the time for aging treatment may be, for example, 0.1 to 100 hours.
  • the aging treatment may be performed in a reduced pressure atmosphere, an inert atmosphere, or the like. By performing the aging treatment, the coercive force of the permanent magnet 10 tends to be higher.
  • the aging treatment may be composed of a one-stage heat treatment process or may be composed of two or more heat treatment processes. For example, after heating at a relatively high temperature, it may be heated at a relatively low temperature. In this case, the coercive force of the permanent magnet 10 tends to be higher.
  • the obtained permanent magnet 10 may be processed into a predetermined shape.
  • the processing method may be, for example, shape processing such as cutting and grinding, or chamfering processing such as barrel polishing.
  • shape processing such as cutting and grinding
  • chamfering processing such as barrel polishing.
  • the surface of the permanent magnet 10 serving as a measurement sample may be processed flat. Due to the flat surface, the exact dimensions of the measurement sample can be obtained.
  • the method for processing the surface to be flat may be, for example, a wet method, a dry method, or the like. The wet method is preferable because the processing time is short and the processing cost is low.
  • a protective layer may be formed on the surface of the sintered body.
  • the protective layer may be, for example, a resin layer or an inorganic layer (for example, a metal layer or an oxide layer).
  • the method for forming the protective layer may be, for example, a plating method, a coating method, a vapor deposition polymerization method, a gas phase method, or a chemical conversion treatment method.
  • the rotating machine according to the present embodiment includes the permanent magnet 10a.
  • An example of the internal structure of the rotating machine is shown in FIG.
  • the rotating machine 200 according to the present embodiment is a permanent magnet synchronous rotating machine (SPM rotating machine).
  • the rotating machine 200 includes a cylindrical rotor 50 and a stator 30 disposed inside the rotor 50.
  • the rotor 50 includes a cylindrical core 52 and a plurality of permanent magnets 10 a arranged along the inner peripheral surface of the core 52.
  • the plurality of permanent magnets 10 a are arranged so that N poles and S poles are alternately arranged along the inner peripheral surface of the core 52.
  • the stator 30 has a plurality of coils 32 provided along the outer peripheral surface thereof.
  • the coil 32 and the permanent magnet 10a are arranged so as to face each other.
  • the rotating machine 200 may be an electric motor.
  • the electric motor converts electrical energy into mechanical energy by the interaction between the field generated by the electromagnet generated by energizing the coil 32 and the field generated by the permanent magnet 10a.
  • the rotating machine 200 may be a generator.
  • the generator converts mechanical energy into electrical energy by the interaction (electromagnetic induction) between the field and the coil 32 by the permanent magnet 10a.
  • the rotating machine 200 that functions as an electric motor may be, for example, a permanent magnet DC motor, a linear synchronous motor, a permanent magnet synchronous motor (SPM motor, IPM motor), or a reciprocating motor.
  • the motor that functions as the reciprocating motor may be, for example, a voice coil motor or a vibration motor.
  • the rotating machine 200 that functions as a generator may be, for example, a permanent magnet synchronous generator, a permanent magnet commutator generator, or a permanent magnet AC generator.
  • the rotating machine 200 may be used for automobiles, industrial machines, household appliances, and the like.
  • the permanent magnet according to the present invention may be manufactured by a hot working method, a film forming method, a spark plasma sintering method, or the like.
  • Example 1 A permanent magnet was produced by the method described below. Nd, Y, Ce, Fe, FeB, Co, Cu, and Al were prepared as starting materials (single or alloy) for the permanent magnet. The purity of each starting material was 99.9% by mass. The composition of the permanent magnet is 13.60 atomic% Nd-0.80 atomic% Y-1.60 atomic% Ce-7.62 atomic% Fe-0.50 atomic% Co-5.58 atomic% B-0.20. Each starting material was weighed and mixed so as to be atomic% Al-0.10 atomic% Cu to prepare a mixed raw material. An alloy flake was obtained by quenching and crushing the melt of the mixed raw material on the surface of the roll by the strip casting method.
