WO2011070827A1 - Aimant anisotropique aux terres rares et procédé de production de cet aimant - Google Patents

Aimant anisotropique aux terres rares et procédé de production de cet aimant Download PDF

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Publication number
WO2011070827A1
WO2011070827A1 PCT/JP2010/064611 JP2010064611W WO2011070827A1 WO 2011070827 A1 WO2011070827 A1 WO 2011070827A1 JP 2010064611 W JP2010064611 W JP 2010064611W WO 2011070827 A1 WO2011070827 A1 WO 2011070827A1
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rare earth
magnet
raw material
diffusion
earth anisotropic
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PCT/JP2010/064611
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English (en)
Japanese (ja)
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本蔵　義信
千里 三嶋
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愛知製鋼株式会社
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Priority to CN201080055297.1A priority Critical patent/CN102640238B/zh
Priority to US13/514,942 priority patent/US20120299675A1/en
Priority to EP10835749.2A priority patent/EP2511920B1/fr
Priority to JP2011545106A priority patent/JPWO2011070827A1/ja
Publication of WO2011070827A1 publication Critical patent/WO2011070827A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0433—Nickel- or cobalt-based alloys
    • C22C1/0441—Alloys based on intermetallic compounds of the type rare earth - Co, Ni
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
    • H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
    • H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
    • H01F1/0576—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together pressed, e.g. hot working
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
    • H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
    • H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
    • H01F41/0293—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets diffusion of rare earth elements, e.g. Tb, Dy or Ho, into permanent magnets

Definitions

  • the present invention relates to a rare earth anisotropic magnet having excellent magnetic properties and a method for producing the same.
  • a rare earth (anisotropic) magnet made of a compact obtained by compression molding rare earth magnet powder or a sintered compact obtained by sintering the compact exhibits very high magnetic properties. For this reason, the utilization is anticipated for various apparatuses, such as an electric appliance and a motor vehicle in which energy saving, weight reduction, etc. are desired.
  • rare earth magnets In order to expand the use of rare earth magnets, high heat resistance that exhibits stable magnetic properties even in a high temperature environment is required. In order to achieve this, research and development for improving the coercive force of rare earth magnets has been actively conducted. Specifically, at present, rare elements such as dysprosium (Dy) and terbium (Tb) effective for improving the coercive force are often diffused from the surface of the rare earth magnet. There are descriptions related to these in the following documents.
  • Dy dysprosium
  • Tb terbium
  • the present invention does not necessarily use a rare element such as Dy, but also provides a rare earth anisotropy capable of developing a high coercive force while ensuring a high magnetization or a high residual magnetic flux density. It is an object of the present invention to provide a production method capable of obtaining a magnet and a rare earth anisotropic magnet obtained by the production method.
  • the present inventor has obtained a mixed raw material in which a diffusion raw material composed of R ′ and Cu is mixed with a magnetic raw material for generating an R 2 TM 14 B 1 type crystal. It has been newly found that a sintered magnet obtained by using a high magnetic flux density and a high coercive force. By further developing this result, the present invention described below has been completed.
  • the method for producing a rare earth anisotropic magnet of the present invention is a tetragonal compound of a rare earth element (hereinafter referred to as “R”), boron (B), and a transition element (hereinafter referred to as “TM”).
  • R ′ a rare earth element
  • a rare earth anisotropic magnet excellent not only in coercive force but also in magnetic characteristics such as residual magnetic flux density can be obtained.
  • it is not always necessary to use rare and expensive Dy or the like as the diffusion material and it is possible to use a diffusion material composed of R ′ and Cu made of Nd or the like that is easily available and relatively inexpensive. For this reason, it is possible to stably obtain a rare earth anisotropic magnet having high magnetic properties at low cost.
  • the mechanism by which the rare earth anisotropic magnet obtained by the production method of the present invention exhibits excellent magnetic properties is not necessarily clear.
