WO2002095772A1 - Materiau magnetique en oxyde - Google Patents
Materiau magnetique en oxyde Download PDFInfo
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- WO2002095772A1 WO2002095772A1 PCT/JP2002/004922 JP0204922W WO02095772A1 WO 2002095772 A1 WO2002095772 A1 WO 2002095772A1 JP 0204922 W JP0204922 W JP 0204922W WO 02095772 A1 WO02095772 A1 WO 02095772A1
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- H—ELECTRICITY
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- 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
- H01F1/10—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 non-metallic substances, e.g. ferrites, e.g. [(Ba,Sr)O(Fe2O3)6] ferrites with hexagonal structure
- H01F1/11—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 non-metallic substances, e.g. ferrites, e.g. [(Ba,Sr)O(Fe2O3)6] ferrites with hexagonal structure in the form of particles
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- 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
- H01F1/12—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 soft-magnetic materials
- H01F1/34—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 soft-magnetic materials non-metallic substances, e.g. ferrites
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- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/26—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on ferrites
- C04B35/2608—Compositions containing one or more ferrites of the group comprising manganese, zinc, nickel, copper or cobalt and one or more ferrites of the group comprising rare earth metals, alkali metals, alkaline earth metals or lead
- C04B35/2633—Compositions containing one or more ferrites of the group comprising manganese, zinc, nickel, copper or cobalt and one or more ferrites of the group comprising rare earth metals, alkali metals, alkaline earth metals or lead containing barium, strontium or calcium
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- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/26—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on ferrites
- C04B35/2683—Other ferrites containing alkaline earth metals or lead
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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
- H01F1/10—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 non-metallic substances, e.g. ferrites, e.g. [(Ba,Sr)O(Fe2O3)6] ferrites with hexagonal structure
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- C01P2004/00—Particle morphology
- C01P2004/60—Particles characterised by their size
- C01P2004/62—Submicrometer sized, i.e. from 0.1-1 micrometer
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- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2006/00—Physical properties of inorganic compounds
- C01P2006/11—Powder tap density
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- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
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- C01P2006/42—Magnetic properties
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- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3224—Rare earth oxide or oxide forming salts thereof, e.g. scandium oxide
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- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/327—Iron group oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3272—Iron oxides or oxide forming salts thereof, e.g. hematite, magnetite
- C04B2235/3274—Ferrites
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3298—Bismuth oxides, bismuthates or oxide forming salts thereof, e.g. zinc bismuthate
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- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/34—Non-metal oxides, non-metal mixed oxides, or salts thereof that form the non-metal oxides upon heating, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3409—Boron oxide, borates, boric acids, or oxide forming salts thereof, e.g. borax
Definitions
- the present invention relates to an oxide magnetic material, and more particularly to a ferrite magnet powder, a magnet using the magnet powder, and a method for producing the same.
- Ferrite is a general term for compounds made of a divalent cation metal oxide and trivalent iron, and ferrite magnets are used for various purposes such as various types of rotating machines and speakers.
- S r ferrite S r F e 12 ⁇ 1 9 having a magnetoplumbite structure of hexagonal and B a Ferrite (B a F e 12 ⁇ 1 9) is widely used et al is in I have.
- These ferrites are manufactured at relatively low cost by powder metallurgy using iron oxide and carbonates such as strontium (Sr) or barium (Ba) as raw materials.
- the base composition of magnetoplumbite structure (M type) ferrite usually, is represented by the chemical formula AO ⁇ 6 F e 2 ⁇ 3.
- Element A is a metal that becomes a divalent cation and is selected from Sr, Ba, and others.
- coercive force can be obtained by substituting a part of Ba and Sr in Ba ferrite or Sr ferrite with a rare earth element such as La and substituting a part of Fe with Co. It is known that Jr is improved (Bull. Acad. Sci. USSR (Tranl.) Phys. Sec. Vol. 25 (1961) 1405-1408, Japanese Patent Application No. 8-3) Japanese Patent Application Laid-Open No. 6-14, JP-A-10-1499010).
