WO2009145229A1 - Aimant permanent et son procédé de fabrication, aimant permanent pour moteur et moteur à aimants permanents - Google Patents

Aimant permanent et son procédé de fabrication, aimant permanent pour moteur et moteur à aimants permanents Download PDF

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Publication number
WO2009145229A1
WO2009145229A1 PCT/JP2009/059713 JP2009059713W WO2009145229A1 WO 2009145229 A1 WO2009145229 A1 WO 2009145229A1 JP 2009059713 W JP2009059713 W JP 2009059713W WO 2009145229 A1 WO2009145229 A1 WO 2009145229A1
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Prior art keywords
permanent magnet
koe
rare earth
phase
coercive force
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PCT/JP2009/059713
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English (en)
Japanese (ja)
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孝雄 沢
勝彦 山田
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株式会社 東芝
東芝マテリアル株式会社
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Application filed by 株式会社 東芝, 東芝マテリアル株式会社 filed Critical 株式会社 東芝
Priority to JP2010514515A priority Critical patent/JP4764526B2/ja
Priority to CN2009801209524A priority patent/CN102047536B/zh
Publication of WO2009145229A1 publication Critical patent/WO2009145229A1/fr

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    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K1/00—Details of the magnetic circuit
    • H02K1/02—Details of the magnetic circuit characterised by the magnetic material
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
    • H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
    • H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
    • H01F41/0266—Moulding; Pressing
    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K1/00—Details of the magnetic circuit
    • H02K1/06—Details of the magnetic circuit characterised by the shape, form or construction
    • H02K1/22—Rotating parts of the magnetic circuit
    • H02K1/27—Rotor cores with permanent magnets
    • H02K1/2706—Inner rotors
    • H02K1/272—Inner rotors the magnetisation axis of the magnets being perpendicular to the rotor axis
    • H02K1/274—Inner rotors the magnetisation axis of the magnets being perpendicular to the rotor axis the rotor consisting of two or more circumferentially positioned magnets
    • H02K1/2753—Inner rotors the magnetisation axis of the magnets being perpendicular to the rotor axis the rotor consisting of two or more circumferentially positioned magnets the rotor consisting of magnets or groups of magnets arranged with alternating polarity
    • H02K1/276—Magnets embedded in the magnetic core, e.g. interior permanent magnets [IPM]
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
    • H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
    • H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
    • H01F41/0273—Imparting anisotropy
    • H01F41/028—Radial anisotropy

Definitions

  • the present invention relates to a permanent magnet, particularly a permanent magnet having a low coercive force and a high squareness ratio suitable for motors, and a method for manufacturing the same. Furthermore, the present invention relates to a permanent magnet motor using these magnets.
  • alnico magnets ferrite magnets, Sm—Co magnets, Nd—Fe—B magnets and the like are known as permanent magnets.
  • permanent magnets appropriate magnets according to the specifications are used for key parts of various electric devices in addition to various motors such as VCM, spindle motor, measuring instrument, speaker, medical MRI and the like.
  • magnets contain a large amount of Fe or Co and rare earth elements.
  • Fe and Co contribute to an increase in saturation magnetic flux density.
  • rare earth elements bring about a very large magnetic anisotropy derived from the behavior of 4f electrons in the crystal field, thereby contributing to an increase in coercive force and realizing good magnet characteristics.
  • motors are especially attracting attention from the viewpoint of energy saving.
  • the loss can be greatly reduced compared to the conventional induction type, and therefore, it is spreading as an energy saving technology for various uses such as in-vehicle and home appliance applications.
  • a surface magnet type permanent magnet motor in which a permanent magnet is attached to the outer periphery of a rotor core
  • an embedded type permanent magnet motor in which a permanent magnet is embedded in the rotor core.
  • An embedded permanent magnet motor is suitable for the variable speed drive motor.
  • FIG. 1 11 is a rotor, 12 is a rotor core, and 14 is a high coercivity permanent magnet.
  • a rectangular cavity is provided in the outer peripheral portion of the rotor core 12 by the same number as the number of poles.
  • the rotor 11 shown in FIG. 1 is a four-pole rotor 11.
  • the rotor core 12 is provided with four cavities, and permanent magnets 14 are inserted into the cavities.
  • the permanent magnet 14 is magnetized in the direction perpendicular to the radial direction of the rotor or the side (long side in FIG. 1) facing the air gap surface in the rectangle of the cross section of the permanent magnet 14.
  • the permanent magnet 14 is mainly an NdFeB permanent magnet having a high coercive force so as not to be demagnetized by a load current.
  • the rotor core 12 is formed by laminating electromagnetic steel plates punched out of cavities.
  • An example of such a motor is a permanent magnet type reluctance type rotating electrical machine described in JP-A-11-136912 (Patent Document 1).
  • the flux linkage of permanent magnets is always generated at a constant rate. For this reason, the induced voltage by a permanent magnet becomes high in proportion to a rotational speed. When driving while changing the magnetization from low speed to high speed, the induced voltage by the permanent magnet becomes extremely high at high speed rotation. As a result, the induced voltage by the permanent magnet is applied to the electronic component of the inverter, and when the voltage exceeds the withstand voltage of the electronic component, the component breaks down. For this reason, it is conceivable to perform a design in which the amount of magnetic flux of the permanent magnet is reduced so as to be equal to or lower than the withstand voltage, but the output and efficiency in the low speed region of the permanent magnet type rotating electrical machine are reduced.
  • the interlinkage magnetic flux of the permanent magnet decreases due to the demagnetizing field of the d-axis current, the decrease of the interlinkage magnetic flux creates a margin of voltage with respect to the upper limit voltage. Since the current can be increased, the output in the high speed region increases. Further, the rotational speed can be increased by the voltage margin, and the range in which the operation can be performed while changing the magnetization is expanded.
  • the demagnetizing field due to the d-axis current generates a harmonic magnetic flux, and the increase in voltage generated by the harmonic magnetic flux or the like is weakened, creating a limit of voltage reduction by the magnetic flux control. Therefore, even if the flux-weakening control is applied to the embedded permanent magnet type rotating electric machine, it is difficult to operate at a variable speed that is three times or more the base speed. Furthermore, the iron loss is increased by the harmonic magnetic flux, and vibration is generated by the electromagnetic force generated by the harmonic magnetic flux.