  • the current situation is considered as follows. First, the melting point of R ′ alone or Cu alone is high, but the melting point of these alloys is generally low. In particular, the melting point of an alloy in the vicinity of the eutectic composition decreases rapidly. Moreover, the molten alloy has very high wettability with respect to a tetragonal compound (R 2 TM 14 B 1 type crystal). For this reason, when the mixed raw material is heated, the diffusion raw material around the magnet raw material starts to melt and smoothly covers the surface of the R 2 TM 14 B 1 type crystal in which R ′ and Cu are the main phases. Further, R ′ and Cu diffuse between the crystals, and form a crystal grain boundary surrounding each crystal (this is referred to as “enveloping layer” or “diffusion layer” as appropriate).
  • the envelope layer made of R ′ and Cu can repair the strain present on the surface of the R 2 TM 14 B 1 type crystal and suppress the occurrence of reverse magnetic domains in the vicinity of the surface.
  • this envelope layer, each of the R 2 TM 14 B 1 type crystals were isolate can block the magnetic interaction by adjacent R 2 TM 14 B 1 type crystal.
  • the magnetization exhibited by the magnet raw material increases as the composition of the magnet raw material approaches the theoretical composition necessary for the formation of the R 2 TM 14 B 1 type crystal. Specifically, it is more preferable that the magnet raw material has a composition of R: 11.8 atomic% (at%), B: 5.9 at%, and TM: composition close to the balance (theoretical vicinity composition). Therefore, when the magnetic raw material according to the present invention is 100 at% as a whole, R: 11.6 to 12.7 at%, further 11.8 to 12.5 at%, further 11.8 to 12.4 at%, B: It is preferable that the composition is near the theoretical value of 5.5 to 7 at% or even 5.9 to 6.5 at%.
  • the magnet raw material or the diffusion raw material may also contain “modified elements” that are effective elements for improving the characteristics of rare earth anisotropic magnets and “unavoidable impurities” that are difficult to remove costly and technically.
  • TM is preferably one or more of 3d transition elements having atomic number 21 (Sc) to atomic number 29 (Cu) or 4d transition elements having atomic number 39 (Y) to atomic number 47 (Ag).
  • TM is preferably a group 8 element of iron (Fe), cobalt (Co) or nickel (Ni), more specifically Fe.
  • Co is an element effective for improving the Curie point, and improves the heat resistance of the rare earth anisotropic magnet. Therefore, 0.5 to 5.4 at% Co may be included when the entire rare earth anisotropic magnet is 100 at%.
  • Co is preferably supplied from at least one of a magnet raw material and a diffusion raw material.
  • modifying elements Nb, Zr, Ti, V, Cr, Mn, Ni, Mo, etc.
  • modifying elements are preferably 2.2 at% or less when the entire rare earth anisotropic magnet is 100 at%.
  • Nd is typical, but Pr may also be included. This is because even if a part of Nd in the magnet raw material or the diffusion raw material is replaced with Pr, the influence on the magnetic properties is small, and a mixed rare earth raw material (zidmium) mixed with Nd and Pr is available at a relatively low cost.
  • coercive force improving elements such as Dy, Tb, and Ho are rare elements and are expensive, and thus are preferably suppressed in use. Therefore, it is preferable that the magnet raw material or the diffusion raw material according to the present invention does not contain Dy, Tb, and Ho.
  • R and R ′ are used as designations to substitute for specific rare earth element names, and unless otherwise specified, mean one or two or more of the rare earth elements, which may be the same or different. .
  • the rare earth element contained in the magnet raw material is “R”
  • the rare earth element contained in the diffusion raw material is “R ′”.
  • the rare earth element constituting the tetragonal compound that is, R 2 TM 14 B 1 type crystal
  • the crystal A rare earth element diffusing on the surface or grain boundary is represented by “R ′”.
  • R that is discharged during the formation of the tetragonal compound to form a grain boundary or the like is expressed as “R ′” for convenience.
  • R or R ′ is one or more of yttrium (Y), lanthanoid and actinoid, and in addition to Nd, Pr, Dy, Tb, Ho, Y, lanthanum (La), cerium (Ce), Typical examples are samarium (Sm), gadolinium (Gd), erbium (Er), thulium (TM element), and lutetium (Lu).
  • the rare earth anisotropic magnet may be a rare earth anisotropic sintered magnet obtained by sintering magnet powder particles, or a rare earth anisotropic dense magnet obtained by densely agglomerating the magnet powder particles.
