WO2004088683A1 - 超小型製品用の微小、高性能希土類磁石とその製造方法 - Google Patents
超小型製品用の微小、高性能希土類磁石とその製造方法 Download PDFInfo
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- WO2004088683A1 WO2004088683A1 PCT/JP2004/002738 JP2004002738W WO2004088683A1 WO 2004088683 A1 WO2004088683 A1 WO 2004088683A1 JP 2004002738 W JP2004002738 W JP 2004002738W WO 2004088683 A1 WO2004088683 A1 WO 2004088683A1
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- Prior art keywords
- magnet
- rare earth
- metal
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- earth magnet
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- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 72
- 150000002910 rare earth metals Chemical class 0.000 title claims abstract description 68
- 238000000034 method Methods 0.000 title claims description 22
- 230000008569 process Effects 0.000 title description 3
- 229910052751 metal Inorganic materials 0.000 claims abstract description 52
- 239000002184 metal Substances 0.000 claims abstract description 52
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- 238000004544 sputter deposition Methods 0.000 claims description 31
- 238000010438 heat treatment Methods 0.000 claims description 20
- 238000004519 manufacturing process Methods 0.000 claims description 19
- 229910001172 neodymium magnet Inorganic materials 0.000 claims description 13
- 238000000227 grinding Methods 0.000 claims description 12
- 238000005498 polishing Methods 0.000 claims description 12
- 229910052771 Terbium Inorganic materials 0.000 claims description 11
- 229910052779 Neodymium Inorganic materials 0.000 claims description 9
- 229910052727 yttrium Inorganic materials 0.000 claims description 8
- 238000005520 cutting process Methods 0.000 claims description 7
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- 238000007733 ion plating Methods 0.000 claims description 5
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- 239000010419 fine particle Substances 0.000 abstract 1
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- 239000010408 film Substances 0.000 description 45
- 230000000052 comparative effect Effects 0.000 description 16
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- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910002651 NO3 Inorganic materials 0.000 description 1
- NHNBFGGVMKEFGY-UHFFFAOYSA-N Nitrate Chemical compound [O-][N+]([O-])=O NHNBFGGVMKEFGY-UHFFFAOYSA-N 0.000 description 1
- 229910052777 Praseodymium Inorganic materials 0.000 description 1
- 229910052774 Proactinium Inorganic materials 0.000 description 1
- BLRPTPMANUNPDV-UHFFFAOYSA-N Silane Chemical compound [SiH4] BLRPTPMANUNPDV-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 238000005513 bias potential Methods 0.000 description 1
- CJZGTCYPCWQAJB-UHFFFAOYSA-L calcium stearate Chemical compound [Ca+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O CJZGTCYPCWQAJB-UHFFFAOYSA-L 0.000 description 1
- 235000013539 calcium stearate Nutrition 0.000 description 1
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- 238000005229 chemical vapour deposition Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
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- 230000006866 deterioration Effects 0.000 description 1
- 238000003745 diagnosis Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
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- KBQHZAAAGSGFKK-UHFFFAOYSA-N dysprosium atom Chemical compound [Dy] KBQHZAAAGSGFKK-UHFFFAOYSA-N 0.000 description 1
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- 229910021645 metal ion Inorganic materials 0.000 description 1
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Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
- H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
- H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
- H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
- H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
- C23C14/3464—Sputtering using more than one target
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
- C23C14/3471—Introduction of auxiliary energy into the plasma
-
- 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
-
- 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
-
- 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 magnet such as an Nd—Fe—B system or a Pr—Fe—B system, and in particular, to a micro and high performance rare earth magnet for a micro product such as a micro motor and a manufacturing method thereof.
- a rare earth magnet such as an Nd—Fe—B system or a Pr—Fe—B system
- a micro and high performance rare earth magnet for a micro product such as a micro motor and a manufacturing method thereof.