  • an embedded permanent magnet motor when applied to a hybrid vehicle drive motor, the motor is rotated when driven by the engine alone. At medium / high speed rotation, the induced voltage of the motor's permanent magnet exceeds the power supply voltage, and the d-axis current continues to flow under the flux-weakening control. In this state, since the motor generates only a loss, the overall operation efficiency is deteriorated. The d-axis current continues to flow, leading to a decrease in efficiency.
  • Patent Document 2 Japanese Patent Application Laid-Open No. 2006-280195 (Patent Document 2) enables an operation while changing the magnetization in a wide range from low speed to high speed. Motors that can change the magnetization state of all or part of permanent magnets that can provide higher torque and higher output in the middle / high-speed rotation range, improved efficiency, and improved reliability (permanent magnet type) Rotating electric machines) have been proposed.
  • this permanent magnet type motor includes a stator provided with a stator winding as shown in FIG. 2 (FIG. 1 of Patent Document 2), and a magnetic field generated by a current of the stator winding in a rotor core. And a rotor in which a low coercivity permanent magnet having a coercive force with which the magnetic flux density is irreversibly changed and a high coercivity permanent magnet having a coercivity more than twice that of the low coercivity permanent magnet are provided. Is.
  • a permanent magnet rotating electrical machine that enables variable speed operation in a wide range from low speed to high speed, realizing high torque in the low-speed rotation range, high output in the medium / high-speed rotation range, improved efficiency, and improved reliability.
  • a high coercive force magnet is an NdFeB magnet
  • a low coercive force magnet is an alnico magnet or an FeCrCo magnet.
  • Patent Document 2 shows an Alnico magnet (AlNiCo) or FeCrCo magnet as a low coercivity permanent magnet and an NdFeB magnet as a high coercivity permanent magnet.
  • the coercive force (magnetic field at which the magnetic flux density becomes 0) of the Alnico magnet is 60 to 120 kA / m. It becomes 1/15 to 1/8 with respect to the coercive force of 950 kA / m of the NdFeB magnet.
  • the coercive force of the FeCrCo magnet is about 60 kA / m, which is 1/15 of the coercive force of the NdFeB magnet of 950 kA / m.
  • Alnico magnets and FeCrCo magnets have considerably lower coercivity than NdFeB high coercivity magnets. Using this low coercive force, a motor capable of changing the magnetization state of all or part of permanent magnets is produced.
  • a high coercive force permanent magnet having a coercive force 8 to 15 times that of the low coercive force permanent magnet is applied, thereby obtaining a rotating electrical machine having excellent characteristics.
  • Patent Document 3 discloses a rare earth metal-containing permanent magnet alloy represented by the following general formula as an SmCo-based magnet whose maximum energy product is improved.
  • Patent Document 4 discloses a manufacturing method in which permanent magnet characteristics are improved, that is, a high coercive force ( ⁇ 6.5 kOe) and stabilization.
  • an R 2 M 17- based permanent magnet alloy composed of a rare earth element R and a transition metal element M (where R is one or a combination of two or more of Y, La, Ce, Pr, Nb, Sm and missile metal, M is One or a combination of two or more of Cu and Co, Fe, or Ni and a combination in which a part of M is replaced with one or more of the elements Mn and Zr) are melted and cast.
  • ingot solution treatment is performed at 1100 to 1250 ° C. for 1 to 10 hours to form a R 2 M 17 phase single phase in a metal structure, which is pulverized and compression molded to form a molded body.
  • the compact is sintered in a temperature range of 1100 to 1250 ° C. in a reduced pressure argon gas atmosphere of 50 to 350 Torr. Furthermore, after sintering in a temperature range of 1100 to 1200 ° C., a rare earth cobalt-based permanent magnet is manufactured by performing rapid cooling at 100 ° C./min or more after solution treatment and aging treatment.
  • aging treatment in the case of one stage, 800 ° C. for 4 hours, in the case of multi-stage heat treatment, 800 ° C. for 2 hours, 700 ° C. for 4 hours, 600 ° C. for 8 hours, 500 ° C. for 16 hours It is. Under any condition, a high coercive force ( ⁇ 6.5 kOe) is achieved.
  • Patent Document 5 a Ce-rich rare earth cobalt magnet for the purpose of providing a permanent magnet having high performance (high coercive force) and low cost is temporarily obtained at 400 to 650 ° C. by aging treatment. It is disclosed to include a step that takes 2 hours or more to 300 ° C. after holding. That is, (i) general formula: Ce 1-u Sm u ( Co 1-x-y-w Cu x Fe y M w) z, (M in the formula is at least one of Zr and Ti, 0.
  • Patent Document 6 provides a rare earth cobalt permanent magnet material having a high coercive force and a high energy product, and has the following technique for the purpose of omitting the aging treatment. It is disclosed. That is, an R 2 M 17- based magnet alloy composed of a rare earth element R and a transition metal M (where R is one or a combination of two or more of Y, La, Ce, Pr, Nb, Sm, and misty metal, and M is Cu. A combination of one or more of Co, Fe or Ni and a combination of one or more of the elements of Mn, Ti, Nb, Zr, Ta and Hf with one or more of them Dissolve and cast.
  • the alloy is pulverized and compression molded.
  • a manufacturing method is disclosed in which aging treatment is omitted by sintering the compression-molded body in a vacuum or in an inert atmosphere and then cooling to 800 ° C. or less at a cooling rate of 20 to 500 ° C./min.
  • Patent Document 7 discloses a technique for improving the coercive force. That is, a composition represented by RM 5 comprising a rare earth component R (one or a combination of two or more of Y, Sm, Pr, Nd, Ce, etc.) and a transition metal component M (Co, Fe, Mn, Ni, Cu, etc.).
  • R rare earth component
  • M transition metal component
  • a rare earth magnet characterized in that after the product is sintered, it is gradually cooled to room temperature at a rate of 10 ° C./min or less, further subjected to aging treatment at a temperature near 850 ° C., and then rapidly cooled from the aging treatment temperature to room temperature. It is a manufacturing method.
  • Japanese Patent Laid-Open No. 11-136912 JP 2006-280195 A Japanese Patent Publication No. 2-27426 Japanese Patent Publication No. 1-2970 Japanese Examined Patent Publication No. 62-45686 Japanese Patent Publication No.62-9658 Japanese Patent Publication No. 60-53107
  • An object of the present invention is to provide a permanent magnet suitable for such a setting and particularly suitable for a low coercive force magnet and a method for manufacturing the same.
