WO2006004014A1 - 磁気異方性希土類焼結磁石の製造方法及び製造装置 - Google Patents
磁気異方性希土類焼結磁石の製造方法及び製造装置 Download PDFInfo
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- WO2006004014A1 WO2006004014A1 PCT/JP2005/012123 JP2005012123W WO2006004014A1 WO 2006004014 A1 WO2006004014 A1 WO 2006004014A1 JP 2005012123 W JP2005012123 W JP 2005012123W WO 2006004014 A1 WO2006004014 A1 WO 2006004014A1
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
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- 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
- H01F41/0206—Manufacturing of magnetic cores by mechanical means
- H01F41/0246—Manufacturing of magnetic circuits by moulding or by pressing powder
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1017—Multiple heating or additional steps
- B22F3/1021—Removal of binder or filler
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
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- 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
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- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
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- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
- H01F1/0555—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together
- H01F1/0557—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together sintered
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
- H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
- H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
- H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
- H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered
Definitions
- the present invention relates to a method for manufacturing a high performance rare earth magnet and an apparatus for manufacturing the same.
- ReB magnets Rare earth * iron * boron-based sintered magnets
- Main applications include computer HDD (hard 'disk' drive) magnetic head drive motor VCM (voice coil motor), high-end speakers, headphones, motor-assisted bicycles, golf carts, permanent magnet magnetic resonance diagnostic equipment (MRI) Etc.
- MRI magnetic resonance diagnostic equipment
- the RFeB magnet was discovered by the present inventors in 1982 (Patent Document 1).
- This RFeB magnet is mainly composed of R Fe B intermetallic compound with tetragonal crystal structure and magnetic anisotropy.
- RFeB sintered magnets are manufactured through the steps of composition blending, melting, forging, grinding, compression molding in a magnetic field, sintering, and heat treatment.
- additive elements Patent No. 1606420, etc.
- heat treatment Patent No. 1818977, etc.
- crystal grain size control Patent No. 1662257, etc.
- Dy, Tb Rare earth elements
- Sintered magnets require a dense and uniform microstructure.
- a method of forging and finely pulverizing molten alloy for example, Patent No. 1431617 was common. If the molten alloy is rapidly cooled by the strip casting method, the appearance of ⁇ -iron is suppressed, and a high energy product can be obtained by reducing the amount of non-magnetic rare earth elements (Patent No. 2665590, JP 2002-2002). 208509).
- the method of obtaining magnetically anisotropic sintered magnets by compression molding powder in a magnetic field originated from the invention of ferrite magnets (Japanese Patent Publication No. 29-885, US Pat. No. 2,762,778), and then RCo magnets and RFeB magnets. (US Pat. No. 3,684,593, Patent No. 1431617). Fine powder is formed with the c-axis of the RFeB tetragonal crystal structure aligned in one direction.
- the die press method is common, but there are CIP method (Patent No. 3383448) and RIP method (Patent No. 2030923, etc.) as a method for obtaining a higher degree of orientation and higher energy product.
- Patent No. 2731337 In order to achieve high orientation while preventing oxidation of fine powder, there is a method in which a mixture of mineral oil, synthetic oil or plant oil and fine powder is injected into a mold at high pressure and wet compression molded in a magnetic field. In this case, there is a report that high magnetic properties can be obtained by pressurizing and filling the slurry (Patent No. 2859517).
- the mold molding method cannot apply pressure from one direction and this is the cause of disturbing orientation. If pressure can be applied isotropically from all directions, the disorder of orientation becomes small.
- the method of applying pressure isotropically is to place fine powder in a rubber container, apply a magnetic field from the outside, and perform cold isostatic pressing (CIP) (Patent No. 3383448). .
- Air tapping is a technique in which a high-speed airflow is intermittently applied to a powder to uniformly and uniformly fill the powder with a die cavity.
- a method of solidifying by using an air tapping method to obtain a molded product of Yournet shave has been proposed (Japanese Patent Laid-Open No. 2000-96104).
- the c-axis direction of the tetragonal structure corresponds to the easy magnetization axis. Oriented in the direction.
- a static magnetic field is applied by an electromagnet, and its magnitude is about 15 kOe at maximum.
- a strong magnetic field of 15 to 55 kOe can be applied in a pulsed magnetic field using an air-core coil, and the magnetic properties are improved by actually applying a high magnetic field (Japanese Patent No. 3307418).
- Patent Document 1 Patent No. 1431617
- the powder metallurgy (sintering) method provides a dense and uniform microstructure. In rare earth cobalt magnets and RFeB magnets, there is no better method than powder metallurgy to obtain high performance permanent magnets by taking advantage of the characteristics of each material.
- ferrite magnets were invented by Went et al. (Japanese Patent Publication No. 35-8281, US Pat. No. 2,762,777).
- the first magnetically anisotropic sintered ferrite magnets were first developed by Golter et al. (Japanese Patent Publication No. 29-885, US Pat. No. 2,762,778). It is said that the purpose of compression molding is to squeeze out the liquid component by compression and to fix the oriented particles. Further, compression molding is considered preferable for obtaining a desired shape. There is an example of heating together with a container in a magnetic field without compression molding, but the density and magnetic properties are low compared to the example of compression molding.
- the present inventors previously proposed the RIP method as a method for obtaining the same effect as CIP (Japanese Patent No. 2030923).
- RIP a fine powder is placed in a rubber mold, a pulse magnetic field is applied, and the entire rubber mold is pressurized with a die press.
- pressure is applied isotropically and a pulsed magnetic field can be used, so the magnetic properties are higher than with the die press method.
- This method is suitable for mass production because it can automate the process of rubber mold filling, pulse magnetic field application, compression molding, and demagnetization continuously.
- 'Fine powder is fed into the mold through the feeder.
- the lower punch is raised (or the die is lowered), and the green compact is pushed out onto the mold.
- the 'robot' arm carries the green compact to the conveyor.
- the green compacts are arranged at intervals in order to avoid collision and welding.
- the green compact may be stored for several days.
- the die press used in powder metallurgy is a precision machine, and if it is a single-piece (single-piece) press, the alignment of punch and dies is relatively easy. is there. Magnets are required to have various shapes and dimensions, such as discs, rectangles, perforated discs, bows, etc. Work is required.
- i'h e pressing pressure should be sufficient to give the powder compact enough mechani cal strength to withstand handling, but not nigh enough to cause particle misorientat ion. " The force S to be applied is high enough to cause disturbance of the particle orientation. In any document, it is recognized that the orientation will be disturbed if the pressure is applied with a large pressure, and the green compact has sufficient strength for handling. It is recognized that it needs to be compressed strongly in order to have it.
- Rare earth magnets contain about 30% by weight of chemically active and easily oxidized rare earth elements.
- the rare earth sintered magnet manufacturing process there is a process for handling fine powders containing a large amount of chemically active rare earth elements and having an average particle size of about 3 ⁇ m. Since it is necessary to orient each of these fine powders in a certain direction in a magnetic field, it is not possible to use means for improving the fluidity of the powder by granulating in advance, as used in general powder metallurgy. Since the fine powder is bulky and each powder has the properties of a magnet, even if the powder is supplied into the mold cavity, a bridge is formed and uniform filling is difficult.
- Some liquid lubricants are excellent in volatility and hardly remain in the sintered body. However, if a large amount of lubricant is added for the purpose of improving the degree of orientation, the green compact strength after die pressing becomes weak, which causes handling problems.
- a static magnetic field is applied by an electromagnet.
- the static magnetic field generated by the electromagnet is at most 10-15 kOe (1-1.5 T) due to the saturation of the magnetic flux by the iron core.
- Oils that evaporate easily and do not remain have been studied, but it is difficult to remove the carbon trapped in the compacted green compact. It is necessary to degrease the oil at a temperature at which it does not react with the rare earth, but for this purpose, it must be kept at a relatively low temperature for a long time, and the mass production efficiency is significantly deteriorated. If degreasing is not performed sufficiently, it will easily react with rare earth elements at high temperatures, deteriorating magnetic properties and deteriorating corrosion resistance.
- the green compact is fragile and easily broken. It is dangerous and inefficient to work with a human hand in the press, like a glove box. In other words, if the entire process including the die press is placed in an inert atmosphere, it is extremely difficult to make the concept successful in mass production.
- the crystal grain size of RFeB sintered magnets used for mass production is the D value, which is the median value of the particle size measured by a laser powder particle size distribution measuring device. It is said to be 5-6 ⁇ . D measurement
- the single domain particle size of the product is even smaller (0.2-5 ⁇ ). Therefore, even in the case of a sintered magnet, a higher coercive force can be expected with a smaller crystal grain size.
- the coercive force rapidly decreases as the particle size decreases. This indicates that oxidation is inevitable in the conventional process for handling fine powder.
- RFeB alloy fines containing chemically active rare earth elements are highly oxidizable and may ignite if left in the atmosphere. The smaller the powder particle size, the greater the risk of ignition. Even if it does not ignite, it oxidizes easily and exists as a non-magnetic oxide in the sintered magnet, which causes a decrease in magnetic properties.