  • x to y in this specification includes a lower limit value x and an upper limit value y.
  • various lower limit values or upper limit values described in the present specification can be arbitrarily combined to constitute a range such as “ab”.
  • any numerical value included in the range described in the present specification can be used as an upper limit value or a lower limit value for setting the numerical value range.
  • the average crystal grain size referred to in the present specification is based on the method for obtaining the average diameter d of crystal grains in JIS G 0551.
  • the present invention will be described in more detail with reference to embodiments of the invention.
  • the contents described in this specification including the following embodiments can be applied not only to the method for manufacturing a rare earth anisotropic magnet according to the present invention but also to a rare earth anisotropic magnet obtained by the manufacturing method. . Therefore, one or two or more configurations arbitrarily selected from the present specification can be added to the configuration of the present invention described above.
  • the structure related to the manufacturing method can be a structure related to an object if understood as a product-by-process. Note that which embodiment is the best depends on the target, required performance, and the like.
  • the method for producing a rare earth anisotropic magnet of the present invention includes at least a mixing step, a forming step, and a diffusion step.
  • the mixing step of the present invention is a magnetic raw material capable of generating an R 2 TM 14 B 1 type crystal that is a tetragonal compound of R, B, and TM, and at least a source of R ′ and Cu.
  • This is a step of obtaining a mixed raw material obtained by mixing a diffusion raw material.
  • a magnet raw material and a diffusion raw material made of pulverized and classified powder are uniformly mixed using a Henschel mixer, a roxing mixer, a ball mill, or the like. This mixing is preferably performed in an antioxidant atmosphere (for example, an inert gas atmosphere or a vacuum atmosphere).
  • the magnet raw material for example, an ingot material melted and cast by various melting methods (high frequency melting method, arc melting method, etc.) or a strip cast material manufactured by a strip cast method can be used. Among them, it is preferable to use a strip cast material. The reason is as follows.
  • the R content and the B content in the magnet raw material are brought close to the stoichiometric composition of the R 2 TM 14 B 1 compound (a composition in the vicinity of the theory).
  • ⁇ Fe as the primary crystal tends to remain.
  • the soft magnetic ⁇ Fe phase tends to remain because the cooling rate during casting is slow. In order to eliminate the ⁇ Fe phase, it is necessary to lengthen the soaking time, and the efficiency is poor and the magnetic characteristics are easily deteriorated. In contrast, in the case of a strip cast material, since the cooling rate at the time of casting is high, the soft magnetic ⁇ Fe phase hardly remains, and even if it remains, it is finely distributed. For this reason, the soft magnetic ⁇ Fe phase can be eliminated in a short soaking time.
  • the crystal grains grow to a preferred size having an average crystal grain size of about 100 ⁇ m (50 to 250 ⁇ m). If the strip thus formed is pulverized, a magnet raw material consisting of crystal grains of an appropriate size in which there is no ⁇ Fe phase and an R-rich phase is formed at the grain boundary can be obtained.
  • the diffusion raw material may be an alloy or compound containing at least R ′ or Cu, and further a mixture of a plurality of types of raw materials (including individual powders) depending on the desired composition.
  • the diffusion raw material is preferably in the form of a powder obtained by hydrogen crushing or mechanical crushing of an ingot material, a strip cast material, or the like.
  • the diffusion raw material is preferably 0.1 to 10% by mass, more preferably 1 to 6% by mass, based on 100% by mass of the entire mixed raw material. If the amount of the diffusion raw material is too small, the formation of the envelope layer (diffusion layer) encapsulating the R 2 TM 14 B 1 type crystal becomes insufficient.
  • At least one of the magnet raw material and the diffusion raw material may be a hydride.
  • a hydride is a substance in which hydrogen is bonded or dissolved in a simple substance, an alloy, a compound, or the like. The hydrogen in these raw materials is discharged at the latest with the progress of the diffusion process, and the diffusion raw materials are melted and diffused to the magnet raw materials.
  • the molding process is a process of obtaining a molded body having a desired shape by pressurizing the mixed raw material placed in the cavity of the mold.
  • the molding pressure at this time is determined in consideration of the desired density of the molded body and the next process, and is, for example, 1 to 10 ton / cm 2 (98 to 980 MPa).