  • the present invention provides a permanent magnet that is extremely effective for increasing the efficiency of motors of various capacities, such as household appliances such as washing machines and air conditioners, in-vehicle applications, and train applications. Furthermore, it is providing the permanent magnet motor and permanent magnet for motors suitable for the above applications.
  • the permanent magnet of the present invention satisfies the following general formula, and has a coercive force at room temperature of 0.5 kOe or more and 5.0 kOe or less, and a squareness ratio expressed by a ratio of residual magnetization to magnetization in a magnetic field of 10 kOe is 80%. It is the above.
  • the coercive force at room temperature is preferably 0.5 kOe or more and 3.5 kOe or less.
  • the general formula a value is preferably 0.10 ⁇ a ⁇ 0.25, and the b value is 0.04 ⁇ b ⁇ 0.12.
  • the average recoil permeability in the second and third quadrants is preferably 1.00 to 1.08.
  • the permanent magnet is preferably a sintered body. Moreover, it is suitable for the permanent magnet mounted on the motor.
  • the coercive force is 0.5 kOe or more and 5.0 kOe or less
  • the squareness ratio expressed by the ratio of the residual magnetization to the magnetization in a magnetic field of 10 kOe is 80% or more
  • the average recoil permeability 1 in the second and third quadrants is 1.
  • the permanent magnet having 0.001 to 1.08 is suitable for a motor that can change the magnetization state of the whole or part of the permanent magnet.
  • the manufacturing method of the permanent magnet of the present invention includes a molding step of adjusting a molded body by molding an alloy powder satisfying the following general formula in a magnetic field, and the molded body in an inert atmosphere at 1000 ° C. or higher and 1200 ° C. or lower.
  • Sintering step for obtaining a sintered body by sintering and forming a solution at a temperature of 10 minutes to 20 hours, heat-treating the sintered body at a temperature of 600 ° C. to 800 ° C. for 10 minutes to 20 hours, And an aging treatment step of cooling to 500 ° C. at a cooling rate of 1 to 10 ° C./min after the heat treatment.
  • the temperature range of the aging treatment is preferably 600 to 750 ° C. Further, CaCu 5 phase by the aging treatment, Th 2 Zn 17 phase, it is preferable that the phase structure having a 3-phase TbCu 7 phase. Moreover, it is preferable that the squareness ratio represented by the ratio of the residual magnetization to the magnetization in a magnetic field of 10 kOe with a coercive force of the permanent magnet of 0.5 kOe or more and 5.0 kOe or less is 80% or more.
  • the sintering step it is preferable to cool to room temperature or the heat treatment temperature at a cooling rate of 1 to 100 ° C./min.
  • a permanent magnet for a motor according to the present invention is a permanent magnet for a motor used for a motor capable of changing the magnetization state of the whole or a part of the permanent magnet,
  • the coercive force at room temperature is 0.5 kOe or more and 5 kOe or less
  • the squareness ratio expressed by the ratio of the residual magnetization to the magnetization in a magnetic field of 10 kOe is 80% or more
  • the average recoil permeability in the second and third quadrants is 1.00 or more.
  • It is a rare earth magnet of 1.08 or less.
  • the permanent magnet motor according to the present invention has a coercive force at room temperature of not less than 0.5 kOe and not more than 5 kOe, a squareness ratio represented by a ratio of residual magnetization to magnetization in a magnetic field of 10 kOe, and 80% or more in the second and third quadrants.
  • a first rare earth permanent magnet for changing the magnetization state having an average recoil permeability of 1.00 to 1.08;
  • a second rare earth permanent magnet having a higher coercive force at room temperature than the first rare earth permanent magnet.
  • the following general formula is satisfied, and the squareness ratio expressed by the ratio of the remanent magnetization to the magnetization in a magnetic field of 10 kOe is not less than 80% and the coercive force is not less than 0.5 kOe and not more than 3.5 kOe.
  • a permanent magnet is provided.
  • a method for producing a permanent magnet comprising an aging treatment step of cooling to room temperature at 10 ° C / min.
  • a permanent magnet for a motor is provided.
  • a permanent magnet having a low coercive force and a high squareness ratio can be provided. Therefore, the low coercive force side magnet of a motor, particularly a motor capable of changing the magnetization state of the whole or a part of the permanent magnet. Is preferred. Moreover, if it is the manufacturing method of this invention, the low coercive force and the permanent magnet of a high squareness ratio can be manufactured efficiently. Furthermore, a high-efficiency permanent magnet motor can be realized by using these magnets.
  • the permanent magnet of the present invention satisfies the following general formula, and has a coercive force at room temperature of 0.5 kOe to 5.0 kOe, and a squareness ratio expressed by a ratio of residual magnetization to magnetization in a magnetic field of 10 kOe is 80%. It is the above, It is characterized by the above.
  • the coercive force at room temperature is 0.5 kOe or more and 5.0 kOe or less.
  • the coercive force is less than 0.5 kOe, the magnetic flux control range in the motor that can change the magnetization state of the whole or a part of the permanent magnets becomes narrow.
  • the coercive force exceeds 5.0 kOe, a great amount of electric energy is required to reverse the magnetization of the magnet, so that the energy saving effect is greatly reduced. Therefore, it is preferably 1 to 3.5 kOe, and more preferably 1 to 3.0 kOe.
  • the squareness ratio is 80% or more. When the squareness ratio is less than 80%, the magnetic flux control range in the motor that can change the magnetization state of the whole or a part of the permanent magnets is narrowed. A preferable value of the squareness ratio is 90 to 100%.
  • the squareness ratio of the present invention is a value expressed by the ratio of residual magnetization to magnetization in a magnetic field of 10 kOe. The reason why 10 kOe is selected is as follows.
  • the permanent magnet of the present invention has a low coercive force of 5 kOe or less and is almost magnetically saturated in a magnetic field of 10 kOe, which is suitable for defining the squareness ratio.
  • the theoretical value of the maximum energy product is usually a value obtained by dividing the square of the residual magnetization by 4.
  • the squareness ratio is obtained by dividing the actual maximum energy product value by this value.
  • the permanent magnet of the present invention controls the coercive force to a relatively small value, the squareness ratio applied to the soft magnetic material was used as a reference as a new index representing the squareness.