- the first problem of the RFeB-based sintered magnet manufacturing method and manufacturing apparatus is that it is difficult to make the manufacturing line completely sealed. It is known that RFeB-based sintered magnets can be improved in properties as the oxidation of the powder and green compact during the manufacturing process is kept as low as possible and the particle size of the powder is reduced. However, the less the surface layer is oxidized, the smaller the powder particle size, the more active the powder, and the production line must always be filled with an inert gas such as N. When air enters even a little, the powder generates heat. In the mass production line, the amount of powder is large, so there is a concern about small heat generation to large heat generation and fire power.
- the powder compact must be taken out of the mold or rubber mold after being compressed.
- the green compact breaks, chip, or sucks excess powder, causing trouble.
- Troubles caused by cracking or chipping of the green compact also occur during the subsequent green compact handling process. Since such a trouble cannot be handled by a robot, air is introduced into the system and the countermeasure is performed manually.
- the conventional production line can temporarily produce RF eB anisotropic sintered magnets in a closed system, but continuous operation for a long time is extremely difficult. Handling powder is actually dangerous as well as being rejected by the production site.
- the RFeB anisotropic sintered magnet production method using the conventional die press method and RIP method is inappropriate as a process for handling active powder, and as a mass-produced product, this
- the powder used in the conventional production system has a median particle size distribution represented by D of 5 in the production of the world's top-level RFeB magnets. It was about am.
- Another problem in the production method of RFeB-based anisotropic sintered magnets is that productivity of flat plate and arcuate plate magnets is low. Of all RFeB anisotropic sintered magnets, the ratio of flat plate and arcuate plate magnets is extremely high. In these magnets, the magnetization direction is perpendicular to the plate surface.
- One of the methods for producing a flat magnet by a conventional method is a method in which a large block-shaped sintered body is sliced with an outer cutter.
- the disadvantage of this method is that some of the expensive sintered body after sintering becomes chipped, and the proportion increases as the thickness of the product decreases.
- Another problem is that machining (cutting) takes time and tool wear is large.
- Another method for producing a plate-shaped magnet by a conventional method is a method in which a compact is formed by pressing in a magnetic field for each sentence by a die pressing method, and sintered separately for each sentence. .
- the disadvantage of this method is that it must use the parallel magnetic field press method for forming the flat magnet.
- the parallel magnetic field press method the orientation of the powder is disturbed during compression, and the maximum energy product of the magnet produced by sintering is lower by about lOMGOe than the pressed product in a perpendicular magnetic field.
- the method of pressing and sintering flat magnets one by one is low in productivity.
- This method has the same problem as the above-described flat magnet. In other words, since the orientation of the magnet after sintering is low, the maximum energy product of the magnet is low, and even if a method of molding one by one or a multi-cavity molding method using a plurality of die cavities is used. This means that the productivity of the process up to sintering is low.
- Another disadvantage of the conventional production method is that it is impossible to produce a sintered body of a long object having a circular or irregular cross section.
- the problem is that the length (height) of the green compact that can be molded is limited and the maximum energy volume of the magnet is low when using the press method in a parallel magnetic field.
- the cross-sectional shape of the green compact that can be molded there is a restriction on the cross-sectional shape of the green compact that can be molded, and it is not possible to form a two-nave.
- a disadvantage of the conventional production method is that it is difficult to produce a flat ring magnet having high characteristics.
- a flat ring magnet is used by being magnetized in a direction perpendicular to the disk surface.
- a parallel magnetic field press method is used, but this method can only produce a product whose maximum energy product is lower by about 1 LOMGOe than a magnet made by a perpendicular magnetic field press method.
- the RIP method was expected to have high performance as a production method for flat ring magnets, but flat ring magnets were not produced by the RIP method due to problems such as distortion of the shape during molding.
- Another problem of the conventional method is that a thin plate-like magnet with a thickness of 1 mm or less, a deformed cross-section long product with a side or diameter of 1 mm or less, and a sintered magnet with a circular cross-section long product are used. In other words, it cannot be directly produced by sintering a green compact having such a small size. The reason for this is that it is difficult to produce a compact with such a small size by means of a die press or the RIP method. This is because it is difficult to handle so that it does not break when placed on a plate, packed in a box, or charged into a sintering furnace.
- Metal injection molding (MIM) is known as one of the possible methods, but due to problems such as residual carbon impurities, it is not often used in the production of RFeB anisotropic sintered magnets.
- An object of the present invention is to provide a manufacturing method and a manufacturing apparatus for magnetic anisotropic rare earth sintered magnets, and a basic method for manufacturing and manufacturing sintered magnets including the current die press method and RIP method.
- a high-density, high-orientation sintered body has a density of 97% or more of the theoretical density, and the degree of orientation depends on the saturation magnetization J of the residual magnetization J when measured by a pulse magnetization measurement method with a maximum applied magnetic field of 10T.
- the ratio J / J force is 3 ⁇ 43% or more.
- the second aspect of the production method according to the present invention is:
- the packing density of the alloy powder in the mold is 35 to 60% of the true density of the alloy as in the first or second aspect. It is characterized by that.
- the packing density of the powder is about 20% of the theoretical density.
- a fourth aspect of the production method according to the present invention is characterized in that, in the third aspect, the packing density is 40 to 55% of the true density.
- a fifth aspect of the manufacturing method according to the present invention is characterized in that in any one of the first to fourth aspects, the orientation magnetic field is 2T or more.
- the degree of orientation of the sintered magnet J / J force 3% or more, so the orientation magnetic field must be at least 2T.
- a sixth aspect of the production method according to the present invention is characterized in that, in the fifth aspect, the orientation magnetic field is 3T or more. Gives more preferred orientation and range of orientation magnetic field.
- a seventh aspect of the manufacturing method according to the present invention is characterized in that, in the sixth aspect, the orientation magnetic field is 5T or more. This gives a more preferred range of orientation magnetic field.
- An eighth aspect of the manufacturing method according to the present invention is characterized in that, in any of the fifth to seventh aspects, the orientation magnetic field is a pulse magnetic field.
- a ninth aspect of the manufacturing method according to the present invention is characterized in that, in the eighth aspect, the orientation magnetic field is an alternating magnetic field.
- a tenth aspect of a manufacturing method according to the present invention is characterized in that, in any of the fifth to ninth aspects, an orientation magnetic field is applied a plurality of times.
- An eleventh aspect of the manufacturing method according to the present invention is characterized in that, in the tenth aspect, the orientation magnetic field is a combination of a DC magnetic field and an alternating magnetic field.
- a lubricant is added to the alloy powder.
- a thirteenth aspect of the production method according to the present invention is characterized in that, in the twelfth aspect, the lubricant is a solid lubricant, a liquid lubricant, or both.
- the liquid lubricant is mainly composed of a fatty acid ester or a depolymerized polymer.
- the sixth to fourteenth aspects provide means for improving the degree of orientation.
- a fifteenth aspect of the production method according to the present invention is characterized in that, in any one of the first to fourteenth aspects, the particle diameter of the alloy powder is 4 ⁇ m or less.
- the sixteenth aspect of the production method according to the present invention is characterized in that, in the fifteenth aspect, the particle size of the alloy powder is not more than 1 / m. This makes it possible to produce magnets with even higher characteristics than in the fifteenth aspect.
- a seventeenth aspect of the production method according to the present invention is characterized in that, in the sixteenth aspect, the particle diameter force / m or less of the alloy powder is not more than one. This makes it possible to produce magnets with even higher characteristics than in the sixteenth aspect.
- An eighteenth aspect of the production method according to the present invention is characterized in that, in the seventeenth aspect, the particle size force of the alloy powder is not more than zm. This makes it possible to produce magnets with even higher characteristics than in the seventeenth aspect.
- the alloy powder has a particle size of 3 ⁇ m or less and a sintering temperature of 1030 ° C or less. It is characterized by being.
- a twentieth aspect of the production method according to the present invention is characterized in that, in the nineteenth aspect, the particle size of the alloy powder is not more than 3 ⁇ 4 ⁇ m and the sintering temperature is not more than 1010 ° C. . This further improves the properties of the RFe B sintered magnet from the nineteenth aspect and further improves the mold life.
- a part or all of the mold is used a plurality of times.
- the mold has a plurality of cavities.
- a twenty-third aspect of the manufacturing method according to the present invention is characterized in that, in any of the first to twenty-second aspects, the cavity is columnar.
- a twenty-fourth aspect of the manufacturing method according to the present invention is characterized in that, in any one of the first to twenty-third aspects, a columnar core is disposed at the center of the cylindrical cavity.
- the alloy powder is filled in the cavity and oriented by applying a magnetic field, and then the core of the mold is removed, or the mold The core is replaced with a thin one and sintered.
- the twenty-fourth and twenty-fifth aspects enable the production of cylindrical ring-shaped magnets having the same characteristics as a press product in a perpendicular magnetic field, which was impossible with the conventional method.
- a twenty-sixth aspect of the production method according to the present invention is any of the twenty-third to the twenty-fifth aspects.
- the magnetic powder is applied in the direction of the main axis of the cavity to orient the alloy powder.
- a twenty-seventh aspect of the manufacturing method according to the present invention is characterized in that, in the twenty-sixth aspect, a material corresponding to a lid and a bottom at both ends of the cavity in the principal axis direction is made of a ferromagnetic material.
- the twenty-sixth and twenty-seventh aspects provide means for obtaining a columnar or cylindrical sintered body with as little distortion as possible.
- a twenty-eighth aspect of the production method according to the present invention is characterized in that, in the twenty-second aspect, the cavity is flat. This provides a high productivity production method for flat magnets.