- Nd-Fe-B rare earth sintered magnets are known as the most high-performance magnets among permanent magnets, such as voice coil motors (VCM) for hard disk drives and magnetic tomography (MR I). Widely used in magnetic circuits for applications. It is also known that this magnet generates a coercive force due to the microstructure of the microstructure surrounding the Nd2Fe14B main phase with a thin Nd-rich subphase surrounding the main phase, and shows a high magnetic energy product. Have been.
- Nd-Fe_B sintered magnets there has been proposed a method of removing the deteriorated layer generated by machining by mechanical polishing or chemical polishing (for example, see Patent Reference 1). Further, a method has been proposed in which a rare earth metal is applied to the surface of a ground magnet to perform diffusion heat treatment (for example, Patent Document 2). Further, there is a method of forming an SmCo film on the surface of an Nd-Fe-B magnet (for example, Patent Document 3).
- Patent Document 1 JP-A-9-1270310
- Patent Document 2 Japanese Patent Application Laid-Open No. 62-74048 (Japanese Patent Publication No. 6-63086)
- Patent Document 3 Japanese Patent Application Laid-Open No. 2001-93715 Disclosure of the Invention
- the deteriorated layer is estimated to be about 10 / im or more, so that it takes a long time to polish, a high-speed polishing causes a new deteriorated layer, and furthermore, in chemical polishing, There are problems such as that the acid solution easily remains in the pores of the sintered magnet and causes corrosion marks.
- Patent Document 2 discloses that a rare-earth metal thin film layer is formed on a deteriorated layer on a surface to be ground of a sintered magnet body and a modified layer is formed by a diffusion reaction.
- OmmX width 5mmX thickness 0.15mm (BH) max obtained is 200 k at most by merely describing the experimental results of forming a sputtered film on a thin test piece.
- m is 3.
- Nd—Fe—B series cylindrical sintered magnets with an outer diameter of about 2 mm have been widely used in mobile phone vibration motors. Since it is around 230 kj Zni 3 , it is difficult to further reduce the size without reducing the vibration intensity. Furthermore, it is even more difficult to apply high-power microminiature actuators required for microrobots and micromotors for in-vivo diagnosis in the future.
- An object of the present invention is to solve the above-mentioned problems of the prior art and to obtain a high-performance rare-earth magnet, which is particularly effective for manufacturing a small-volume rare-earth magnet and a micro motor using the same. It is intended to provide a means.
- the inventors of the present invention have conducted extensive investigations and countermeasures on the deterioration of magnetic properties due to processing damage when manufacturing micro magnets machined by cutting, drilling, grinding, polishing, etc. of sintered magnet blocks.
- the present invention provides: (1) a cylindrical or disc shape having a holed inner surface formed by cutting, drilling, and machining such as surface grinding and polishing of a magnet block material; Wherein the magnet has a surface area of Z body
- the product ratio is 2 ⁇ 1 or more and the volume is 100 mm 3 or less, and the R metal ( ⁇ ⁇ ) is placed inside the magnet at a depth equal to or more than the depth corresponding to the radius of the crystal grain exposed on the outermost surface of the magnet.
- R is one or more rare earth elements selected from Y and Nd, Dy, Pr, Ho, and Tb), and diffuses and penetrates from the magnet surface to modify the damaged parts due to the above processing.
- (BH) max having a magnetic property of 280 kJ Zm 3 or more, which is a micro, high-performance rare earth magnet for micro products.
- the present invention also provides (2) the magnet according to (1), wherein the magnet is an Nd-Fe-B system or a Pr_Fe-B system, and the R metal is Dy or Tb. Small, high performance rare earth magnets.
- the present invention provides (3) a cylindrical or disk shape having an inner surface with a hole having a damaged surface formed by machining such as cutting, drilling, and surface grinding and polishing of a magnet block;
- a cylindrical or prismatic rare earth magnet having no holes is supported in a decompression tank, and R metal or an alloy containing R metal vaporized or atomized by a physical method in the decompression tank is used.