  • the flakes were pulverized by hydrogen pulverization to obtain a coarse powder.
  • the coarse powder was dehydrogenated.
  • the dehydrogenation temperature was 300 ° C.
  • the dehydrogenation time was 5 hours.
  • Lubricant was added to the coarse powder after dehydrogenation.
  • the lubricant was oleic amide.
  • the content of the lubricant in the coarse powder was 0.1% by mass.
  • the coarse powder to which the lubricant was added was pulverized by a jet mill in a high-pressure argon gas atmosphere to obtain a fine powder.
  • the fine powder was put into a molding space (cavity) in the molding machine.
  • a fine powder was pressed in a magnetic field and molded to obtain a molded body.
  • the pressing direction was a direction perpendicular to the magnetic field direction.
  • the strength of the magnetic field was 15 ⁇ (10 3 / 4 ⁇ ) kA / m.
  • the pressure applied to the fine powder was 140 MPa.
  • the sintered body was sintered to obtain a sintered body.
  • the sintering temperature was 1030 ° C.
  • the sintering time was 6 hours.
  • the sintered body was processed into a rectangular parallelepiped shape by inner peripheral cutting.
  • the volume and weight of the sintered body after processing were measured, and the relative density was calculated.
  • the relative density of the sintered body was 99.0% or more.
  • the fracture surface of the sintered body was observed with an optical microscope. As a result, coarse particles were not confirmed. From the observation of the relative density of the sintered body and the cross-sectional structure of the sintered body, it was confirmed that the molded body could be sintered under an appropriate temperature condition.
  • the sintered body was subjected to an aging treatment to obtain the permanent magnet of Example 1.
  • the temperature of the aging treatment was 700 ° C.
  • the time for aging treatment was 1 hour.
  • the content (unit: mass%) of O in the permanent magnet of Example 1 was measured by an inert gas melting-non-dispersive infrared absorption method.
  • the C content (unit: mass%) in the permanent magnet of Example 1 was measured by combustion in an oxygen stream-infrared absorption method.
  • the N content (unit: mass%) in the permanent magnet of Example 1 was measured by an inert gas melting-thermal conductivity method. Table 2 shows the results.
  • the coercive force HcJ (unit: kA / m) of the permanent magnet of Example 1 was measured using a BH tracer. Further, the external magnetic field Hk applied to the permanent magnet when the magnetic flux density of 90% of the residual magnetic flux density Br was obtained was obtained.
  • the squareness ratio 100 ⁇ Hk / HcJ (unit:%) of the permanent magnet of Example 1 was determined from HcJ and Hk. Table 2 shows the HcJ and the squareness ratio of Example 1.
  • the unit (kOe) of the coercive force HcJ in the following table is equivalent to “ ⁇ (10 3 / 4 ⁇ ) ⁇ (kA / m)”.
  • HcJ is preferably 12 ⁇ (10 3 / 4 ⁇ ) kA / m or more.
  • the squareness ratio is preferably 85% or more, and more preferably 90% or more.
  • Examples 2 to 9, Comparative Examples 1 to 24, Reference Example 1 Each starting material of Examples 2 to 9, Comparative Examples 1 to 24 and Reference Example 1 was weighed so that the composition of the permanent magnet was as shown in Tables 1 to 5. According to the following procedure, appropriately sintered sintered bodies (the sintered bodies of Examples 2 to 9, Comparative Examples 1 to 24, and Reference Example 1) were obtained. A plurality of molded bodies were individually produced by the same method as in Example 1. A plurality of sintered bodies were individually manufactured by changing the sintering temperature from 950 ° C. to 1100 ° C. in increments of 10 ° C. The relative density of each sintered body was measured by the same method as in Example 1, and the cross-sectional structure of each sintered body was observed. A sintered body in which the relative density of the sintered body was 99.0% or more and coarse particles were not confirmed on the fracture surface of the sintered body was determined to be an appropriately sintered sintered body.