  • the molding process may be performed once or multiple times.
  • the number of moldings may be selected in consideration of the post process. For example, if the sintering step is performed after the molding step, a liquid phase is generated between the powder particles even during the single molding, so that a sufficiently high-density rare earth anisotropic magnet can be obtained. Even when the compact is not sintered, a high-density rare earth anisotropic magnet can be obtained without difficulty by molding many times. In that case, you may change a pressurization atmosphere (temperature), a pressurization apparatus, etc. each time.
  • the molding step includes a preforming step in which a mixed raw material is cold or warm pressed to obtain a preform, and a hot compacted hot compacted compact body is obtained.
  • thermoforming step It may consist of a densification step.
  • a preform that has been cold-formed or cold-formed at low pressure is re-formed hot to form a dense molded product (dense molded product).
  • hot means the temperature range above the recrystallization temperature of the R 2 TM 14 B type 1 crystal
  • cold means a temperature range near or below room temperature
  • warm means between them. It means temperature range.
  • the forming step or the pre-forming step is preferably a forming step in a magnetic field performed in an orientation magnetic field.
  • diffusion step diffusion process by heating the molded body made of the mixed material, the diffusion material composed of Cu and at least R 'in step to diffuse to the surface, or grain boundaries of R 2 TM 14 B 1 type crystal is there.
  • the diffusion raw material depends on its total composition, it generally has a low melting point and is excellent in wettability with respect to R 2 TM 14 B type 1 crystals.
  • diffusion includes surface diffusion, grain boundary diffusion, or body diffusion.
  • the diffusion referred to in the present invention is mainly surface diffusion or grain boundary diffusion. Therefore, the diffusion step is preferably a step of heating the molded body to a temperature at which the diffusion raw material is melted and surface diffusion or grain boundary diffusion is performed.
  • the diffusion step is performed, for example, in an oxidation preventing atmosphere (such as a vacuum atmosphere or an inert atmosphere) at 400 to 900 ° C. If the heating temperature is too low, diffusion does not proceed. On the other hand, if the heating temperature is too high, the R 2 TM 14 B 1 type crystal becomes coarse, which is not preferable.
  • a diffusion material suitable for this is, for example, a material containing 2 to 43 at% Cu and optionally 2.6 to 64 at% Al when the whole is 100 at%. In this case, the heating temperature is preferably 600 to 850 ° C.
  • the diffusion raw material may include Co, Ni, Si, Mn, Cr, Mo, Ti, V, Ga, Zr, Ge, Fe, or the like instead of Al or together with Al. The total amount of these elements is preferably 5 to 64 at% with respect to 100 at% of the entire diffusion raw material.
  • the diffusion process may be a process in which the molded body is heated in a predetermined temperature range
  • other processes performed in the temperature range can also serve as at least a part of the diffusion process.
  • the above-described densification step and the sintering step or anisotropic process described later can also serve as part of the diffusion step.
  • a rare earth anisotropic sintered magnet is obtained.
  • a rare earth (anisotropic) sintered magnet having high magnetic properties, high strength, and high heat resistance can be obtained.
  • the sintering temperature is to suppress the coarsening of the R 2 TM 14 B 1 type crystal grains, and more preferably 1050 ° C. or less 1100 ° C. or less.
  • SPS spark plasma sintering
  • the anisotropic process is a process for providing a rare earth anisotropic magnet by imparting anisotropy to a compact made of an isotropic magnet raw material (rare earth isotropic magnet powder). It is. Specifically, this is a step of subjecting the molded body to a process of aligning the easy magnetization axis (c axis) of the R 2 TM 14 B 1 type crystal in a specific direction. At this time, the c-axis of the R 2 TM 14 B 1 type crystal is oriented in the same direction as the direction in which the processing stress is applied.
  • the processing performed in the anisotropic process is strong processing, hot processing is preferable. Moreover, if it is hot working, the crystal orientation of the R 2 TM 14 B 1 type crystal is easily aligned. Examples of hot working include hot extrusion, hot drawing, hot forging, hot rolling, and the like, which may be used alone or in combination.
  • hot working include hot extrusion, hot drawing, hot forging, hot rolling, and the like, which may be used alone or in combination.