- Y and Nd, Dy one or more of the rare earth elements selected from Pr, Ho, and Tb) are three-dimensionally scattered over all or a part of the surface of the magnet to form a film; Modifying the damaged part due to the above-mentioned processing by diffusing and permeating R metal from the magnet surface inside the magnet to a depth equal to or greater than the radius of the crystal grains exposed on the outermost surface of the magnet (1) or (2) of the small, high-performance rare earth magnet Production method is,.
- the present invention is (4) the method for producing a small, high-performance rare earth magnet according to the above (3), wherein the diffusion and infiltration are performed while forming a film.
- the present invention provides (5) a method in which the physical method comprises the steps of: Is a sputtering method that forms a film on the surface of the rare earth magnet by atomizing a plurality of targets made of an alloy containing R metal into particles by ion bombardment, or particles generated by melting and evaporating an alloy containing R metal or R metal. (3) or (4), wherein the method is a method for producing a fine, high-performance rare-earth magnet, which is an ion plating method of forming a film on the surface of the rare-earth magnet by ionization.
- the present invention also provides (6) the outer surface of the magnet by holding the rare earth magnet rotatably or tumbling in a plasma space in the middle of a target disposed to be opposed by a predetermined distance and sputtering the outer surface of the magnet.
- the present invention also provides (7) an electrode wire extending to a plasma space in the middle of an opposed target, and the electrode wire being inserted into a hole of a cylindrical or disk-shaped rare earth magnet having a holed inner surface. Then, while rotating the magnet with the electrode wire as a rotation axis, finely divided R metal or an alloy containing the R metal is made to fly to uniformly form a film on the outer surface of the magnet. (6) The method for producing a micro, high-performance rare earth magnet according to the above (6).
- the present invention also provides (8) a micro target according to (7), wherein the opposing target is a ring-shaped target disposed concentrically with the center axis direction of the cylindrical or disk-shaped magnet. And a method for producing a high-performance rare earth magnet.
- the magnet surface will be damaged and its magnetic properties deteriorate.
- one of rare earth metals selected from Y, Nd, Dy, Pr, Ho, and Tb.
- these rare earth metals are mainly Nd2FeMB.
- Phase and Nd-rich rich phase with Nd because it is the same kind of rare-earth metal as the grain boundary phase, easily reacts with the Nd-rich phase and easily repairs the parts damaged by alteration by machining. Performs the function of restoring magnetic properties.
- any of the rare earth metals increases the magnetocrystalline anisotropy of the major phase, It has the function of increasing the coercive force and restoring magnetic properties.
- T b is the crystal magnetic anisotropy at room temperature of T b 2 F ei4B substituted all N d elements of the main phase is likely a large coercive force is obtained for about three times the N d2F e 14B.
- a similar recovery function can be obtained for a Pr-Fe-B magnet.
- the depth at which the rare earth metal penetrates by the diffusion treatment is equal to or greater than the depth corresponding to the radius of the crystal grains exposed on the outermost surface of the magnet.
- the crystal grain size of Nd-Fe-B sintered magnet is about 6 to 1
- the minimum required is 3 / xm or more, which is equivalent to the radius of the crystal grains exposed on the outermost surface of the magnet. is there. Below this value, the reaction with the Nd rich phase surrounding the crystal particles becomes insufficient, and the recovery of the magnetic properties becomes small.
- the recovery of magnetic properties by surface modification is not limited to the size of the rare earth magnet, but a magnet with a smaller volume and a magnet with a larger surface area to volume ratio The effect becomes more pronounced.
- the demagnetization curve squareness of,: rectangularity) that results in a decrease in the coercive force is force s worse are obviously summer.
- the surface area Z volume magnet volume by 8 mm 3 is 3 m m-1 der Rukoto is easily calculated.
- the surface area / volume ratio is further increased, and the squareness and coercive force are significantly reduced.
- the outer diameter of the magnet mounted on a commercially available mobile phone vibration motor, the inner diameter, the length are each 2. 5 mm, l mm, 4 mm approximately, the volume of about 1 6.