  • compositions of the permanent magnets of Examples 2 to 9, Comparative Examples 1 to 24, and Reference Example 1 were analyzed in the same manner as in Example 1. The results are shown in Tables 1-5.
  • Example 10 to 15 In Examples 10 and 11, the contents of C, N, and O in the permanent magnet were adjusted to the values shown in Table 5 by adjusting the amount of oleic amide added to the coarse powder. Except for this point, the permanent magnets of Examples 10 and 11 were individually manufactured by the same method as in Example 4. When obtaining the fine powders of Examples 12 and 13, the contents of C, N and O in the permanent magnet were adjusted to the values shown in Table 5 by using a mixed gas of argon and nitrogen instead of argon gas. did. Except for this point, permanent magnets of Examples 12 and 13 were individually produced by the same method as in Example 4.
  • compositions of the permanent magnets of Examples 10 to 15 were analyzed in the same manner as in Example 1. The results are shown in Table 5.
  • FIG. 4 shows the relationship between [T] / [B] and HcJ in the experimental group 1 shown in Table 1.
  • FIG. 5 shows the relationship between [T] / [B] and the squareness ratio in Experimental Group 1.
  • [T] / [B] of the experimental group 2-1 shown in Table 2 is 14.
  • [T] / [B] in the experimental group 2-2 is 18.
  • [T] / [B] is 12 in the experimental group 2-3.
  • [T] / [B] in the experimental group 2-4 is 20.
  • FIG. 6 shows the relationship between [Y] / [R] and HcJ in each of the experimental groups 2-1 to 2-4.
  • FIG. 7 shows the relationship between [Y] / [R] and the squareness ratio in each of the experimental groups 2-1 to 2-4.
  • FIG. 8 shows the relationship between [Ce] / [R] and HcJ in the experimental group 3 shown in Table 3.
  • FIG. 9 shows the relationship between [Ce] / [R] and the squareness ratio in Experimental Group 3.
  • [Ce] / [R] of the experimental group 4-1 shown in Table 4 is 0.55.
  • [Ce] / [R] is 0.65.
  • FIG. 10 shows the relationship between [Y] / [R] and HcJ in each of the experimental groups 4-1 and 4-2.
  • FIG. 11 shows the relationship between [Y] / [R] and the squareness ratio in each of the experimental groups 4-1 and 4-2.
  • the C content, the N content, or the O content in the permanent magnets are different from each other.
  • HcJ of all examples was 12 kOe or more, and the squareness ratio of all examples was 85% or more.
  • the permanent magnet of Comparative Example 4 had a low liquidus temperature of the main phase and could not perform liquid phase sintering at a sufficiently high temperature. Therefore, the R 2 T 17 phase was used as the main phase. It is considered that the squareness ratio was lowered due to the inability to modify. In the permanent magnet of Comparative Example 7, the amount of substitution of Y in the main phase increased, and the anisotropy magnetic field Ha of the main phase decreased.
  • the permanent magnet of Reference Example 1 had a coercive force of 12 kOe or more and a squareness ratio of 85% or more.
  • the squareness ratio did not decrease even when part of the rare earth element R was replaced with Ce.
  • the Ce content in the permanent magnet since the Ce content in the permanent magnet is small, there is almost no effect of making the permanent magnet inexpensive.
  • the permanent magnets each Comparative Example 4, and 16-19 the main phase of the liquid phase temperature is low, because it could not implement the liquid-phase sintering at a sufficiently high temperature, the R 2 T 17 phase It is considered that the squareness ratio was lowered because the main phase could not be modified.
  • the permanent magnet of Comparative Example 4 had a low liquidus temperature of the main phase and could not perform liquid phase sintering at a sufficiently high temperature, so the R 2 T 17 phase was the main phase. It is considered that the squareness ratio was lowered due to the inability to modify.
  • the amount of substitution of Y in the main phase was increased, and the anisotropic magnetic field Ha of the main phase was decreased.
  • the permanent magnet according to the present invention is used, for example, in a rotating machine.