  • the average recoil permeability in the second and third quadrants is preferably 1.00 to 1.08. In principle, recoil permeability is less than 1.00. If the recoil permeability exceeds 1.08, the magnetic flux control amount of the motor that can change the magnetization state of the whole or a part of the permanent magnets is reduced, and the range in which high-efficiency operation can be performed becomes narrow.
  • a preferred recoil permeability is 1.07 or less.
  • the recoil permeability is obtained from a change due to the magnetic field of the magnetization in the second and third quadrants using a sample vibration type magnetometer, for example, a change from 15 kOe to zero magnetic field.
  • the magnetization measurement is performed by applying a magnetic field up to ⁇ 15 kOe opposite to the direction of magnetizing the sample magnetized with a pulse magnetic field of 60 kOe and changing the strength of the magnetic field from there to 0. Thereafter, after applying a magnetic field up to ⁇ 14 kOe, the magnetic field is similarly changed to zero and the magnetization is measured. This is repeated every 1 kOe and measured in the range from the third quadrant to the second quadrant.
  • the recoil permeability approximates a straight line, and is a value obtained by dividing each magnetic field ( ⁇ 15 kOe, ⁇ 14 kOe,...) And the magnetization difference when the magnetic field is zero by the amount of change in the magnetic field. The average of them is the average recoil permeability.
  • Coercive force and squareness ratio can be obtained by ordinary measurement.
  • the coercive force is a coercive force when a full loop measurement is performed with a maximum magnetic field of 10 kOe.
  • the squareness ratio is the remanent magnetization relative to the magnetization at 10 kOe.
  • Sm is an essential element which is the basis of the permanent magnet of the present invention together with Co.
  • Ce is an element that can replace the Sm site, maintains the crystal structure, and realizes the characteristics of the present invention.
  • the amount x is 0.5 or less, and when it exceeds that, magnetization decreases.
  • the R element is at least one selected from the group consisting of La, Pr and Nd.
  • R element is an element effective together with Sm and Ce to control the coercive force by heat treatment.
  • the amount x of the R element is 0.3 or less, and if this amount is exceeded, the magnetization will decrease as in the case of Ce.
  • Sm is the element that preferably has the highest content.
  • R elements preferred elements are Pr and La. Instead of R element or Ce, a rare earth element before separation such as misch metal or didymium may be used.
  • Fe is an element that contributes to an increase in saturation magnetization.
  • the amount a is less than 0.05, the effect is small, and when it exceeds 0.3, the squareness decreases and the recoil permeability increases.
  • a preferable range of the a value is 0.10 ⁇ a ⁇ 0.25, and a more preferable range is 0.15 ⁇ a ⁇ 0.23.
  • Cu is an essential element for controlling the coercive force, and is an element that promotes the two-phase separation of the TbCu 7 phase into the CaCu 5 phase and the Th 2 Zn 17 phase by aging treatment.
  • the amount b is 0.02 ⁇ b ⁇ 0.15. If it is 0.02 or more, its function is exhibited. On the other hand, if it exceeds 0.15, the magnetization decreases. More preferably, 0.04 ⁇ b ⁇ 0.12.
  • the M element is at least one selected from the group consisting of Ti, Zr and Hf.
  • the M element is an element that promotes stabilization of the TbCu 7 phase that is a high-temperature phase.
  • This solution makes it easy to obtain a single phase of TbCu 7 phase after solution forming in a wide range.
  • a part of the TbCu 7 phase is separated into two phases of a CaCu 5 phase and a Th 2 Zn 17 phase. It is preferable to control the coercive force while leaving the TbCu 7 phase being used, and to have a structure having three phases.
  • the amount c is less than 0.01, the effect is hardly exhibited.
  • the amount c exceeds 0.04, it is difficult to obtain the target TbCu 7- phase single phase, and the Th 2 Ni 17 phase is excessively increased, making it difficult to control the coercive force and the squareness.
  • the T element is at least one selected from the group consisting of Mn, V, Nb, Ta, Cr, Mo, W and Ni, and is an element effective for controlling coercive force and squareness.
  • the amount is 0.05 or less, and if it exceeds that, the magnetization will decrease. As a result, the residual magnetization (residual magnetic flux density) is lowered, and more magnets are used to obtain a constant magnetic flux amount. Preferably, it is 0.04 or less.
  • the z value is the total atomic ratio of Co, Fe, etc. with respect to the rare earth element.
  • the ratio of the two phases (CaCu 5 phase and Th 2 Zn 17 phase) precipitated from the TbCu 7 phase by aging treatment varies depending on this value.
  • the coercive force is controlled by a configuration having these three phases. If the z value is less than 6, it is difficult to control the coercive force. On the other hand, if the z value exceeds 8.3, the squareness ratio decreases and the recoil permeability increases, so the amount of magnetic flux that can be controlled decreases.
  • a preferable range of the z value is 6.1 or more and 8.2 or less.
  • the magnet of the present invention may contain oxygen of 5000 wtppm or less, hydrogen of 2000 wtppm or less, and nitrogen of 1000 wtppm or less.
  • oxygen 5000 wtppm or less
  • hydrogen 2000 wtppm or less
  • nitrogen 1000 wtppm or less.
  • hydrogen may remain somewhat, but there is no problem in characteristics.
  • other components including impurities may be contained in a total amount of 0.1 wt% or less.
  • the method for producing the permanent magnet of the present invention is not particularly limited, but the following method can be mentioned as a method for obtaining it efficiently.
  • the mother alloy is prepared at a predetermined ratio, then melted by a method such as high-frequency melting, and is produced by casting or strip casting.
  • a method such as high-frequency melting
  • the casting method it is preferable to cast on a water-cooled mold or a water-cooled metal plate in order to obtain a sufficient cooling rate.
  • the thickness of the obtained flakes is preferably about 70 ⁇ m or more and 2 mm or less. More preferably, it is mainly 100 ⁇ m or more and 1 mm or less.
  • the pulverized powder may be finely pulverized using a jet mill, and the average particle size of the pulverized powder is preferably 1 to 15 ⁇ m.
  • the average particle size is 1 ⁇ m or less, it becomes difficult to obtain a sufficient sintered density, and oxidation tends to occur.
  • the average particle size exceeds 15 ⁇ m, the squareness starts to deteriorate.
  • the thickness is preferably 2 to 12 ⁇ m, more preferably 3 to 10 ⁇ m.