  • casting used for an anisotropic process is the dense compact mentioned above, an anisotropic compact
  • the rare earth anisotropic magnet powder is obtained, for example, by subjecting a base magnet alloy (mother alloy) to a known hydrogen treatment.
  • the hydrogen treatment includes a disproportionation step in which the master alloy absorbs hydrogen to cause a disproportionation reaction, and a recombination step in which the master alloy after the disproportionation step is dehydrogenated and recombined, and HDDR (hydrogenation). It is called -decomposition (or decomposition) -destruction-recombination) or d-HDDR (dynamic-hydrogenation-decomposition (or disporation) -decomposition-recombination).
  • the disproportionation process comprises at least a high-temperature hydrogenation process
  • the recombination process comprises at least a dehydrogenation process (more specifically, a controlled exhaust process).
  • a dehydrogenation process more specifically, a controlled exhaust process
  • the low-temperature hydrogenation step is performed at a low temperature range below the temperature at which the hydrogenation / disproportionation reaction occurs so that the hydrogenation / disproportionation reaction in the next step (high-temperature hydrogenation step) proceeds slowly.
  • This is a process in which hydrogen is sufficiently absorbed and dissolved in the alloy.
  • the low-temperature hydrogenation step is a step in which the magnet alloy of the magnet raw material is held in a hydrogen gas atmosphere at a temperature not higher than the disproportionation reaction temperature (for example, 600 ° C. or lower), and the magnet alloy stores hydrogen. It is. By performing this step in advance, it becomes easy to control the reaction rate of the normal structure transformation in the subsequent high-temperature hydrogenation step.
  • the hydrogen pressure at that time is not particularly limited, but is, for example, about 0.03 to 0.1 MPa.
  • the hydrogen gas atmosphere may be a mixed gas atmosphere of hydrogen gas and inert gas.
  • the hydrogen pressure in this case is a hydrogen gas partial pressure. The same applies to the high-temperature hydrogenation process and the controlled exhaust process.
  • the high-temperature hydrogenation step is a step of causing a hydrogenation / disproportionation reaction to the magnet alloy.
  • the high-temperature hydrogenation step is a step of holding the magnet alloy after the low-temperature hydrogenation step in a hydrogen gas atmosphere at 0.01 to 0.06 MPa and 750 to 860 ° C.
  • the magnet alloy after the low-temperature hydrogenation process has a three-phase decomposed structure ( ⁇ Fe phase, RH 2 phase, Fe 2 B phase).
  • the tissue transformation reaction can be allowed to proceed gently in a state where the hydrogen pressure is suppressed.
  • the reaction rate When the hydrogen pressure is too low, the reaction rate is low, and the untransformed structure remains, leading to a decrease in coercive force. If the hydrogen pressure is excessive, the reaction rate is high and the anisotropic ratio is lowered. If the temperature of the hydrogen gas atmosphere is too low, the three-phase decomposition structure tends to be non-uniform and the coercive force is reduced. If the temperature is excessive, the crystal grains become coarse and the coercive force is lowered. In the high-temperature hydrogenation process, the hydrogen pressure or temperature does not need to be constant throughout. For example, at the end of the process in which the reaction rate decreases, at least one of hydrogen pressure and temperature may be increased to adjust the reaction rate to promote three-phase decomposition (tissue stabilization step).
  • the controlled exhaust process is a process in which the structure that has undergone the three-phase decomposition in the high-temperature hydrogenation process is recombined.
  • dehydrogenation is performed slowly under a relatively high hydrogen pressure, and the recombination reaction proceeds slowly.
  • the controlled exhaust process is a process of maintaining the magnet alloy after the high-temperature hydrogenation process in a hydrogen gas atmosphere at 750 to 850 ° C. with a hydrogen pressure of 0.7 to 6.0 kPa.
  • hydrogen is removed from the RH 2 phase during the above three-phase decomposition.
  • the forced exhaust process is a process for removing hydrogen remaining in the magnet alloy and completing the dehydrogenation process.