- the surface area / volume ratio 2 mm- 1 or more, more preferably 3 mm- 1 or more, and a volume of approximately 1 0 O mm 3 or less, you still more 2 0 mm 3 or less of the small magnet information, particularly remarkable effects of the surface modification, with respect to (BH) ra ax is approximately 2 4 0 kj Zm 3 of N d- F e- B based magnet mounted on a commercially available vibration motor, in the present invention, 2 8 0 k J Zm 3 or more, for example, the value of Takairebe Le of 3 0 0 ⁇ 3 6 0 k J Zm 3 is obtained.
- FIG. 1 is a schematic diagram around a target of a three-dimensional sputtering apparatus that can be suitably used in the method of the present invention.
- Fig. 2 shows the samples (1) and (3) of the present invention and the sample of the comparative example.
- FIG. 3 is a graph showing a demagnetization curve of (1).
- Figure 3 is a drawing substitute photograph showing an SEM image (a: backscattered electron image, b: Dy element image) of the sample of the present invention (2) heat-treated after Dy film formation.
- FIG. 4 is a graph showing the relationship between the magnet sample size and (BH) max of the present invention and the comparative sample.
- the rare earth magnet block material used in the method of the present invention is manufactured by a hot plastic working method after sintering the raw material powder or hot pressing the raw material powder.
- the rare earth magnet block material is machined by cutting, drilling, grinding, polishing, etc. to produce cylindrical or disk-shaped micromagnets with an inner surface with holes, and cylindrical or prismatic micromagnets without holes.
- Nd—Fe—B system and Pr—Fe—B system are typical examples of alloy systems suitable for the micromagnet. Among them, Nd-Fe-B sintered magnets have the greatest magnetic properties, but their properties are greatly reduced by machining.
- the metal deposited on the magnet surface having the altered surface is composed of Y, Nd, Dy, Pr, Y, and Nd for the purpose of strengthening the restoration of rare earth metal rich phases such as Nd that constitute the magnet.
- An alloy containing a considerable amount of rare earth metals such as Dy, Pr, Ho, and Tb, for example, an Nd-Fe alloy or a Dy-Co alloy is used.
- the method of forming a film on the magnet surface is not particularly limited, and physical film forming methods such as vapor deposition, sputtering, ion plating, and laser deposition, and chemical vapor deposition such as CVD and MO-CVD. Law, and the Mesh Law are applicable. And ⁇ , in each process of deposition and heating diffusion, 10- 7 Torr or less, such Rapi to oxygen, not to desirable air from gases such as water vapor carried in the following clean atmosphere number + ppm. '
- the atmosphere in which the R metal is diffused and penetrated from the magnet surface by heating has a purity equivalent to that of a commonly available high-purity argon gas
- the gas derived from the atmosphere contained in the argon gas that is, oxygen, water vapor, carbon dioxide, Due to nitrogen or the like
- the R metal adhered to the surface during the heating of the magnet becomes an oxide, a carbide, or a nitride, and may not efficiently reach the internal structure phase. Therefore, it is desirable that the concentration of the impurity gas derived from the atmosphere contained in the atmosphere when the R metal is heated and diffused is about 50 ppm or less, and preferably about 10 ppm or less.
- a sputtering method in which metal components are formed three-dimensionally on the magnet surface from multiple targets, or An ion plating method in which a metal component is ionized and a film is formed by utilizing the electrostatic attraction and strong deposition characteristics is particularly effective.
- rare earth magnets can be held in the plasma space during the sputtering operation by holding one or more magnets rotatably with a wire or plate, or by loading a plurality of magnets into a cage made of wire mesh. It is possible to adopt a method of holding freely rolling Wear. With such a holding method, a uniform film can be formed three-dimensionally over the entire surface of the micromagnet.
- the above-mentioned rare earth metal for film formation does not recover its magnetic properties simply by being coated on the surface of the magnet, at least a part of the formed rare earth metal component diffuses to the inside of the magnet and Nd etc. Must react with the rare earth metal rich phase. Therefore, usually, a short-time heat treatment is performed at 500 to 100 ° C. after the film is formed to diffuse the film-forming metal.