  • hydrogen pulverization using hydrogen may be used, but this method may not reach a predetermined average particle size. For this reason, hydrogen storage / release may be repeated a plurality of times, or after hydrogen pulverization, further pulverization may be performed by a wet method such as a ball mill or a dry method such as a jet mill.
  • Forming in a magnetic field may be a longitudinal magnetic field or a transverse magnetic field, and the magnetic field at that time is preferably stronger in order to orient, but may be 20 kOe that is normally used.
  • the molding pressure is preferably higher, but it may be 100 kg / cm 2 or more, which is usually used.
  • Sintering and solution treatment are first performed from room temperature to 1 to 50 ° C./min.
  • the temperature is raised at a rate of 500 ° C. to 700 ° C. for 1 to 2 hours.
  • the content of gas components such as oxygen, hydrogen, and nitrogen can be reduced.
  • the temperature was increased in the Ar atmosphere to a sintering temperature of 1000 to 1200 ° C. at the same temperature rising rate, and sintering was continued for a total of 10 minutes to 20 hours in this temperature range, followed by solution treatment.
  • the solution treatment is a treatment aiming at a single phase, and the treatment time is preferably about 1 to 10 hours.
  • the solution treatment is preferably performed at the same temperature as the sintering temperature or about 20 to 30 ° C.
  • the aging may be performed at a temperature of 600 ° C. or higher and 800 ° C. or lower for 10 minutes to 20 hours following sintering and solution treatment, and thereafter 1 to 10 ° C./min. Cool to 500 ° C. at a cooling rate of 1-10 ° C./min.
  • the cooling rate may be up to room temperature, but considering the production efficiency, it is sufficient to control the cooling rate to 500 ° C.
  • the treatment may be once cooled to room temperature or continuously.
  • aging can control the coercive force by one-stage (one temperature condition) treatment, but it may be two-stage (two temperature conditions) or more treatment. In this case, it is preferable to go from the high temperature side to the low temperature, and in this case, the cooling rate between the two temperatures is 1 to 5 ° C./min. To do. In the case of multiple stages, the entire aging time may be 20 hours or less.
  • the aging temperature is preferably 600 ° C. or higher and lower than 800 ° C., more preferably 600 ° C. or higher and 750 ° C. or lower.
  • the atmosphere in this process is preferably a non-oxidizing atmosphere, and treatment in Ar, nitrogen and vacuum is preferred.
  • the sintered density is preferably 95% or more.
  • the sintered density is determined by (actual measured value / theoretical density by Archimedes method) ⁇ 100%.
  • the cooling rate varies depending on whether the aging treatment, which is the next step, is performed continuously, or when aging is performed after cooling to room temperature. That is, in the case of continuous processing, if the cooling rate is too high, there is a possibility of overshooting. 10 ° C./min. The following is preferred. In the case of cooling to room temperature once, 10 ° C./min. 100 ° C./min. The following is preferred.
  • the cooling rate is 5 ° C./min.
  • the CaCu 5 phase having high magnetic anisotropy, the Th 2 Zn 17 phase main phase which is a highly saturated magnetization phase, and the TbCu 7 phase formed before the aging treatment also remain.
  • the above-described magnet characteristics can be satisfied with a configuration having three phases. Therefore, sintering, single phase of TbCu 7 phase in the solution treatment, or is important to the main phase, by aging a TbCu 7 phase of high saturation magnetization Th 2 Zn 17 phase and high magnetic anisotropy of
  • the coercive force can be controlled by separating into two phases of CaCu 5 phase.
  • the phase ratio of the TbCu 7 phase is preferably 30% or more, more preferably 50% or more by volume. Further, when the TbCu 7 phase is 100%, the coercive force is extremely small. Preferably it is 95% or less, More preferably, it is 90% or less.
  • Th 2 Ni 17 phase is generated in addition to the CaCu 5 phase, the Th 2 Zn 17 phase, and the TbCu 7 phase depend on the composition and heat treatment conditions. Since the Th 2 Ni 17 phase has a small magnetic anisotropy constant or has in-plane magnetic anisotropy, it may have a 4-phase configuration. In the case of a four-phase configuration, the amount of Th 2 Ni 17 phase is preferably 10% or less.
  • Presence / absence of TbCu 7 phase, CaCu 5 phase and Th 2 Zn 17 phase can be determined by XRD (X-ray diffraction method). In the present invention, it is not excluded that only each phase has a phase configuration other than three phases. The phase ratio can be determined by X-ray diffraction.
  • the evaluation method uses an X-ray diffraction method. That is, the characteristic diffraction line of each phase is obtained from the diffraction intensity. That is, the TbCu 7 phase is based on diffraction on the (200) plane in X-ray diffraction in a single phase after solution treatment, and the ratio of the phase is obtained with a decrease in strength.
  • the Th 2 Zn 17 phase, the CaCu 5 phase, and the Th 2 Ni 17 phase are separately produced as single phases, and the diffraction of the (024) plane, (110) plane, (200) plane, and (203) plane is performed. Obtained as a relative value to the intensity.
  • the conditions for the X-ray diffraction measurement are 50 kV and 100 mA. Moreover, since the same result is obtained also by observation of SEM and EPMA, this method may be used.
  • the TbCu 7 phase is preferably 20% or more, and more preferably 30% or more.
  • the above aging conditions are preferable. If control can be performed in a shorter time, there is no problem even with heat treatment on the high temperature side exceeding 800 ° C. Considering time control in aging at the time of mass production, it is preferably less than 800 ° C., more preferably 790 ° C. or less.
  • the obtained magnet has excellent oxidation resistance, but it can be used in a wide variety of environments by performing various surface treatments such as Ni plating, Cu plating, and Al plating in order to provide further oxidation resistance. I can do it.
  • the permanent magnet motor using the permanent magnet according to the present invention reverses the magnetization direction of some magnets and controls the amount of magnetic flux, thereby improving the efficiency. It is intended. That is, the permanent magnet motor has a coercive force at room temperature of 0.5 kOe or more and 5 kOe or less, a squareness ratio represented by a ratio of residual magnetization to magnetization in a magnetic field of 10 kOe, and an average recoil of the second and third quadrants.
  • the first rare earth permanent magnet is a low coercivity magnet that reverses the magnetization direction to control the magnetic flux.