- a twenty-ninth aspect of the production method according to the present invention is characterized in that, in the twenty-second aspect, the cavity has an arcuate plate shape. This provides a high productivity production method for arcuate plate magnets.
- a thirtieth aspect of the manufacturing method according to the present invention is the same as that of the twenty-eighth or twenty-ninth aspect. It is characterized in that the alloy powder is oriented by applying a magnetic field in a direction perpendicular to the flat plate or arcuate plate.
- the material of the portion forming the hollow flat plate surface or the arcuate plate surface is a non-magnetic material or has a saturation magnetization of 1.5 T or less. It is characterized by that.
- the saturation magnetization is 1
- the thirtieth to thirty-second embodiments provide means for obtaining a high-density sintered body without a nest when producing a flat plate or arcuate plate magnet.
- a thirty-third aspect of the production method according to the present invention is any of the twenty-second to thirty-second aspects.
- the mold is characterized in that a plurality of cavities are arranged in two or more rows.
- a thirty-fourth aspect of the production method according to the present invention is the process according to any one of the first to thirty-third aspects, wherein one of the parts constituting the wall parallel to the magnetic field orientation direction of the alloy powder among the parts of the mold. Part or whole is a ferromagnetic material.
- a thirty-fifth aspect of the production method according to the present invention is characterized in that in any one of the first to thirty-fourth aspects, an anti-seizure coating is applied to the inner wall of the cavity.
- a mechanical tapping method using mechanical vibration in any of the first to thirty-fifth aspects, a mechanical tapping method using mechanical vibration, a pusher method by pushing a push rod, or The mold is forcibly filled with alloy powder by an air tapping method using a gas flow impact or a combination thereof.
- a fine powder obtained by pulverizing an alloy obtained by a molten metal quenching method is used as the alloy powder. And features.
- the first aspect of the magnetic anisotropic rare earth sintered magnet manufacturing apparatus according to the present invention is:
- an alloy powder filling means for densely filling an alloy powder obtained by finely pulverizing an alloy into a mold; b) an orientation means in a magnetic field for orienting the alloy powder in a magnetic field;
- an atmosphere adjusting means for making the inside of the container an inert gas atmosphere or a vacuum.
- the second aspect of the magnetic anisotropic rare earth sintered magnet manufacturing apparatus according to the present invention is:
- an alloy powder filling means for densely filling an alloy powder obtained by finely pulverizing an alloy into a mold; b) an orientation means in a magnetic field for orienting the alloy powder in a magnetic field;
- pre-sintering means for pre-sintering the alloy powder as it is in the mold
- main-sintering means for main-sintering the pre-sintered alloy powder
- atmosphere adjusting means for making the inside of the container an inert gas atmosphere or a vacuum.
- This provides a means to increase the safety of the apparatus embodying the present invention.
- a third aspect of the production apparatus according to the present invention is characterized by comprising an external container for housing the container. This provides a means to further increase the safety of the apparatus implementing the present invention.
- a fine mold powder is filled in a cavity mold, and a magnetic field is applied from an external force to align the powder, followed by sintering as it is.
- the shape and dimensions of the cavity are designed according to the desired shape and dimensions of the product. In that case, it is desirable to design in consideration of shrinkage during sintering.
- the production method of the present invention is applied to the production of RCo (rare earth cobalt) magnets and RFeB (rare earth ⁇ iron′boron) magnets.
- the process according to the present invention is applied to a rare earth magnet such as an RFeB magnet or an SmCo magnet, there is no opportunity to come into contact with oxygen in the atmosphere in the form of fine powder, so that oxygen in the sintered body can be reduced.
- the amount of rare earth (Nd, Sm) can be reduced to the limit, and high magnetic properties can be obtained.
- high orientation is maintained and high B and high energy products are realized.
- sintering in the case of the first embodiment
- pre-sintering in the case of the second embodiment
- the mold has a deaeration opening, pores, slits or grooves formed during sintering or preliminary sintering.
- deaeration openings and the like may be formed from the beginning, but may be formed after the filling of the alloy powder and the orientation in the magnetic field.
- the powder may contain a large amount of hydrogen absorbed in the alloy at the time of hydrogen cracking, and there are always adsorbed gas components such as nitrogen and moisture.
- the lubricant and binder mixed in the fine powder vaporize at high temperatures.
- These gaseous components must be discharged out of the mold during sintering or pre-sintering. If these gas components remain sealed in the mold, the density of the sintered body will not increase during sintering, or the sintered body will react and contaminate with these gas components, adversely affecting the magnetic properties.
- the core (the 24th or 25th embodiment) may be removed to form the opening. Note that the above-described gaps and pores may be naturally formed gaps such as fitting between the cavity and its lid.
- a mold having a cavity that is predetermined based on a desired size and shape is obtained. After filling the fine powder and applying the magnetic field from the outside to orient the powder, it can be sintered or pre-sintered as it is.
- the magnetic alloy fine powder is filled in the mold at a high density.
- the degree of high-density filling is lower than the relative density of compression molded bodies in the conventional mold press method, CIP method, and RIP method, which is higher than the degree of filling in the conventional die press method.
- the force that required a strong green compact strength for green compact handling in the conventional method In the present invention, since there is no green compact handling step, there is no need to compress.
- the alloy powder must be filled in the mold sufficiently densely and uniformly. Otherwise, the density of the sintered body will decrease, or powder will be biased during the orientation of the pulsed magnetic field, and a nest will be formed in the sintered body.
- the rare earth magnet of the present invention is preferably an RFeB magnet.
- RFeB magnets are in atomic percentage, R (R is at least one of rare earth elements including Y): 12
- W, Mn, Al, Sn, Zr, Hf, Ga, etc. may be added. These additive elements may be added in combination, but in any case, the total amount is preferably 6 atomic% or less.
- the total amount is preferably 6 atomic% or less.
- sintering is performed between 900 and 1200 ° C.
- the method for producing a rare earth magnet of the present invention can also be applied to a rare earth cobalt magnet (RCo magnet).
- RCo magnet rare earth cobalt magnet
- the composition range of type 1-5 magnet is RTx (R is Sm or Sm and one or more of La, Ce, Pr, Nd, Y, Gd, T is Co or Co.
- R is Sm or Sm and one or more of La, Ce, Pr, Nd, Y, Gd, T is Co or Co.
- Mn, Fe, Cu, and Ni, 3.6 ⁇ x ⁇ 7.5 is 1050-1200 ° C.
- composition range of the 2-17 type RCo magnet is R (where R is Sm or two or more rare earth elements containing 50% by weight or more of Sm): 20 to 30% by weight, Fe: 10 to 45% by weight, Cu : l ⁇ 10wt%, Zr, Nb, Hf, V
- R is Sm or two or more rare earth elements containing 50% by weight or more of Sm
- Fe 10 to 45% by weight
- Cu : l ⁇ 10wt%
- One or more of: 0.5-5% by weight, balance Co and inevitable impurities, sintering temperature is 1050-1250 ° C.
- the coercive force can be increased by heat treatment at 900 ° C or lower during sintering.
- the optimum sintering temperature can be defined as the sintering temperature at which the sintering density can be made sufficiently high and no grain growth occurs.
- the optimum sintering temperature depends on the magnet composition, powder particle size, sintering time, and the like.
- pre-sintering is performed until a part of the powder is bonded and the shape can be preserved.
- the pre-sintering temperature should be 500 ° C or higher.
- the temperature of pre-sintering should be 30 ° C lower than the optimum sintering temperature. This is because, at the optimum sintering temperature, the filled powder is highly reactive and tends to have a strong seizure to the mold.
- RFeB magnets and RCo magnets have a higher stoichiometric composition than intermetallic compounds (R Fe B and RCo).
- One of the features of the present invention is to use a mold having a cavity designed so that a sintered magnet having a desired shape and size is obtained after sintering, and repeatedly using the mold. is there.
- Rare earth sintered magnets are often produced in units of 1 million pieces per product. This is an essential requirement for industrial technology.
- the present inventor has demonstrated that repeated use of the mold is industrially possible when the proposed technique satisfies certain conditions.
- the present invention in order to realize higher productivity, it is proposed to use a mold having a large number of cavities.
- the overwhelming advantage compared to the conventional mold press method and RIP method is that the number of flat magnets and arcuate plate magnets that can be manufactured with one mold is many times larger. The characteristics of the magnets made in this way are extremely uniform with little variation among the magnet pieces. This is because in the present invention, a very long air-core coil can be used for the orientation of the alloy powder. For example, if a bitter type coil is used as the coin and the length of the coil is 20 cm, 30 typical rare earth sintered magnets having a flat plate shape or an arcuate plate shape can be manufactured with one mold.
- the magnetic field in the coil is uniform, the magnetic properties of the flat or arcuate plate magnets produced in this way are uniform with almost no variation from piece to piece.
- the reason why the bitter type coil is used is that this type of coil has a long life as a coil that repeatedly generates a high magnetic field as compared with a normal winding type coil.
- the selection of the material constituting the mold is important for using the present invention as an industrial technology.
- an iron mold when used as a mold for a flat magnet, when a pulse magnetic field is applied, the alloy powder in the mold is pressed against the outer periphery of the flat plate and sintered as it is.
- a sintered body with a large nest can be formed.
- the parts other than this nest are high-density and highly oriented sintered bodies. It is natural that such a magnet is not suitable as an industrial material.