- a short-time heat treatment is performed at 500 to 100 ° C. after the film is formed to diffuse the film-forming metal.
- the temperature of the magnet during film formation can be raised to the above temperature range, for example, 800 ° C. Diffusion can be performed simultaneously with film formation.
- FIG. 1 shows the concept of a three-dimensional sputtering apparatus suitable for carrying out the manufacturing method of the present invention.
- a target 1 and a target 2 made of a ring-shaped film-forming metal are arranged to face each other, and a water-cooled copper high-frequency coil 3 is arranged between them.
- An electrode wire 5 is inserted into the cylinder of the cylindrical magnet 4, and the electrode wire 5 is fixed to a rotating shaft of a motor 6 and holds the cylindrical magnet 4 so as to be rotatable.
- a method can be adopted in which a plurality of magnet products are loaded into a wire mesh basket and rolled.
- the electrode wire 5 is twisted into a fine waveform and contacts the inside of the cylinder. Since the weight of the micromagnet is about several tens of mg, there is almost no slippage between the electrode wire 5 and the cylindrical magnet 4 during rotation.
- reverse sputtering of the cylindrical magnet 4 is performed by the cathode switching switch (A). It has a mechanism that can be applied. At the time of reverse sputtering, the surface of the magnet 4 is etched by setting the magnet 4 to a negative potential through the electrode wire 5. Normally, switch to switch (B) during sputtering. Normally, during sputtering, it is common to form a sputter film without applying a potential to the electrode wire 5, but in order to control the type and film quality of the metal to be formed, a positive electrode may be applied to the magnet 4 through the electrode wire 5 in some cases. In some cases, a bias potential is applied to form a film by sputtering.
- a plasma space 7 in which Ar ions, metal particles generated from the targets 1 and 2, and metal ions are mixed is formed, and three-dimensionally from the top, bottom, left, right, front, and back of the surface of the cylindrical magnet 4 The metal particles fly and a film is formed.
- the inside of the sputtering device is returned to the atmospheric pressure and then transferred to the glove box connected to the sputtering device without contacting the atmosphere.
- a small electric furnace installed in the glove bottus is charged and heat treatment is performed to diffuse the film into the magnet.
- Alloy thin flakes having a thickness of 0.2 to 0.3 mm were produced from an ingot of Nd i2.5 F e 78.s CoiB s by strip casting. Next, put this slice in a container After filling and releasing hydrogen gas at 500 kPa at room temperature, irregular-shaped powder with a size of about 0.15 to 0.2 mm was obtained. A fine powder with a diameter of about 3 / m was produced.
- this cubic magnet block material was cut with a grindstone, outer diameter ground, and ultrasonically drilled to produce a cylindrical magnet having an outer diameter of lmm, an inner diameter of 0.3mm, and a length of 3mm.
- the sample in this state was used as a comparative sample (1).
- Dysprosium (Dy) metal was used as the target.
- a tungsten wire with a diameter of 0.2 mm was inserted as an electrode wire inside the cylinder of the cylindrical magnet.
- the size of the annular target used was 80 mm in outer diameter, 30 mm in inner diameter, and 2 Omm in thickness.
- the actual film forming operation was performed in the following procedure.
- Set by ⁇ the Tandasu Ten lines the cylindrical interior of the cylindrical magnet, after evacuating the inside of the sputtering apparatus to 5 X 10- 5 P a, 3 in the apparatus by introducing a high-purity Ar gas P a Maintained.
- the cathode switch was set to the (A) side, RF output 20W and DC output 2W were applied, and reverse sputtering was performed for 10 minutes to remove the oxide film on the magnet surface.
- the switch was set to the (B) side, RF output 80W and DC output 120W were added, and normal sputtering was performed for 6 minutes.
- the obtained film-forming magnet is transferred to a glove box connected to the sputtering apparatus without contacting the atmosphere, and loaded into a small electric furnace also installed in the glove box.