  • This step is not particularly limited in terms of processing temperature, degree of vacuum, etc., but is preferably performed in a vacuum atmosphere of 750 to 850 ° C. and 1 Pa or less. If the treatment temperature is too low, it takes a long time to exhaust, and if it is too high, the crystal grains become coarse. When the degree of vacuum is too low, hydrogen remains, and the magnetic properties of the obtained rare earth anisotropic magnet powder may be deteriorated. Rapid cooling after this step is preferable because growth of crystal grains is suppressed.
  • the forced exhaust process does not need to be performed continuously with the controlled exhaust process.
  • a cooling process for cooling the magnet alloy after the control exhaust process may be inserted before the forced exhaust process. If a cooling process is provided, the forced exhaust process with respect to the magnet alloy after a control exhaust process can be batch-processed.
  • the magnet alloy (magnet raw material) in the cooling process is a hydride and has oxidation resistance. For this reason, it is also possible to take the magnet raw material into the atmosphere temporarily.
  • the average grain size is an aggregate of fine R 2 TM 14 B 1 type crystal of 0.01 ⁇ 1 [mu] m. Note that, even by the liquid quenching method, particles composed of an aggregate of fine R 2 TM 14 B 1 type crystals of about 0.03 ⁇ m are obtained, but these particles are isotropic. For this reason, in order to obtain a rare earth anisotropic magnet from the isotropic magnet powder, the above-described anisotropic treatment is preferably performed.
  • the magnet raw material used for the mixing step preferably has an average particle size of 3 to 200 ⁇ m.
  • the diffusion raw material preferably has an average particle size of 3 to 30 ⁇ m. If the average particle size is too small, it is uneconomical and difficult to handle. On the other hand, if the average particle size is excessive, it is difficult to uniformly mix both raw materials.
  • the use of the rare earth anisotropic magnet of the present invention is not limited and can be used for various devices. If this rare earth anisotropic magnet is used, it is possible to achieve energy saving, light weight, high performance, etc. of these devices.
  • Example 1 (Sintering method: Sample No. 1 and Sample No. C1) ⁇ Production of sample>
  • This molded object was heated up to about 800 degreeC in the inert gas atmosphere, and was heated for 0.5 hour (diffusion process). Furthermore, this was heated at 1000 degreeC for 1 hour, and the sintered compact was obtained (sintering process).
  • This sintering process is also a diffusion sintering process that also serves as a part of the diffusion process.
  • Example 2 Hot working method: Sample No. 2 and Sample No. C2
  • Example 2 Preparation of raw materials (mixing process)
  • sample no. An ingot obtained by casting the raw materials weighed to the composition shown in Fig. 2 (composition near the theory) by the button arc method was obtained.
  • a magnet alloy mother alloy
  • a liquid quenching method using a single roll. This was heat-treated at 800 ° C. for 10 minutes in an inert gas atmosphere.
  • an isotropic ribbon having a crystal grain size of 0.02 to 0.04 ⁇ m was obtained.
  • This was further pulverized by a ball mill to obtain a magnet powder having an average particle size of 100 ⁇ m. This was used as a magnet raw material.
  • the same diffusion raw material (6 mass%) as Example 1 was added to this magnet raw material, and the mixed raw material was obtained like Example 1.
  • FIG. 1 the same diffusion raw material (6 mass%) as Example 1 was added to this magnet raw material, and the mixed raw material was obtained like Example 1.
  • Example 3 Hot compression method: Sample No. 3 and Sample No. C3
  • Table 1 composition near the theory
  • magnet alloy mother alloy
  • This magnet alloy was held in an Ar gas atmosphere at 1140 ° C. for 10 hours to homogenize the structure (homogenization heat treatment step).
  • the magnet alloy after hydrogen pulverization was subjected to hydrogenation (d-HDDR) to obtain a powdered magnet raw material.
  • the hydrogenation process at this time was performed as follows.