- Select the material of the mold appropriately, that is, use a non-magnetic material for the part that forms the flat plate surface or the arcuate plate surface of the cavity, or the saturation magnetization of 1.5T or less, more preferably 1.3T or less. By using low materials, these problems can be solved.
- the orientation of the alloy powder after the magnetic field orientation becomes a magnetic circuit. Fixed and stabilized. As a result, even if some impact force is applied to the mold during handling of the mold after magnetic field orientation, the orientation is not disturbed. Speed up and stable production.
- the cavity has a columnar shape or a cylindrical ring shape, it is desirable to use a ferromagnetic material for the lid and the bottom portions at both ends of the cavity in the main axis direction (depth direction). By doing so, the orientation of the alloy powder after the magnetic field orientation is kept stable.
- BN (boron nitride) coating is an effective coating for preventing seizure.
- BN coating Even the mechanical application of BN powder is effective to some extent for preventing seizure.
- a resin is used as an adhesive for fixing, the coating should be performed every time it is sintered.
- thin film coatings made of various nitrides such as TiN, TiC, TiB, etc., such as sputtering, ion plating, CVD, etc., carbides, borides, alumina, etc. are durable and have a smooth surface. It is effective as an anti-seizure coating that can be used multiple times.
- the world's top-level neodymium magnet sintered body has a crystal grain size of 5 to 15 ⁇ m, and the grain size of the fine powder before sintering is 4.5 to 6 / im.
- D represents the median value of the particle size distribution measured with a laser type particle size distribution measuring instrument (eg, manufactured by Sympatech, manufactured by Horiba, Ltd.).
- the particle size of fine particles with a measured force of 3 ⁇ 4 ⁇ m, measured with an air permeation particle size distribution analyzer (Fischer's Sub'Sheave 'Sizer 1, FSSS), is about 4.5 to 5 ⁇ m. m is displayed.
- rare earth magnet alloy compositions containing more than 30% by weight of rare earth elements it was difficult to handle fine powders with a D force of 5 ⁇ m (3 ⁇ m in F.S.S.S.) or less by the conventional mold pressing method.
- a fine powder is filled in a mold in an inert atmosphere such as nitrogen, oriented by a magnetic field, and carried into a sintering furnace, so even if it is a fine powder that does not have a process of touching air. There is no danger in handling.
- the conventional die press, CIP and RIP manufacturing processes are not suitable for handling RFeB magnetic alloy fine powder containing a large amount of chemically active rare earth elements. If Sarase RFeB alloy powder small particle size of 4 ⁇ ⁇ below which is not oxidized in the atmosphere, fire, explosion risk Stable production is not possible. Even if it is not necessary to ignite, the fine powder has a large surface area, so that the amount of oxygen increases and the magnetic properties deteriorate. Since these effects cannot be avoided by the conventional method, it was not possible to handle a large amount of fine powder of 4.5 ⁇ m or less industrially.
- a neodymium sintered magnet having a high energy product and high coercive force is obtained.
- RFeB magnets having high coercive force which are used in small cars, hybrid cars and industrial motors, with little or no amount of Dy and Tb, even if they are used, are used at all. Stone can be mass-produced stably.
- One of the features of the present invention is that pressure molding is not performed after the powder is oriented, as in a die press, CIP, or RIP.
- the powder oriented in the mold is sintered while maintaining a high orientation that does not disturb the orientation when a pressure is applied.
- a high degree of orientation achieves a high residual magnetic flux density (B) and a high maximum energy product ((BH)).
- the value of D is less than ⁇ ⁇ ⁇ or less than 2 ⁇ ⁇ , or higher coercive force.
- the process from fine powder production to sintering can be processed in a completely inert atmosphere
- Rare earth-containing magnet powders with a D value of 0.5 ⁇ m or less can also be handled.
- the magnet alloy powder can be obtained by pulverizing a forged ingot whose composition is melted in a melting furnace, or a flake obtained by a molten metal quenching method (strip casting method).
- the pulverization is generally divided into coarse pulverization and fine pulverization.
- Coarse pulverization includes a mechanical pulverization method and a hydrogen pulverization method (hydrogen pulverization method), and is often used because the hydrogen pulverization method is excellent in productivity.
- As the fine pulverization method a method using a ball mill or an attritor or a jet mill pulverization method using an air stream such as nitrogen is generally used.
- the present invention is characterized by using a fine powder of several ⁇ m or less, a method other than the above may be used without any limitation on the method of obtaining the fine powder.
- the filling density of the powder in the mold according to the present invention is preferably S between 35% and 60% of the true density, and more preferably between 40% and 55%.
- a robust green compact was required for handling that led to subsequent processes. For this reason, in order to obtain sufficient magnetic properties, it was necessary to apply a stronger pressing force.
- the present invention since there is no green compact handling process, it is necessary to consider the green compact strength as in the conventional method.
- the powder filling it is preferable to use a mechanical tapping method using mechanical vibration, a pusher method in which a push bar is pushed into a mold, or an air tapping method (Japanese Patent Laid-Open No. 2000-96104).
- Micron-sized magnet powder aggregates and forms a bridge easily when it is immediately filled into a mold, making uniform filling difficult.
- the bridge is mechanically broken and high-density filling is performed.
- the powder can be uniformly and densely filled into the mold with high density by covering the powder in the powder feeder with a periodic air impact by the air tapping method.
- a powder with a binder added in advance is filled into a mold by an air-tapping method, the binder is solidified by a method such as heating, and the powder is bonded to form a compact.
- a method of obtaining and then sintering is described.
- the present invention does not have the idea of sintering (or pre-sintering) a mold that is not oriented by a magnetic field, which is not the case with magnets.
- the use of a binder for obtaining a powder compact does not require handling of a powder compact solidified with a binder.
- the external magnetic field generating source used for the orientation of the powder is preferably a pulsed magnetic field.
- a pulsed magnetic field is applied by placing a mold filled with powder in the air core coil.
- the applied magnetic field is 1.5 T at most, whereas in the pulse magnetic field method, a higher magnetic field can be applied.
- the magnitude of the pulse magnetic field in the present invention is 2T or more, preferably 3T or more, and more preferably 5T or more.
- a pulse magnetic field for orienting the powder is preferably applied by applying an alternating decay type waveform magnetic field in advance and then applying a DC pulse magnetic field rather than applying a DC pulse only once.
- Japanese Patent No. 3307418 confirms that magnetic properties are improved by applying a magnetic field of 1.5 to 5 T in the manufacture of RFeB magnets.
- a pulsed magnetic field is applied to a conventional mold press, eddy current loss and hysteresis loss occur in the mold, and continuous use is possible. Kinare.
- the impact force due to the pulsed magnetic field is applied to the mold, so the mold may be damaged.
- the powder orientation magnetic field in the present invention may be any magnetic field as long as a strong magnetic field can be obtained by a superconducting coil or the like.
- a thin ribbon for obtaining a fine powder having a thickness of 200 ⁇ m or less it is preferable.
- the coercive force of the finally obtained neodymium sintered magnet can be maximized by obtaining fine powder using an alloy ribbon having an appropriate thickness.
- all the steps from taking out the fine powder from the pulverizer to carrying it into the sintering furnace are performed in an inert atmosphere.
- the fine powder placed in the hopper is filled into a mold placed in an inert gas atmosphere through high-density filling means such as mechanical tapping or air tapping, capped, and subjected to orientation means in a magnetic field. Move to the place you set up.
- the powder in the mold is oriented by a magnetic field orientation means such as a pulsed magnetic field and transported to the sintering furnace as it is.
- solid lubricants have low vapor pressure and high boiling point
- liquid lubricants have high vapor pressure and low boiling point. Considering that it is easy to spread throughout the fine powder and easy to degrease, a liquid lubricant is good.
- liquid lubricants As liquid lubricants, it is known to use methyl cabronate or methyl methyl plyrate together with saturated fatty acids (Japanese Patent Laid-Open No. 2000-109903). However, when these lubricants are used in the die press method, only a very small amount of 0.05 to 0.5% by weight can be used with respect to the magnet powder. These have the feature that they do not remain in the sintered body with good volatility. When sintering strongly compacted green compacts, it is difficult to remove even the lubricant components confined inside the green compacts. The lubricant and magnet components react at high temperatures and become magnetic. This is because the characteristics may be deteriorated.
- the powder in the mold is not compressed, and the lubricant component is gasified and easily removed. Therefore, it is preferable that the amount of the liquid lubricant of the present invention is large. However, if it is too much, there is a risk that it will not be filled with high density.
- the amount of liquid lubricant added is 0.1 to 1%.
- the liquid lubricant of the present invention is good if it is lubricious and easily volatilizes.
- methyl stearate can be used.
- Lubricants that are solid at room temperature, such as zinc stearate, have the disadvantage of being difficult to apply evenly to the powder particle surface compared to liquid lubricants.
- a device that applies a solid lubricant to the surface of the powder particles such as a mixer called a super mixer (manufactured by Karitane Earth)
- the lubrication effect of the solid lubricant will be maximized.
- Powders to which a solid lubricant is added in this way have the advantage that solidification due to compression is less likely to occur than powders to which a liquid lubricant is added.
- the powder is pressed against the outer periphery during pulse orientation and hardens, and a nest is formed in the center of the sintered body by subsequent sintering. Can be prevented.