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Abstract

L'invention concerne un aimant permanent ayant une force coercitive élevée et un taux de rectangularité élevé parmi des aimants permanents comprenant Ce en tant qu'élément alternatif pour Nd, et une machine rotative comprenant l'aimant permanent. L'aimant permanent contient un élément de terre rare R, un élément de métal de transition T et du bore B, l'élément de terre rare R comprenant au moins Nd, Y et Ce; l'élément de métal de transition T comprend au moins Fe; une teneur totale de l'élément de terre rare R dans l'aimant permanent est [R] en %; une teneur totale de l'élément de métal de transition T dans l'aimant permanent est [T] en %; la teneur en B dans l'aimant permanent est [B] en %; la teneur en Y dans l'aimant permanent est [Y] en %; la teneur en Ce dans l'aimant permanent est [Ce] en %; [Y]/ [R] est de 0,05 à 0,25; [Ce]/ [R] est de 0,10 à 0,55; et [T]/ [B] est de 14 à 18.
PCT/JP2018/012997 2017-03-30 2018-03-28 Aimant permanent et machine rotative WO2018181592A1 (fr)

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CN110853856A (zh) * 2019-11-22 2020-02-28 安泰科技股份有限公司 一种高矫顽力含铈磁体及其制备方法
CN113782292A (zh) * 2021-06-04 2021-12-10 钢铁研究总院 一种具有改进温度稳定性的钇铈基稀土永磁材料
CN115249558A (zh) * 2022-07-20 2022-10-28 钢铁研究总院有限公司 一种含铈稀土永磁体
JP7535837B2 (ja) 2022-08-30 2024-08-19 煙台東星磁性材料株式有限公司 Ｃｅ添加型ＲＥ－Ｔ－Ｂ－Ｍ系焼結磁性体

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WO2022123992A1 (fr) * 2020-12-09 2022-06-16 Tdk株式会社 Aimant permanent à base de r-t-b

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WO2014148076A1 (fr) * 2013-03-22 2014-09-25 Tdk株式会社 Aimant permanent de type r-t-b
JP2015192043A (ja) * 2014-03-28 2015-11-02 Tdk株式会社 Ｒ−ｔ−ｂ系永久磁石
JP2015204390A (ja) * 2014-04-15 2015-11-16 Tdk株式会社 永久磁石およびモータ
JP2015207663A (ja) * 2014-04-21 2015-11-19 Tdk株式会社 Ｒ−ｔ−ｂ系永久磁石、ｒ−ｔ−ｂ系永久磁石用原料合金

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JP2014027268A (ja) * 2012-06-22 2014-02-06 Tdk Corp 焼結磁石
WO2014148076A1 (fr) * 2013-03-22 2014-09-25 Tdk株式会社 Aimant permanent de type r-t-b
JP2015192043A (ja) * 2014-03-28 2015-11-02 Tdk株式会社 Ｒ−ｔ−ｂ系永久磁石
JP2015204390A (ja) * 2014-04-15 2015-11-16 Tdk株式会社 永久磁石およびモータ
JP2015207663A (ja) * 2014-04-21 2015-11-19 Tdk株式会社 Ｒ−ｔ−ｂ系永久磁石、ｒ−ｔ−ｂ系永久磁石用原料合金

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Publication number Priority date Publication date Assignee Title
CN110853856A (zh) * 2019-11-22 2020-02-28 安泰科技股份有限公司 一种高矫顽力含铈磁体及其制备方法
CN110853856B (zh) * 2019-11-22 2021-07-13 安泰科技股份有限公司 一种高矫顽力含铈磁体及其制备方法
CN113782292A (zh) * 2021-06-04 2021-12-10 钢铁研究总院 一种具有改进温度稳定性的钇铈基稀土永磁材料
CN113782292B (zh) * 2021-06-04 2022-06-10 钢铁研究总院 一种具有改进温度稳定性的钇铈基稀土永磁材料
CN115249558A (zh) * 2022-07-20 2022-10-28 钢铁研究总院有限公司 一种含铈稀土永磁体
CN115249558B (zh) * 2022-07-20 2025-04-08 钢铁研究总院有限公司 一种含铈稀土永磁体
JP7535837B2 (ja) 2022-08-30 2024-08-19 煙台東星磁性材料株式有限公司 Ｃｅ添加型ＲＥ－Ｔ－Ｂ－Ｍ系焼結磁性体

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