  • the first rare earth permanent magnet is preferably in the range of 5 to 70% of the total magnet volume. By setting it as such a range, the output of a motor, efficiency, and reliability can be improved. Preferably it is 10 to 67%, more preferably 15 to 50%.
  • the coercive force of the first rare earth permanent magnet at room temperature is 0.5 kOe or more and 3.5 kOe or less.
  • the first rare earth permanent magnet preferably has a composition containing a rare earth element containing Sm and a transition metal element containing Co as a main component.
  • a more preferable composition is a composition represented by the general formula described above.
  • Examples of the second rare earth permanent magnet include an NdFeB magnet.
  • the permanent magnet motor of the present invention may be either an inner rotor type or an outer rotor type, and may have either a surface magnet type (SPM) or an embedded magnet type (IPM).
  • SPM surface magnet type
  • IPM embedded magnet type
  • SPM surface magnet type
  • IPM embedded magnet type
  • a permanent magnet including a first rare earth permanent magnet and a second rare earth permanent magnet is embedded in a rotor.
  • an inner rotor type IPM type is shown in FIG.
  • the rotor 1 includes a rotor core 2, a plurality of first rare earth permanent magnets (low coercivity permanent magnets) 3, and a plurality of second rare earth permanent magnets (high coercivity permanent magnets) 4. It is configured.
  • the first rare earth permanent magnet 3 and the second rare earth permanent magnet 4 are embedded in the rotor core 2 and arranged in the circumferential direction of the rotor 1.
  • the first cavity 5 is provided at both ends of the first rare earth permanent magnet 3.
  • the second cavity 6 is provided at both ends of the second rare earth permanent magnet 4.
  • Reference numeral 7 denotes a magnetic pole portion of the rotor core 2.
  • the rotor 21 in the permanent magnet motor of this embodiment includes a rotor core 22, a first rare earth permanent magnet 23, and a second rare earth permanent magnet 24.
  • the rotor core 22 is configured by stacking silicon steel plates, for example.
  • Four first rare earth permanent magnets 23 and two second rare earth permanent magnets 24 are embedded in the radial cross section of the rotor core 22.
  • the first rare earth permanent magnet 23 is disposed along the radial direction of the rotor 21 and has a trapezoidal cross section.
  • the magnetization direction of the first rare earth permanent magnet 23 is substantially the circumferential direction.
  • the second rare earth permanent magnet 24 is disposed substantially in the circumferential direction and has a rectangular cross section.
  • the magnetization direction of the second rare earth permanent magnet 24 is substantially the radial direction.
  • Cavities 25 are provided at both ends of each of the first rare earth permanent magnet 23 and the second rare earth permanent magnet 24.
  • the bolt hole 26 is opened in the rotor core 22.
  • the magnetic pole core 27 of the rotor core 22 is formed so as to be surrounded by the two first rare earth permanent magnets 23 and the one second rare earth permanent magnet 24.
  • the central axis direction of the magnetic core part 27 of the rotor core 22 is the d axis, and the central axis direction between the magnetic poles is the q axis.
  • the first rare earth permanent magnet 23 is arranged in the q-axis direction which is the central axis between the magnetic poles, and the magnetization direction of the first rare earth permanent magnet 23 is 90 ° or 90 ° with respect to the q axis.
  • the magnetic pole faces facing each other are the same.
  • the second rare earth permanent magnet 24 is disposed in a direction perpendicular to the d axis that is the central axis of the magnetic pole core 27, and the magnetization direction is 0 ° or 180 ° with respect to the d axis.
  • the directions of the magnetic poles are opposite to each other.
  • Such a rotor 21 is accommodated in the stator 28.
  • the stator 28 is configured by housing the armature winding 29 in a slot formed inside the stator core 30.
  • the inner peripheral surface of the stator 28 and the outer peripheral surface of the rotor 21 are opposed to each other through an air gap 31.
  • the rotor 41 in the permanent magnet motor of the present embodiment has a first rare earth permanent magnet 43 and a second rare earth permanent magnet 44 embedded in a rotor core 42. It is a configuration.
  • the rotor core 42 is configured by laminating silicon steel plates. Eight first rare earth permanent magnets 43 and two second rare earth permanent magnets 44 are embedded in the radial cross section of the rotor core 42. Each of the eight sets of the first rare earth permanent magnet 43 and the second rare earth permanent magnet 44 is installed in a convex shape on the inner diameter side of the rotor 41.
  • the magnetization directions of the first rare earth permanent magnet 43 and the second rare earth permanent magnet 44 are both substantially smaller in magnet size.
  • both ends of the first rare earth permanent magnet 43 and the second rare earth permanent magnet 44 may be provided with a magnetic flux short circuit and a cavity 45 for stress relaxation.
  • the magnetic core 46 of the rotor core 42 is formed so as to be surrounded by the first rare earth permanent magnet 43 and the second rare earth permanent magnet 44.
  • Reference numeral 47 denotes a rotating shaft.
  • Such a rotor 41 is accommodated in the stator 48.
  • the stator 48 is configured by accommodating the armature winding 49 in a slot formed inside the stator core 50.
  • the inner peripheral surface of the stator 48 and the outer peripheral surface of the rotor 41 are opposed to each other through an air gap 51.
  • the permanent magnet motor used in the present invention is not limited to the forms shown in FIGS.
  • the present invention is applicable to a permanent magnet motor in which a plurality of permanent magnets are regularly arranged. Permanent magnets are arranged in the circumferential direction of the rotor, and magnets with high coercive force and low coercive force are alternated or the number or thickness is changed so that the volume ratio is within the above range. It can be a magnet motor.
  • Example 1A and Table 1B About the composition shown to Table 1A and Table 1B, after preparing raw material powder, it melt
  • the obtained sample was coarsely pulverized and then finely pulverized with a jet mill to an average particle size of 3 to 5 ⁇ m, and formed into a predetermined shape in a magnetic field under conditions of a magnetic field of 20 kOe and a press pressure of 0.5 t / cm 2 .
  • the obtained molded body is sintered at a temperature lower than the melting point of the parent phase by 50 ° C.
  • the solution was treated and cooled to room temperature at a rate of 50 ° C./min.
  • the aging treatment of the odd-numbered examples was performed by performing heat treatment at 700 ° C. for 3 hours and then cooling at a rate of 10 ° C./min.