- the present invention has been found as a method for solving the problems and contradictions of the conventional methods in a method for producing a magnetically anisotropic sintered magnet of a rare earth magnet such as an RFeB magnet or an RCo magnet.
- a rare earth magnet such as an RFeB magnet or an RCo magnet.
- An isotropic sintered magnet is obtained.
- the air-core coil can provide a strong pulsed magnetic field, and can treat chemically active fine powders containing rare earth elements without exposure to the atmosphere.
- Rare earth magnets with high coercivity can be obtained without using Tb or Dy.
- high-performance magnets of the product shape most produced as rare earth magnet products such as thin plates and arcuate plates are produced very efficiently. The ability to produce S
- FIG. 1 is a perspective view showing an example of a unit price mold used for carrying out the method for producing a magnetic anisotropic rare earth sintered magnet of the present invention.
- FIG. 2 is a perspective view showing an example of a multi-piece mold used for carrying out the method for producing a magnetic anisotropic rare earth sintered magnet of the present invention.
- FIG. 3 is a perspective view showing an example of a multi-piece mold used for carrying out the method for producing a magnetic anisotropic rare earth sintered magnet of the present invention.
- FIG. 4 is a perspective view showing an example of a lid used in the mold of this example.
- FIG. 5 is a schematic configuration diagram showing an example of an apparatus for producing a magnetic anisotropic rare earth sintered magnet according to the present invention.
- FIG. 6 is a schematic configuration diagram showing an example of an apparatus for producing a magnetic anisotropic rare earth sintered magnet according to the present invention.
- FIG. 7 is a photograph of the disk-shaped NdFeB sintered magnet produced in this example and the monored used for its production.
- FIG. 8 is a photograph of a cylindrical ring-shaped NdFeB sintered magnet produced in this example (the magnetic field orientation direction is parallel to the axis) and the mold used for the production.
- the mold is preferably made of a material that can withstand a high sintering temperature ( ⁇ 1100 ° C.). In the process of raising the temperature of the mold in advance, slight bonding of the particles occurs, and the object to be sintered is in a state capable of self-holding. In this pre-sintered state, part or all of the mold can be removed, and the pre-sintered body can be transferred to another mold or base plate.
- the pre-sintering temperature is preferably between 500 ° C and 30 ° C lower than the sintering temperature, so the mold used during pre-sintering should be a material that can withstand this temperature.
- iron, iron alloy, stainless steel, permalloy, heat-resistant steel, heat-resistant alloy, superalloy, molybdenum, tungsten or their alloys, and ceramics such as ferrite and alumina can be used.
- a release agent such as BN to the inner wall of the mold in advance.
- BN a release agent
- a high melting point metal such as Mo or W
- the sintered body adheres to the inner wall of the mold during sintering.
- a thin film such as TiN, TiC, ⁇ , Al 2 O, or ZrO is applied to the surface of a mold such as stainless steel.
- Durable anti-fusing coatings can be made by tulling, CVD, or ion plating.
- the filling method is important. Since permanent magnet alloy fine powder that cannot be granulated has the properties of magnetite, it forms a bridge that easily aggregates, and it is difficult to quantitatively fill the mold.
- the forced filling used in the present invention includes, for example, a mechanical tapping method, A pusher method or an air tapping method (Japanese Patent Laid-Open No. 2000-96104) developed by the present inventor can be used.
- the packing density is preferably 35% to 60% of the true density of the alloy. If it is 35% or less, a large nest is formed in the sintered body, or the entire sintered body becomes low-density and porous, and a practical permanent magnet cannot be obtained. In order to obtain a high-quality permanent magnet that can be used practically, the packing density needs to be 35% or more. If the packing density exceeds 60%, sufficient orientation cannot be obtained due to magnetic field orientation. A more preferable packing density range is 40 to 55% in order to obtain a high-density sintered body that is sufficiently oriented and free of nests and cracks.
- a single mold corresponding to each shape as shown in Fig. 1 can be used.
- a multi-piece mold as shown in Fig. 2 or Fig. 3 can be used.
- the partition of each cavity may be a detachable thin partition (for example, the partition 21 in FIG. 2 (3)).
- molds such as those shown in Fig. 2 (1), (2), (4), and (5) can be directly hollowed into a solid material by cutting with a drill or end mill or by electric discharge. It is made by forming. If a mold having a cavity with a predetermined shape calculated in advance from the shrinkage rate is prepared and subjected to a predetermined forced filling, a sintered body with a uniform predetermined shape can be obtained.
- the perforated cylindrical ring-shaped magnet manufactured by the mold shown in Fig. 1 (3) or (4) can be manufactured only by the parallel magnetic field pressing method in the conventional mold pressing method. Due to the low magnetic properties of sintered magnets produced by the parallel magnetic field pressing method, it was desired to develop a method for manufacturing cylindrical ring magnets with magnetic properties equivalent to or higher than those of perpendicular magnetic field pressing. Attempts were made to place a metal rod (core) in the center of the rubber mold and compress it with a CIP or RIP after applying a pulsed magnetic field. The net shape is poor and the productivity is low. In the production method according to the present invention, the fine powder may be put into a mold, pulse-oriented and then sintered as it is.
- FIGS. 1 (3) and 1 (4) show an example in which the mold cavity is cylindrical, the cavity may have another shape such as a hexagonal column. Further, the core is not limited to a cylindrical shape, and may be another shape such as a hexagonal column shape.
- Fig. 1 (2) shows an example of a mold for a large block. According to the present invention, it is possible to easily achieve a force having a magnitude that has been difficult due to the limit of the pressing pressure and the limit of the uniform magnetic field region in the conventional mold pressing method.
- Fig. 2 (3) shows a flat magnet mold separated by thin partitions. By using this mold, a large number can be obtained.
- Fig. 2 (4) shows a mold for arcuate plate magnets used in motors.
- the partition may be detachable as in FIG. 2 (3).
- Fig. 2 (5) shows a mold for manufacturing a columnar magnet having a sector cross section. Magnets obtained by cutting the produced sector-shaped columnar magnets to a predetermined thickness are used for voice coil motors and the like.
- Fig. 3 shows an example of a mold that can produce a larger number of flat magnets at one time than the molds in Figs. 2 (1) and (3).
- it is not necessary to use a die press so that two rows of flat cavities can be arranged side by side.
- three or more rows of such cavities can be arranged, and two or more rows of cavities of other shapes such as an arcuate plate shape can be arranged in place of the flat plate-like cavities (not shown).
- a coil having a larger core capacity than before can be used. Therefore, even if two or more cavities are arranged in this way, the variation in magnet characteristics for each flat magnet is sufficiently large. Can be kept small.
- the lid is designed to fit lightly into the mold. If the fit between the lid and mold mouth is too tight, the cavity will be sealed. If the cavity is hermetically sealed, densification of the sintered body will be roughened during sintering, or it may be contaminated by carbon components contained in the lubricant, resulting in a decrease in magnetic properties. Therefore, adjust the fit so that a small gap is created between the lid and the mold opening, or form a small hole for deaeration as shown in Figs. 4 (1) and (2).
- the present invention is applied to a method for producing a rare earth magnet containing R (R is at least one kind of rare earth element including Y) and a transition element.
- the composition of the rare earth magnet is not particularly limited as long as it contains a rare earth element and a transition element.
- an RFeB-based sintered magnet part of Fe can be replaced by Co
- Suitable for manufacturing RCo-based sintered magnets are particularly limited as long as it contains a rare earth element and a transition element.
- the composition of the RFeB rare earth magnet usually preferably contains 27 to 38% by weight of R, 51 to 72% by weight of Fe, and 0.5 to 4.5% by weight of B. If the R content is too small, an iron-rich phase precipitates and high coercivity cannot be obtained. On the other hand, if the R content is too high, the residual magnetic flux density decreases.
- the rare earth element R examples include Y, La, Ce, Pr, Nd, Eu, Gd, Tb, Dy, Ho, Tm, Yb, Lu, and the like, and it is particularly preferable that Nd and / or Pr is included. .
- high coercivity can be obtained by replacing a part of R with dysprosium (Dy) or terbium (Tb), which are heavy rare earth elements.
- the amount of heavy rare earth element substitution is preferably 6% by weight or less. If the B content is too low, a high coercive force cannot be obtained, and if the B content is too high, a high residual magnetic flux density cannot be obtained. It is also possible to replace part of Fe with Co. In that case, if the amount of substitution is too large, the coercive force is reduced, so the amount of Co is preferably 30% by weight or less.
- elements such as Al, Cu, Nd, Cr, Mn, Mg, Si, C, Sn, W, V, Zr, Ti, Mo, and Ga are added. However, if the total amount of these additives exceeds 5% by weight, the residual magnetic flux density decreases, which is not preferable.
- a magnet alloy having such a composition has a main phase of a substantially tetragonal crystal structure. Moreover, it usually contains a nonmagnetic phase of about 0.1 to 10% by volume.
- the method for producing the magnet powder is not particularly limited.
- the mother alloy ingot is produced by smashing it, or it is produced by pulverizing the alloy powder obtained by the reduction diffusion method.
- the average particle size of the magnet fine powder is preferably 0.5 to 5 / im in the case of the RFeB magnet.
- fine powder or green compact was exposed to the atmosphere, so fine powder of 4 ⁇ or less could not be used.