- the first stage was subjected to a heat treatment at 700 to 850 ° C for 10 minutes, and the second stage was subjected to a heat treatment at 600 ° C for 30 minutes. These were designated as Samples (1) to (4) of the present invention.
- the purified Ar gas was circulated in the glove box to keep the oxygen concentration at 2 p or less and the dew point at 175 ° C or less.
- Table 1 shows the magnetic properties of each sample
- FIG. 2 shows the demagnetization curves of the comparative sample (1) and the samples (1) and (3) of the present invention.
- the Dy film was observed for the sample after the above measurement.
- the material (1) of the present invention was embedded in a resin, polished, lightly etched with alcohol nitrate, and observed with an optical microscope at 500 ⁇ magnification. As a result, it was found that a film of about 2 ⁇ was formed uniformly on the entire outer periphery of the sample.
- the internal structure of the magnet was observed using an analytical scanning electron microscope.
- the surface of the sample had a different structure from the interior due to Dy deposition and subsequent heat treatment.
- the Dy element image in Fig. 3 (b) shows that the Dy element diffuses and penetrates into the sample at the same time as the high concentration of Dy exists in the surface layer, and the diffusion depth is approximately 10%. ⁇ . It is presumed that the high-density Dy spot in the center of the image was partially transferred from the surface layer peeled off during polishing.
- Metals of Nd, Dy, Pr, Tb, and A1 were formed on the cylindrical magnet having an outer diameter of 1 mm, an inner diameter of 3 mm, and a length of 3 mm manufactured in Example 1.
- the target dimensions of Nd and A1 are the same as Dy of Example 1, with an outer diameter of 8 Omm
- the diameter of the target was 3 Omm
- the thickness was 2 Omm
- the Pr and Tb targets were manufactured by attaching and fixing each metal of 2 mm thickness only on the surface of the A1 target facing the sample.
- the comparative sample (1) is listed again from Table 1, and the comparative sample (3) is a sample that has not been heat-treated with Nd deposited.
- Table 2 shows the magnetic properties of the obtained magnet samples. As is clear from Table 2, when the deposited metal is A1, the magnetic properties are almost the same as those of the comparative sample (1) having no metal film, and the effect of surface modification is not seen. In Comparative sample (3), no diffusion layer was formed because no diffusion heat treatment was performed, and no recovery of magnetic properties was observed. On the other hand, in each of the samples of the present invention, the coercive force Hcj and the maximum energy product B Hmax recovered significantly.
- a sintered magnet block of N di2Dy2.5F e76.5C ⁇ ⁇ 8 composition was cut, ground and drilled to produce a disk-shaped magnet with an outer diameter of 10 mm, an inner diameter of 3 mm and a length of 1.4 mm.
- Volume 100 mm 3 the surface area 200 mm2, the ratio of surface area / volume 2. 0 mm - 1.
- Tb films were formed on the front and back surfaces.
- the sputtering conditions were as follows: RF output 40 W and DC output 2 W were applied, reverse sputtering was performed for 10 minutes, and DC output was varied up to 100 800 W as RF output 150 W to produce magnets with different sputtering conditions.
- the thickness of the Tb film formed here was determined after examining the relationship between the DC output and the film thickness in advance, and was set to 20 minutes at 100 W and 5 minutes at 800 W.
- the sputtering time was controlled so as to be about 3 ⁇ .
- the thermal diffusion of Tb metal was intended by increasing the temperature of the magnet sample during film formation without performing diffusion heat treatment after film formation.
- the sample temperature during film formation increased with an increase in the DC output, and red heat of the sample was observed when the DC output was 600 W.
- the temperature at that time was estimated to be about 700 ° C.
- the diffusion depth of Tb metal was measured from the distribution of the Tb element image from the magnet sample surface using an analytical scanning electron microscope with each sample embedded after the measurement of the magnetic properties.