  • the first-stage aging treatment of the even-numbered examples was performed at 670 ° C. for 4 hours and then to 600 ° C. at 5 ° C./min. By cooling at a rate of The second-stage aging treatment of the even-numbered examples was performed by holding at 600 ° C.
  • the cooling rate in the aging treatment was from the heat treatment temperature to 500 ° C., and then natural cooling was performed.
  • the temperature rise until sintering is performed at 5 ° C./min in vacuum, once kept at 600 ° C. for degassing, and thereafter all in an Ar atmosphere.
  • the residual magnetic flux density (Br), the coercive force (Hc), the squareness ratio, the recoil permeability, and the Hc range were measured as the evaluation of the magnet characteristics.
  • the residual magnetic flux density (Br), the coercive force (Hc), the squareness ratio, and the recoil permeability were measured using the method described above, and the average value of 100 pieces was obtained.
  • the Hc range indicates the variation in coercive force, and was determined from the “maximum value-minimum value” of 100 coercive forces (Hc) measured. The results are shown in Table 1A and Table 1B.
  • Comparative Examples 1, 2, 3 For the compositions shown in Table 2A, the ingots of Comparative Examples 1, 2, and 3 obtained by high-frequency dissolution were pulverized to a particle size of 1 to 5 ⁇ m with a brown mill and then molded in a magnetic field. The molded body was sintered in vacuum, cooled, and then melted again at 1100 ° C. After aging at 850 ° C for 2 hours, the molded body was cooled to 500 ° C at a rate of 0.5 ° C / min, and subjected to aging treatment. It was. As a result of evaluating the magnetic characteristics, as shown in Table 2A, those having a high coercive force were obtained.
  • the obtained sample was coarsely pulverized in an iron mortar, and then made into a fine powder having an average particle size of 4 ⁇ m by a ball mill in an organic solvent.
  • the obtained fine powder was pressed in a magnetic field of 15 kOe to form a compression molded body.
  • This compression-molded body is sintered at 1210 ° C. for 2 hours in an argon atmosphere of 200 Torr, followed by 1190 ° C. for 2 hours after solution treatment, followed by rapid cooling at a cooling rate of 150 ° C./min. did. Further, an aging treatment was performed at 800 ° C. for 4 hours to obtain Comparative Example 4. Moreover, the permanent magnet of the comparative example 5 was obtained with the manufacturing method similar to the said comparative example 4 without performing the ingot solution treatment of 1180 degreeC for 4 hours.
  • Comparative Example 4 a coercive force of 6.5 kOe was obtained, while in Comparative Example 5, a coercive force of 4.3 kOe was obtained. In particular, in Comparative Example 5, the variation in coercive force was large.
  • Comparative Examples 6 and 7 The permanent magnet of Comparative Example 6 was produced by the following method. Ce 0.56 Sm 0.44 (Co 0.697 Cu 0.13 Fe 0.16 Zr 0.013 ) A molded product obtained by molding a powder having the composition given by 6.2 in the absence of a magnetic field is 1140. Sintered at 1 ° C. for 1 hour and cooled to room temperature so as to pass from 1100 ° C. to 600 ° C. in 15 minutes. Next, this product was held at 600 ° C. for 15 minutes and aged to 300 ° C. over 8 hours. The characteristics shown in Table 2A were obtained. That is, the high coercive force and its variation are relatively large.
  • the permanent magnet of Comparative Example 7 was produced by the following method.
  • a molded product having a composition given by Ce 0.85 Sm 0.15 (Co 0.702 Fe 0.16 Cu 0.13 Zr 0.008 ) 5.95 was molded in the absence of a magnetic field.
  • the obtained molded product was sintered at 1120 ° C. for 1 hour in the same manner as in Comparative Example 6, and then cooled to room temperature so as to pass from 1100 ° C. to 500 ° C. in about 60 minutes. Subsequently, after maintaining at 500 ° C. for 20 minutes, it was gradually cooled to 300 ° C. in 4 hours.
  • Comparative Example 6 has too high coercive force
  • Comparative Example 7 has a large variation in coercive force.
  • Comparative Examples 8 and 9 The permanent magnet of Comparative Example 8 was produced by the following method.
  • the alloy shown in Table 2A was melted at high frequency in an argon gas atmosphere, and an ingot obtained by casting was subjected to a solution treatment at 1180 ° C. for 6 hours. After the treatment, the alloy was rapidly cooled in liquid nitrogen.
  • the obtained alloy was coarsely pulverized in an iron mortar and further finely pulverized in an organic solvent by ball milling to obtain a powder of 2 to 10 ⁇ m. This powder was press-molded in a magnetic field of 12 kOe to obtain a compression molded body.
  • the compression molded body was sintered in a hydrogen atmosphere at 1200 ° C. for 2 hours, and after sintering, the permanent magnet of Comparative Example 8 was cooled to a temperature of 800 ° C. or less at a cooling rate of 100 ° C./min. Got.
  • the permanent magnet of Comparative Example 9 was produced by the following method. Without subjecting the ingot after casting as described above to solution treatment, coarse pulverization, fine pulverization, press molding and sintering under the same conditions as described above, followed by solution treatment after sintering at 1160 ° C. for 8 hours. A permanent magnet of Comparative Example 9 was obtained. In any case, 100 samples were prepared, and the average values of the evaluation results of the magnet characteristics are shown in Table 2A.
  • Comparative Example 11 only the cooling rate after sintering in Comparative Example 10 was set to 1000 ° C./min, and then optimum aging treatment was performed at 800 ° C. for 4 hours. In all cases, 100 samples were prepared, and the average value of the evaluation results of the magnet characteristics is shown in Table 2A. In Comparative Example 10, the coercive force was 8.8 kOe, and in Comparative Example 11, it was 2.3 kOe. In Comparative Example 10, the coercive force was large.
  • Comparative Examples 12 and 13 The permanent magnet of Comparative Example 12 was produced by the following method.
  • An alloy having a composition represented by the chemical formula Sm (Ni 0.11 Fe 0.19 Co 0.6 Cu 0.1 ) 6.9 was high-frequency dissolved in an argon gas atmosphere and coarsely pulverized in an iron mortar.
  • the coarsely pulverized powder was further made into a fine powder having an average particle size of 2 to 10 ⁇ m by ball milling in a hexane solvent.
  • the obtained fine powder was compression molded using a mold at a pressure of 5 ton / cm 2 in a magnetic field of 12 kOe.