- a powder of 3 / im or less, or 2 ⁇ or less can be used.
- the crystal grain size of the sintered body is as close as possible to 0.2 to 0.3 ⁇ , which is the size of the single domain particle diameter of the RFeB type magnet. In order to achieve this, it is desirable that the fine powder particle size is fine.
- the particle size of the fine powder was measured using a numerical value measured by Fisher's Sub-sieve-sizer (FSS S.S.) (for example, Japanese Patent Laid-Open No. 59-163802).
- FSS S.S. Fisher's Sub-sieve-sizer
- D the median value of the particle size distribution obtained by a laser type particle size distribution measuring device (eg, manufactured by Sympatech, manufactured by Horiba, Ltd.). It is known that the measured values of both methods differ by 1.5 to 2 times. In this application, the value of D measured with a laser particle size distribution device is used.
- the preferable crystal grain size is 4 ⁇ or less as the value of D in the case of the RFeB magnet. In order to obtain a large coercive force, 3 ⁇ or less is preferable. Since the process of the present invention is performed in a completely closed system, 2 ⁇ m or less is more preferable. In addition, the optimum size in order to approximate the crystal grain size of the single domain particle size of the RFeB intermetallic compound is l z m or less.
- the preferred powder particle size is 1 to 5 ⁇ m in either case of 1-5 type or 2-17 type.
- a pulse magnetic field is applied to the powder-filled mold by an air-core coil arranged in a continuous device.
- the demagnetization process for handling the green compact necessary for the die press method, CIP, and RIP method is not required.
- the magnetic field for orientation is preferably strong, but in reality, there are limits depending on the size of the power source, the strength of the coil, and the frequency of continuous use. Considering these factors, a preferable magnetic field strength is 2T or more, more preferably 3T or more, and even more preferably 5T or more.
- a magnetic field of this level can be obtained by an air-core coinor.
- the coil diameter must be larger than that of the mold in the mold press. Since the mold is much larger than the size of the cavity into which the powder can enter, an air core coil with a large inner diameter that can contain such a mold is required.
- the inner diameter of the air-core coil may be as large as the mold can enter.
- the magnetic field strength increases as the coil inner diameter decreases even with the same ampere-turn. Therefore, by using the method of the present invention, it is possible to reduce the coil inner diameter. , Can increase economics.
- the fine powder in the mold oriented by the pulsed magnetic field is usually conveyed to the degreasing process which is a pre-sintering process without demagnetization.
- the sintering furnace is preferably a continuous processing furnace, because it can be a closed process without contact with oxygen.
- the mold is put into a sealed container, the sealed container is put into a transport chamber filled with an inert gas, and the mold is sealed in an atmosphere chamber provided in the front chamber of the sintering furnace. It is also possible to transfer it on a plate.
- the mold In the pre-sintering chamber, the mold is heated in a vacuum or an inert gas decompression atmosphere. If a lubricant is used, it is degreased at this stage.
- a conventional mold press, CIP, or RIP When using a conventional mold press, CIP, or RIP, and strongly compressing the powder, the lubricant contained inside the compact can be easily degreased.
- the lubricant component applied to the particle surface in the powder easily evaporates through a gap between the mold and the lid or a deaeration hole provided in the mold or the lid.
- the entire apparatus (hereinafter referred to as the system) is surrounded by a partition wall 40 and filled with an inert gas such as Ar gas N gas.
- the system has a powder balance as shown in Figure 5.
- a certain amount of powder is supplied to the mold 46 from the weighing / filling section 41 with a shaker and a hopper 47.
- a guide 48 is attached to the upper part of the mold 46 in order to hold a predetermined amount of powder in the mold 46.
- a lid 49 is placed on the powder upper surface of the upper part of the mold 46, and as shown in FIG. 5, the lower part of the Monored 46 is tapped while pressing the lid 49 with the push rod 51 of the press cylinder 50.
- the device 52 is driven and the powder is densified.
- the tapping device is an exciter (tapping) that intermittently applies downward acceleration to the powder in the mold 46.
- the powder in the mold 46 is pushed down to the upper end of the mold 46 (the lower end of the guide) or slightly below it, and the lid 49 is attached to the upper surface of the mold 46.
- the holder 53 and the guide 48 at the time of tapping are removed from the mold 46, and the mold with the lid is conveyed to the magnetic field orientation section by the conveyor in a state where the powder is filled with high density.
- the mold 46 filled with powder is directed in a predetermined direction and placed at a predetermined position (center part of the coil).
- a large pulse current flows in the coil 54 installed outside the partition wall 40, and the pulse magnetic field generated thereby causes the powder in the mold 46 to be oriented in a predetermined direction.
- the mold 46 filled with the powder is transported to the sintering furnace.
- the feature of this system is that the powder is carried in the mold, so it is easy to handle (delivery and transfer) of the powder, and there is no need for a robot or manual operation (manual operation) with complicated movement.
- the entire system is completely covered by the bulkhead 40 because the huge pressure device, such as the total pressure of 10 to 200 tons used in mold presses, is unnecessary. It is easy to enclose.
- This powder is filled into a stainless steel pipe with an inner diameter of 10 mm, an outer diameter of 12 mm, and a length of 30 mm so that the powder packing density is 3.0, 3.2, 3.4, 3.6, 3.8, 4.0 g m 3.
- a stainless steel lid was attached.
- a Null magnetic field was applied to the NdFeB magnet powder packed in this stainless steel pipe in a direction parallel to the axis of the pipe.
- the peak value of the strength of the Norse magnetic field is 8T.
- An alternating decaying magnetic field (hereinafter referred to as an AC pulse) that attenuates while alternating the direction is changed, and the magnetic field direction is not changed after reaching the peak value of 8T.
- pulsed magnetic fields Two types of pulsed magnetic fields (hereinafter referred to as DC pulses).
- a pulse magnetic field having a peak value of 8 T was applied to magnet powder filled in a stainless steel pipe in the order of AC, DC, and DC.
- the stainless steel pipe filled with the magnetic powder was transferred to a sintering furnace and sintered at 1050 ° C for 1 hour.
- the filling of the powder into the stainless steel pipe, the pulsed magnetic field orientation, the charging into the sintering furnace, and all the transportation in the middle are all performed in an inert gas, and the magnet powder is not exposed to air.
- pulverization to sintering was implemented.
- the sintered body was taken out from the stainless pipe. Sintering when the powder packing density 3.0g N m 3, the force packing density cavities was made more like nest in the sintered body when the m 3 N 3.2g was m 3 N 3.4g The body had no cavities except for a small portion that touched the lid. When the packing density is 3.6 g m 3 or more, the density of the sintered body reaches 98.7% of the theoretical density, and there are very few or no cavities. It was confirmed that it was formed.
- the sintered body was processed into a cylinder with a diameter of 7 mm and a height of 7 mm, and a pulse magnetic field with a maximum magnetic field of 10 T was applied to measure the magnetic field.
- the ratio of remanent magnetization to the value of magnetization at 10T was obtained from magnetic measurements by applying a pulsed magnetic field, and the degree of orientation in the sintered body was measured.
- the degree of orientation of the sintered body produced with a packing density of 3.6 g m 3 was 97.0%, and that of 3.8 g m 3 was 96.0%.
- the degree of orientation of the sintered body produced by the conventional molding method in the mold magnetic field was 95.6%.
- the space filled with mold powder is 25mm in diameter and 7mm in thickness.
- the powder is packed into these cavities so that the packing density is 3.8 g m 3 , and the same magnetic field as AC ⁇ DC ⁇ DC (peak magnetic field is 8T for each) is applied to the powder together with Experiment 1 to orient the powder. And then sintered.
- the powder was sintered in the whole process without touching the air.
- the same strip cast alloy as in Experiment 1 was pulverized with hydrogen, and then the pulverization conditions were changed by a jet mill to produce fine powders with different particle sizes.
- the work was done in high purity Ar gas.
- a sintered body was also produced using a conventional mold press.
- all operations were performed in an inert gas so that the powder or green compact did not touch the air before sintering.
- the thickness of the mold was 3 mm on both sides and 2 mm on the side.
- the inner surface of the mold was rubbed with a mixture of BN powder and solid wax to form an anti-adhesion film during sintering.
- the size of the sintered body was 19.0 to 19.5 mm in diameter and 2.7 to 2.8 mm in thickness (the higher the packing density, the larger). From the photograph, all sintered bodies produced using an iron mold have holes in the middle, and it is worth noting that a piece of the sintered body remains in the center of the mold. Thus, when producing a relatively thin sintered body using an iron mold, a large hole is formed at the center even when the powder packing density is high. It can be seen that when a magnetic stainless steel (SUS440) mold is used, if the packing density is low, a nest tends to be formed at the center of the disk-shaped sintered body.
- SUS440 magnetic stainless steel
- the powder loading was varied from 3.2 g m 3 to 3.9 g m 3 at intervals of O.lg m 3 , and the sintering conditions were the same as in Experiment 4.
- the direction of the orientation magnetic field was a direction parallel to the direction of the long side outside the mold.
- the mold outer material is iron, magnetic stainless steel or permalloy
- the top and bottom plates are non-magnetic stainless steel
- the partition plate is non-magnetic stainless steel or permalloy.
- the cavities at both ends of the plural cavities partitioned by the partition plate that is, the flat plate surface or the arcuate plate surface are formed in the cavities formed in contact with the outer frame.