- Table 3 shows the magnetic properties of the obtained magnet samples. As is evident from Table 3, sample heating occurs as the DC output increases, and in the present invention samples (9) to (13) having a diffusion depth t of 3 ⁇ or more, 287 kj / m 3 (approximately 3 6MGO e) High energy product was obtained. On the other hand, the comparative samples (4) to (6), which are presumed to be insufficiently heated, have low values because the diffusion of Tb metal into the magnet is hardly observed. As described above, by appropriately selecting the sputtering conditions, the diffusion of Tb metal into the magnet can be performed simultaneously with the film formation, and the subsequent heat treatment step can be omitted.
- a disc-shaped sintered magnet having an outer diameter of 5.2 mm, an inner diameter of 1.9 mm, and a thickness of 3 mm was manufactured from an alloy having a composition of Nd 12.5 Fe 78.5 Coi B 8 in the same process as in Example 1. .
- the outer diameter is 5 mm
- the inner diameter is 2 mm
- the thickness is 0.1 mm, 0.2 mm, 0.5 mm, 0.8 mm 1 .2 mm, 1.
- 8111111 disk-shaped magnets of various dimensions were obtained.
- the volume is about 2111111 3 to 30111111 3
- the ratio of surface area Z volume is about 21 mm- 1 to 2 mm_i.
- this sample was loaded into a small electric furnace inside a glove box, and the first stage was subjected to a diffusion heat treatment at 850 ° C for 10 minutes, and the second stage was subjected to a diffusion heat treatment at 550 ° C for 60 minutes.
- a sample of the present invention (19) having a thickness of 1.8 mm was obtained from the sample of the present invention (14) having a thickness of 1 mm.
- the magnets after the grinding were designated as Comparative Example Samples (7) to (12) in order of thickness.
- Figure 4 shows the results of the magnetic properties (BH) max when the thickness, surface area ratio, and volume of these samples were used as parameters. From FIG.
- a rare-earth metal is formed and diffused on a magnet surface that has been damaged and damaged by machining, thereby repairing the magnet surface layer that has been damaged and damaged by machining such as cutting, drilling, grinding, and polishing, and improving magnetic properties. It can be greatly recovered. As a result, it contributes to the realization of ultra-compact, high-output motors using small, high-performance magnets.
Abstract
Description
Claims
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US10/551,432 US7402226B2 (en) | 2003-03-31 | 2004-03-04 | Minute high-performance rare earth magnet for micromini product and process for producing the same |
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JP2003096866A JP3897724B2 (ja) | 2003-03-31 | 2003-03-31 | 超小型製品用の微小、高性能焼結希土類磁石の製造方法 |
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Cited By (5)
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US20130189426A1 (en) * | 2006-09-15 | 2013-07-25 | Intermetallics Co., Ltd. | Method for producing sintered ndfeb magnet |
CN101853725B (zh) * | 2009-04-03 | 2012-04-25 | 中国科学院宁波材料技术与工程研究所 | 烧结钕铁硼永磁材料的制备方法 |
CN102005277A (zh) * | 2010-09-30 | 2011-04-06 | 广州金南磁性材料有限公司 | 一种应力场取向各向异性可挠性粘结钕铁硼磁体及其制备方法 |
CN111524670A (zh) * | 2019-02-01 | 2020-08-11 | 天津三环乐喜新材料有限公司 | 稀土扩散磁体的制备方法及稀土扩散磁体 |
CN111524670B (zh) * | 2019-02-01 | 2022-04-12 | 天津三环乐喜新材料有限公司 | 稀土扩散磁体的制备方法及稀土扩散磁体 |
Also Published As
Publication number | Publication date |
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US7402226B2 (en) | 2008-07-22 |
US20060278517A1 (en) | 2006-12-14 |
JP2004304038A (ja) | 2004-10-28 |
JP3897724B2 (ja) | 2007-03-28 |
CN1764990A (zh) | 2006-04-26 |
CN100394520C (zh) | 2008-06-11 |
TW200421358A (en) | 2004-10-16 |
TWI239536B (en) | 2005-09-11 |
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