  • the compressed body thus obtained was sintered in an inert gas atmosphere at a temperature of 1210 ° C. for 2 hours and then cooled to 500 ° C. or less at a cooling rate of 60 ° C./min.
  • Comparative Example 13 only the cooling rate after sintering in Comparative Example 12 was set to 1000 ° C./min, and then an aging treatment was performed at 800 ° C. ⁇ 4 hours. In any case, 100 samples were prepared and the magnetic characteristics were evaluated, and as a result, the coercive force was too large or too small, and the coercive force variation was large.
  • Comparative Examples 14 and 15 The permanent magnet of Comparative Example 14 was produced by the following method.
  • An alloy having a composition represented by the composition formula Sm (Co 0.60 Fe 0.19 Ni 0.11 Cu 0.1 ) 6.9 was melted at high frequency in an argon gas atmosphere and coarsely pulverized in an iron mortar.
  • the coarsely pulverized powder was further made into a fine powder having an average particle size of 3 ⁇ m by ball milling in a hexane solvent.
  • This fine powder was compression molded using a mold in a magnetic field of 12 kOe at a pressure of 5 ton / cm 2 .
  • the compressed body thus obtained was sintered in an inert gas atmosphere at a temperature of 1190 ° C. for 2 hours, and subsequently cooled to 500 ° C. or less at a cooling rate of 200 ° C./min.
  • Comparative Example 15 only the cooling rate after sintering in Comparative Example 14 was set to 1000 ° C./min, and then optimal aging treatment was performed at 800 ° C. for 2 hours. In any case, as a result of producing 100 samples and evaluating the magnet characteristics, the variation in coercive force was large.
  • MM used in Comparative Examples 22 and 23 is a misch metal whose composition is La60Ce10Pr20Nd10 by weight ratio.
  • the permanent magnet motors used as references are all based on the efficiency when using NdFeB magnets (Comparative Example 38: the same magnet as the low coercive force side is used for the low coercive force side) as the reference, and the relative efficiency of the example and the comparative example are relative to each other. Shown as a value.
  • the evaluation condition is an average value of efficiency at high speed rotation (3000 rpm), medium speed rotation (2000 rpm), and low speed rotation (1000 rpm) of the motor. These conditions are low torque, medium torque, and high torque when torque is used as an index, and the efficiency under each operating condition is reflected.
  • the motor which can change the magnetization state of the whole or a part of permanent magnet of the structure shown in FIG. 2 as an embodiment this time, a magnet having a high coercive force and a magnet having a relatively small coercive force.
  • the permanent magnet having the magnetic characteristics of the present embodiment is used as a permanent magnet motor magnet constituted by the combination, the motor structure is not particularly limited.
  • Examples 35 to 40 Comparative Examples 39 to 40
  • raw material powders having the same composition as in Example 1 were prepared, and the production conditions were changed as shown in Table 3 for production.
  • the obtained permanent magnet was measured for the same magnetic properties as in Example 1. The results are shown in Table 3.
  • the permanent magnet motor used in this embodiment is an example, and any type of permanent magnet motor of inner rotor type, outer rotor type, SPM type, or IPM type (for example, in FIGS. High efficiency can be achieved even with the structure shown).

Abstract

La présente invention concerne un aimant samarium-cobalt (SmCo) qui présente une faible force coercitive et un rapport élevé de perpendicularité et qui peut servir d'aimant pour un moteur, ainsi que son procédé de fabrication. Un aimant permanent comportant une composition spécifique présente une force coercitive de 0,5 kOe à 5 kOe et un taux de rectangularité d'au moins 80 % quand il est exprimé comme le rapport entre la magnétisation résiduelle et la magnétisation par un champ magnétique de 10 kOe.
PCT/JP2009/059713 2008-05-30 2009-05-27 Aimant permanent et son procédé de fabrication, aimant permanent pour moteur et moteur à aimants permanents WO2009145229A1 (fr)

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CN2009801209524A CN102047536B (zh) 2008-05-30 2009-05-27 永久磁铁及其制造方法、电动机用永久磁铁及永久磁铁电动机

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US9774234B2 (en) 2010-03-30 2017-09-26 Kabushiki Kaisha Toshiba Permanent magnet and method for manufacturing the same, and motor and power generator using the same
CN102821891A (zh) * 2010-03-30 2012-12-12 株式会社东芝 永久磁石及其制造方法、以及使用该磁石的发动机和发电机
JP2011216716A (ja) * 2010-03-31 2011-10-27 Toshiba Corp 永久磁石およびそれを用いたモータおよび発電機
JP2012069750A (ja) * 2010-09-24 2012-04-05 Toshiba Corp 永久磁石とその製造方法、およびそれを用いたモータと発電機
CN102447314A (zh) * 2010-09-24 2012-05-09 株式会社东芝 永磁体及其制造方法、以及使用永磁体的电动机和发电机
US9583243B2 (en) 2010-09-24 2017-02-28 Kabushiki Kaisha Toshiba Permanent magnet and method for manufacturing the same, and motor and power generator using the same
TWI477036B (zh) * 2012-05-28 2015-03-11 Hitachi Ind Equipment Sys Compound Torque Rotary Motor
JP2013140993A (ja) * 2013-02-04 2013-07-18 Toshiba Corp 永久磁石およびそれを用いたモータおよび発電機
WO2017061126A1 (fr) * 2015-10-08 2017-04-13 国立大学法人九州工業大学 Aimant permanent à base de terres rares et cobalt
JPWO2017061126A1 (ja) * 2015-10-08 2018-09-13 国立大学法人九州工業大学 希土類コバルト系永久磁石
US11380465B2 (en) 2015-10-08 2022-07-05 Kyushu Institute Of Technology Rare earth cobalt-based permanent magnet
GR20180100148A (el) * 2018-04-04 2019-11-28 Δημητριος Γεωργιου Νιαρχος Κραματα υψηλης εντροπιας σπανιων γαιων και κραματα μεταβατικων στοιχειων ως δομικα στοιχεια για τη συνθεση νεων μαγνητικων φασεων για μονιμους μαγνητες
CN113381538A (zh) * 2020-03-09 2021-09-10 丰田自动车株式会社 旋转电机
CN113381538B (zh) * 2020-03-09 2024-04-12 丰田自动车株式会社 旋转电机

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