- the body had a nest. From these cavities other than both ends, a good sintered body without a nest was obtained.
- the core is made of non-magnetic stainless steel and the upper and lower lids are made of a magnetic material (iron, magnetic stainless steel, permalloy)
- the cavity is filled with powder and the magnetic field is axially directed to the cylindrical ring-shaped cavity.
- the magnetized powder was adsorbed by the upper and lower lids, and the powder did not fall or collapse even when the core was pulled out.
- the mold and the cylinder axis were placed vertically in a sintering furnace and sintered at 1010 ° C for 2 hours.
- the sintered body thus produced had a cylindrical ring shape as expected from the sintering shrinkage without deformation or distortion.
- the cylindrical ring-shaped NdFeB sintered body produced in this experiment is much higher in B and NdFeB sintered magnets than those produced by the conventional parallel magnetic field press (die press).
- Fig. 8 shows a photograph of the mold used in this experiment and the cylindrical ring-shaped NdFeB sintered magnet produced thereby.
- the outer diameter of the mold cavity was 23.0 mm
- the inner diameter was 10.0 mm
- the height was 33.2 mm.
- the produced cylindrical ring magnet had an outer diameter of 19.1 mm, an inner diameter of 8.6 mm, and a height of 22.3 mm.
- the lid was not particularly provided with small holes, and the clearance at the fitting portion between the lid and the mold mouth was used as a deaeration hole during sintering.
- the mold filled with the powder was put in a sealed container, and a pulsed magnetic field was applied to the powder and the mold while being put in the sealed container.
- the pulse magnetic field was varied in the range of 1.8 T to 9 T, and an AC decay pulse and a DC pulse were sequentially applied to perform magnetic field orientation of the powder.
- the sealed container was coupled to the sintering furnace inlet, the mold in the sealed container without any contact with air was transferred into the sintering furnace, and the sintering furnace inlet was closed. Sintering was carried out in a high vacuum of more than 10- 4 Pa.
- the sintering temperature was varied in the range of 950 ° C to 1050 ° C, and the lowest temperature at which the density of the sintered body after sintering (sintering density) exceeded 7.5 gm 3 was determined as the optimum temperature.
- the sintering time was 2h. After sintering, the sintered body was rapidly cooled from 800 ° C to room temperature, and then quenched by heating at 500 to 600 ° C for lh. After heat treatment, all samples were processed into 7mm diameter and 7mm long cylinders, and the magnetization curve was measured by appearance inspection, density measurement, and pulse magnetization measurement with a maximum magnetic field of 10T. The main results of this experiment are shown in Table 4.
- the orientation magnetic field of 9.0P or 1.8P means a pulsed magnetic field with peak values of 9.0T and 1.8T, respectively.
- a dc pulse with the same peak value was applied twice in the same direction, followed by one attenuation pulse.
- 2.5D indicates that a 2.5T DC magnetic field was applied.
- a DC magnetic field was first applied in one direction of the mold, and then a DC magnetic field having the same strength was applied by changing the magnetic field application direction in the opposite direction while the mold was fixed.
- the method of the present invention makes it possible to safely use powders with extremely small particle sizes that are difficult to handle by conventional mold press and RIP methods, and have high coercivity that is difficult to achieve by conventional methods. It was confirmed that the sintered magnet can be manufactured industrially.
- Samples 1 to 13 have high residual magnetic flux density B, maximum energy product (BH), coercive force H, and degree of orientation J / J.
- Samples 14 and 15 have a slightly lower force (BH) and coercive force H, which are higher than the other samples, than the other samples.
- Sample 16 also has a low orientation magnetic field max c;
- Sample 17 has a packing density of r max rs Force that is lower than other samples Cavities were formed in the sintered body, and magnetic properties comparable to those of other samples could not be measured.
- the comparative example shows an example of a NdFeB sintered magnet produced by using a conventional powder having a standard particle size by a conventional die press method.
- the particle size of the powder cannot be made very small, so that the coercive force obtained is smaller than the example of the magnet of the present invention.
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Abstract
Description
Claims
Priority Applications (5)
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CN2005800203043A CN1969347B (zh) | 2004-07-01 | 2005-06-30 | 磁各向异性稀土类烧结磁体的制造方法及其制造装置 |
US11/630,898 US8545641B2 (en) | 2004-07-01 | 2005-06-30 | Method and system for manufacturing sintered rare-earth magnet having magnetic anisotropy |
EP05765338.8A EP1788594B1 (en) | 2004-07-01 | 2005-06-30 | Production method for magnetic-anisotropy rare-earth sintered magnet |
KR1020077000697A KR101185930B1 (ko) | 2004-07-01 | 2005-06-30 | 자기이방성 희토류 소결자석의 제조방법 및 제조장치 |
US13/975,616 US20130343946A1 (en) | 2004-07-01 | 2013-08-26 | Method and system for manufacturing sintered rare-earth magnet having magnetic anisotropy |
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JP2004195935A JP4391897B2 (ja) | 2004-07-01 | 2004-07-01 | 磁気異方性希土類焼結磁石の製造方法及び製造装置 |
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KR (1) | KR101185930B1 (ja) |
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Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH02250922A (ja) * | 1989-03-25 | 1990-10-08 | Kobe Steel Ltd | 希土類元素―遷移元素―b系磁石の製造方法 |
JPH0696973A (ja) * | 1991-11-28 | 1994-04-08 | Inter Metallics Kk | 永久磁石の製造方法 |
JPH07153612A (ja) | 1993-11-26 | 1995-06-16 | Sumitomo Special Metals Co Ltd | Fe−B−R系磁石材料の製造方法 |
JPH0970696A (ja) * | 1995-09-07 | 1997-03-18 | Toyota Auto Body Co Ltd | 粉体成形用金型装置 |
JP2001028309A (ja) * | 1999-07-14 | 2001-01-30 | Mitsubishi Electric Corp | 磁石およびその磁場成形装置 |
US20020159909A1 (en) | 1999-03-03 | 2002-10-31 | Sumitomo Special Metals Co., Ltd. | Case for use in sintering process to produce rare-earth magnet, and method for producing rare-earth magnet |
JP2004002998A (ja) * | 2002-04-12 | 2004-01-08 | Sumitomo Special Metals Co Ltd | 希土類合金粉末のプレス成形方法および希土類合金焼結体の製造方法 |
Family Cites Families (50)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
NL87162C (ja) | 1950-09-19 | |||
NL93755C (ja) | 1951-12-21 | |||
US3684593A (en) | 1970-11-02 | 1972-08-15 | Gen Electric | Heat-aged sintered cobalt-rare earth intermetallic product and process |
JPS5596616A (en) | 1979-01-17 | 1980-07-23 | Matsushita Electric Ind Co Ltd | Method of manufacturing copper-substituted rare earth cobalt permanent magnet |
JPS5946008A (ja) | 1982-08-21 | 1984-03-15 | Sumitomo Special Metals Co Ltd | 永久磁石 |
JPS5989401A (ja) | 1982-11-15 | 1984-05-23 | Sumitomo Special Metals Co Ltd | 永久磁石 |