  • the magnet alloy was put in a processing furnace and kept in a low temperature hydrogen atmosphere of room temperature ⁇ 0.1 MPa ⁇ 1 hour (low temperature hydrogenation step). Following this, the magnet alloy was held at 780 ° C. ⁇ 0.03 MPa ⁇ 30 minutes (high temperature hydrogenation step), further heated to 840 ° C. over 5 minutes, and held at 840 ° C. ⁇ 0.03 MPa ⁇ 60 minutes ( Organization stabilization process). Thus, while adjusting the reaction rate, a forward transformation that decomposes the magnet alloy into three phases ( ⁇ -Fe, RH 2 , Fe 2 B) was caused (disproportionation step). Thereafter, hydrogen is exhausted from the inside of the processing furnace and the magnet alloy is held at 840 ° C. ⁇ 1 kPa ⁇ 90 minutes to cause a reverse transformation that produces R 2 TM 14 B 1 type crystals in the magnet alloy after the forward transformation. (Control exhaust process / recombination process).
  • the magnet alloy was rapidly cooled (first cooling step). This magnet alloy was completely dehydrogenated while being kept at 840 ° C. ⁇ 30 minutes ⁇ 10 ⁇ 1 Pa or less (forced exhaust process).
  • the magnet alloy thus obtained was pulverized in an inert gas atmosphere in a mortar and then adjusted in particle size to obtain a powdered magnet raw material having an average particle size of 100 ⁇ m.
  • the same diffusion raw material (6 mass%) as Example 1 was added to this magnet raw material, and the mixed raw material was obtained like Example 1.
  • FIG. The particle diameter of the diffusion raw material powder used here was 7 ⁇ m or less.
  • the average particle diameter of the powder particles referred to in the present specification is measured by a HELOS & RODOS laser diffraction particle size distribution measuring apparatus (the same applies hereinafter).
  • the coercive force (iHc) of the magnet powder itself was 0.8 kOe (64 kA / m), and the saturation magnetization (value at 50 kOe (3979 kA / m)) was 15.2 kG (1.52 T).
  • This preform was pressed with a hot press machine at 700 ° C. (hot) ⁇ 2 ton / cm 2 ⁇ 10 seconds. Thus, a dense molded body was obtained (densification step).
  • This densification step was heated at the same temperature (700 ° C.) for 5 minutes in an inert gas atmosphere (diffusion step). The density of the dense molded body at this time was 7.5 g / cm 3 .
  • the densification step is also a diffusion densification step that also serves as part of the diffusion step.

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  • Organic Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Hard Magnetic Materials (AREA)
  • Manufacturing Cores, Coils, And Magnets (AREA)
  • Powder Metallurgy (AREA)

Abstract

L'invention porte sur un procédé pour produire un aimant anisotropique aux terres rares qui est caractérisé en ce qu'il comprend : une étape de moulage consistant à mélanger une matière première d'aimant qui peut produire des cristaux du type R2TM14B1 qui sont des cristaux d'un composé tétragonal composé d'un élément des terres rares (R), de bore (B) et d'un élément de transition (TM), avec une matière première de diffusion qui sert de source d'alimentation pour au moins un élément aux terres rares (R') et Cu pour produire une matière première mélangée, et à mouler à la presse la matière première mélangée pour produire un produit moulé ; et une étape de diffusion consistant à chauffer le produit moulé pour provoquer la diffusion d'au moins R' et Cu dans des régions superficielles ou dans les frontières des grains de cristaux des cristaux de type R2TM14B1. Dans le procédé, la matière première de diffusion qui a un point de fusion bas et une haute mouillabilité enduit les cristaux du type R2TM14B1 et, de cette façon, un aimant anisotropique aux terres rares ayant une haute coercivité peut être produit sans détériorer la magnétisation qui peut être développée intrinsèquement par la matière première de l'aimant.
PCT/JP2010/064611 2009-12-09 2010-08-27 Aimant anisotropique aux terres rares et procédé de production de cet aimant WO2011070827A1 (fr)

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CN201080055297.1A CN102640238B (zh) 2009-12-09 2010-08-27 稀土类各向异性磁铁及其制造方法
US13/514,942 US20120299675A1 (en) 2009-12-09 2010-08-27 Anisotropic rare earth magnet and method for producing the same
EP10835749.2A EP2511920B1 (fr) 2009-12-09 2010-08-27 Procédé de production d'aimant anisotropique aux terres rares
JP2011545106A JPWO2011070827A1 (ja) 2009-12-09 2010-08-27 希土類異方性磁石とその製造方法

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JPWO2011070827A1 (ja) 2013-04-22
JP5892139B2 (ja) 2016-03-23
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