JPS59163802A (ja) | 1983-03-08 | 1984-09-14 | Sumitomo Special Metals Co Ltd | 永久磁石材料 |
JPS6032306A (ja) | 1983-08-02 | 1985-02-19 | Sumitomo Special Metals Co Ltd | 永久磁石 |
US4792367A (en) | 1983-08-04 | 1988-12-20 | General Motors Corporation | Iron-rare earth-boron permanent |
JPS6063304A (ja) | 1983-09-17 | 1985-04-11 | Sumitomo Special Metals Co Ltd | 希土類・ボロン・鉄系永久磁石用合金粉末の製造方法 |
JPS60182104A (ja) | 1984-02-28 | 1985-09-17 | Sumitomo Special Metals Co Ltd | 永久磁石材料の製造方法 |
JPS6144414A (ja) | 1984-08-09 | 1986-03-04 | Citizen Watch Co Ltd | 永久磁石の製造方法 |
JPS61160201A (ja) | 1985-01-08 | 1986-07-19 | 小松ゼノア株式会社 | チエンソ− |
JPH066728B2 (ja) | 1986-07-24 | 1994-01-26 | 住友特殊金属株式会社 | 永久磁石材料用原料粉末の製造方法 |
JP2665590B2 (ja) | 1987-06-19 | 1997-10-22 | 住友特殊金属株式会社 | 希土類―鉄―ボロン系磁気異方性焼結永久磁石原料用合金薄板並びに磁気異方性焼結永久磁石原料用合金粉末,及び磁気異方性焼結永久磁石 |
JP2561704B2 (ja) | 1988-06-20 | 1996-12-11 | 株式会社神戸製鋼所 | 希土類−Fe−B系磁石の製造方法 |
JPH0230923A (ja) | 1988-07-20 | 1990-02-01 | Fuji Heavy Ind Ltd | 6気筒エンジンの吸気装置 |
JP2545603B2 (ja) | 1989-03-10 | 1996-10-23 | 住友特殊金属株式会社 | 異方性焼結磁石の製造方法 |
EP0393815B1 (en) * | 1989-04-15 | 1994-05-18 | Fuji Electrochemical Co.Ltd. | Method for packing permanent magnet powder |
JPH0358281A (ja) | 1989-07-27 | 1991-03-13 | Nisca Corp | データ処理方法 |
JPH0744121B2 (ja) | 1990-11-30 | 1995-05-15 | インターメタリックス株式会社 | 永久磁石の製造方法、製造装置及び磁界中配向成形用ゴムモールド |
EP0646937B1 (en) | 1990-11-30 | 1997-09-03 | Intermetallics Co., Ltd. | Method for producing a permanent magnet and an apparatus for producing a green compact |
US5672363A (en) | 1990-11-30 | 1997-09-30 | Intermetallics Co., Ltd. | Production apparatus for making green compact |
JP3307418B2 (ja) | 1992-02-21 | 2002-07-24 | ティーディーケイ株式会社 | 成形方法および焼結磁石の製造方法 |
JPH06108104A (ja) | 1992-09-30 | 1994-04-19 | Hitachi Metals Ltd | 希土類磁石の製造方法及びその装置 |
JP2731337B2 (ja) | 1993-03-19 | 1998-03-25 | 日立金属株式会社 | 希土類焼結磁石の製造方法 |
JP2859517B2 (ja) | 1993-08-12 | 1999-02-17 | 日立金属株式会社 | 希土類磁石の製造方法 |
JP3383448B2 (ja) | 1994-12-09 | 2003-03-04 | 住友特殊金属株式会社 | R−Fe−B系永久磁石材料の製造方法 |
US5666635A (en) * | 1994-10-07 | 1997-09-09 | Sumitomo Special Metals Co., Ltd. | Fabrication methods for R-Fe-B permanent magnets |
JP3459477B2 (ja) | 1994-10-07 | 2003-10-20 | 住友特殊金属株式会社 | 希土類磁石用原料粉末の製造方法 |
JP3777199B2 (ja) | 1994-12-09 | 2006-05-24 | 株式会社Neomax | 高性能R−Fe−B系永久磁石材料の製造方法 |
JP3710184B2 (ja) | 1995-12-15 | 2005-10-26 | インターメタリックス株式会社 | 被充填物の充填方法 |
JPH0978103A (ja) | 1995-09-11 | 1997-03-25 | Inter Metallics Kk | 粉末充填方法及びその装置 |
JP2900885B2 (ja) | 1996-06-21 | 1999-06-02 | 日本電気株式会社 | 時刻情報補正装置 |
JP3978262B2 (ja) | 1997-08-07 | 2007-09-19 | インターメタリックス株式会社 | 充填方法及びその装置 |
JP4216929B2 (ja) | 1998-10-06 | 2009-01-28 | 日立金属株式会社 | R−Fe−B系磁石成形用離型剤 |
JP2000306753A (ja) | 1999-04-21 | 2000-11-02 | Sumitomo Special Metals Co Ltd | R‐Fe‐B系永久磁石の製造方法とR‐Fe‐B系永久磁石成形用潤滑剤 |
JP3992376B2 (ja) | 1998-09-24 | 2007-10-17 | インターメタリックス株式会社 | 粉末成形方法 |
JP3418605B2 (ja) | 1999-11-12 | 2003-06-23 | 住友特殊金属株式会社 | 希土類磁石の製造方法 |
JP3233359B2 (ja) | 2000-03-08 | 2001-11-26 | 住友特殊金属株式会社 | 希土類合金磁性粉末成形体の作製方法および希土類磁石の製造方法 |
JP2002088403A (ja) | 2000-03-08 | 2002-03-27 | Sumitomo Special Metals Co Ltd | 希土類合金磁性粉末成形体の作製方法および希土類磁石の製造方法 |
JP4759889B2 (ja) | 2000-09-12 | 2011-08-31 | 日立金属株式会社 | 粉末充填装置、それを用いたプレス成形装置および焼結磁石製造方法 |
JP3294841B2 (ja) | 2000-09-19 | 2002-06-24 | 住友特殊金属株式会社 | 希土類磁石およびその製造方法 |
JP3452561B2 (ja) | 2000-11-08 | 2003-09-29 | 住友特殊金属株式会社 | 希土類磁石およびその製造方法 |
CN2475105Y (zh) * | 2001-03-14 | 2002-01-30 | 包头稀土研究院 | 一种磁环的多极聚合辐射取向成型装置 |
JP4089212B2 (ja) | 2001-11-28 | 2008-05-28 | 日立金属株式会社 | 希土類合金の造粒粉の製造方法および希土類合金焼結体の製造方法 |
CN1306527C (zh) * | 2001-12-18 | 2007-03-21 | 昭和电工株式会社 | 用于稀土磁体的合金薄片及其生产方法、用于稀土烧结磁体的合金粉末、稀土烧结磁体、用于结合磁体的合金粉末和结合磁体 |
DE10392157B4 (de) | 2002-04-12 | 2007-01-25 | Neomax Co., Ltd. | Verfahren zum Pressen eines Seltenerdmetall-Legierungspulvers und Verfahren zur Herstellung eines Sinterkörpers aus einer Seltenerdmetall-Legierung |
US6992553B2 (en) * | 2002-06-18 | 2006-01-31 | Hitachi Metals, Ltd. | Magnetic-field molding apparatus |
JP4391897B2 (ja) * | 2004-07-01 | 2009-12-24 | インターメタリックス株式会社 | 磁気異方性希土類焼結磁石の製造方法及び製造装置 |
-
2004
- 2004-07-01 JP JP2004195935A patent/JP4391897B2/ja not_active Expired - Fee Related
-
2005
- 2005-06-30 US US11/630,898 patent/US8545641B2/en active Active
- 2005-06-30 WO PCT/JP2005/012123 patent/WO2006004014A1/ja active Application Filing
- 2005-06-30 EP EP05765338.8A patent/EP1788594B1/en not_active Not-in-force
- 2005-06-30 CN CN2005800203043A patent/CN1969347B/zh active Active
- 2005-06-30 EP EP12195806.0A patent/EP2597659A3/en not_active Withdrawn
- 2005-06-30 KR KR1020077000697A patent/KR101185930B1/ko active IP Right Grant
- 2005-06-30 EP EP12195828.4A patent/EP2597660A3/en not_active Withdrawn
- 2005-07-01 TW TW094122355A patent/TW200609061A/zh not_active IP Right Cessation
-
2013
- 2013-08-26 US US13/975,616 patent/US20130343946A1/en not_active Abandoned
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH02250922A (ja) * | 1989-03-25 | 1990-10-08 | Kobe Steel Ltd | 希土類元素―遷移元素―b系磁石の製造方法 |
JPH0696973A (ja) * | 1991-11-28 | 1994-04-08 | Inter Metallics Kk | 永久磁石の製造方法 |
JPH07153612A (ja) | 1993-11-26 | 1995-06-16 | Sumitomo Special Metals Co Ltd | Fe−B−R系磁石材料の製造方法 |
JPH0970696A (ja) * | 1995-09-07 | 1997-03-18 | Toyota Auto Body Co Ltd | 粉体成形用金型装置 |
US20020159909A1 (en) | 1999-03-03 | 2002-10-31 | Sumitomo Special Metals Co., Ltd. | Case for use in sintering process to produce rare-earth magnet, and method for producing rare-earth magnet |
JP2001028309A (ja) * | 1999-07-14 | 2001-01-30 | Mitsubishi Electric Corp | 磁石およびその磁場成形装置 |
JP2004002998A (ja) * | 2002-04-12 | 2004-01-08 | Sumitomo Special Metals Co Ltd | 希土類合金粉末のプレス成形方法および希土類合金焼結体の製造方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP1788594A4 |
Cited By (17)
Publication number | Priority date | Publication date | Assignee | Title |
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US8153047B2 (en) * | 2007-07-20 | 2012-04-10 | Siemens Aktiengesellschaft | Method for manufacturing of magnet poles |
US20110070118A1 (en) * | 2007-08-20 | 2011-03-24 | Intermetallics Co., Ltd. | METHOD FOR MAKING NdFeB SINTERED MAGNET AND MOLD FOR MAKING THE SAME |
JP2009049202A (ja) * | 2007-08-20 | 2009-03-05 | Inter Metallics Kk | NdFeB系焼結磁石の製造方法およびNdFeB焼結磁石製造用モールド |
US9831034B2 (en) * | 2007-08-20 | 2017-11-28 | Intermetallics Co., Ltd. | Method for making NdFeB sintered magnet and mold for making the same |
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Also Published As
Publication number | Publication date |
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US8545641B2 (en) | 2013-10-01 |
JP2006019521A (ja) | 2006-01-19 |
EP1788594A1 (en) | 2007-05-23 |
US20130343946A1 (en) | 2013-12-26 |
KR101185930B1 (ko) | 2012-09-26 |
EP2597659A3 (en) | 2018-03-21 |
TW200609061A (en) | 2006-03-16 |
EP1788594A4 (en) | 2010-07-14 |
US20070245851A1 (en) | 2007-10-25 |
TWI369259B (ja) | 2012-08-01 |
JP4391897B2 (ja) | 2009-12-24 |
CN1969347B (zh) | 2011-06-01 |
EP1788594B1 (en) | 2017-04-12 |
KR20070043782A (ko) | 2007-04-25 |
EP2597659A2 (en) | 2013-05-29 |
EP2597660A2 (en) | 2013-05-29 |
EP2597660A3 (en) | 2018-03-21 |
CN1969347A (zh) | 2007-05-23 |
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