- H In the case of a ferrite in which part of Ba or Sr is replaced by La and part of Fe is replaced by Co, H is used. j is reported to improve, but when part of the above Ba or Sr is replaced by La and part of Fe is replaced by Zn, and compared with ferrite, the improvement of Jr is + min. Not.
- ferrites using rare earth elements such as La as a substitute element such as Co are used as substitute elements, and raw materials for these substitute elements are expensive.
- the manufacturing cost was relatively low compared to rare earth magnets, etc., which could have lost the original characteristics of ferrite magnets.
- L a ⁇ 0 3 only addition and C aO-, S I_ ⁇ 2, CoO, C
- the improvement of the magnetic properties is small by the combined addition of r 2 ⁇ 3 , A ⁇ 2 ⁇ 3 , S r ⁇ , and BaO.
- the present invention has been made in view of the above points, and a main object of the present invention is to provide a ferrite magnet capable of improving the magnetic characteristics at low cost (manufacturing cost is low) and a method of manufacturing the same. Even when sintered at a high temperature, a decrease in coercive force is reduced.
- At least selected from the group consisting of Sr, Ba, Pb and Ca A is also composed of one element,
- composition ratio of each of A, R, Fe and B is determined based on the total amount of the elements A, R, Fe and B.
- R 0.07 atomic% or more ⁇ . 44 atomic% or less
- Oxide magnetic material that satisfies the following relationship.
- the oxide magnetic material according to the above (1) which is:
- AI 2 ⁇ 3 0% by weight or more 5.0; 1% by weight or less
- the raw material mixed powder is calcined at a temperature of 110 ° C. or more and 1300 ° C. or less, whereby
- Equation (1-x) AO ⁇ (x / 2)
- Light are from the group consisting of 3 B a, P b and C a
- At least one element selected R is at least one element selected from the group consisting of rare earth elements including Y and B i, 0. ⁇ 1 ⁇ x ⁇ 0. ⁇ 5, ⁇ .001 ⁇ forming a calcined body of ferrite having a composition of y ⁇ 0.05, 5.2 ⁇ n ⁇ 6.2),
- a method for producing a ferrite calcined body comprising:
- a method for producing a magnet powder comprising:
- the raw material mixed powder is calcined at a temperature of 110 ° C. or more and 13 ⁇ 0 ° C. or less, whereby
- Equation (1 X) AO ⁇ (x / 2) R 2 0 3 -n (F e 2 0 3 ) ⁇ y (B
- the slurry is concentrated, kneaded, molded in a magnetic field or molded in a non-magnetic field, Sintering,
- a method for producing a sintered magnet comprising:
- the composition X, the residual magnetic flux density J r and the coercive force H of the sintered magnet are obtained. This is a graph showing the relationship with j.
- the composition y, the residual magnetic flux density J r of the sintered magnet, and the coercive force H This is a graph showing the relationship with j.
- Figure 5 shows that (1 X) S r O ⁇ (x / 2) L a 2 O s -n (F e 2 ⁇
- 4 is a graph showing the relationship between the sintered body and H c j.
- the inventor of the present invention substituted a part of Sr, Ba, Pb or Ca of hexagonal M-type magnet plumbite structure ferrite with La, further added B, and added the The coercive force, even if the sintering temperature is high, can be determined by carefully examining the ratio of ⁇ and the manufacturing conditions.
- the present invention has been found to have a small decrease in the density, increase the density, and increase the magnetization Jr.
- Oxide magnetic material of the present invention (1 one X) Arufa_ ⁇ ⁇ ( ⁇ / 2) R 2 ⁇ 3 * n (F e 2 0 3) - is represented by y (B 2 0 3), substantially Magne It is a ferrite with a top plan structure.
- A is at least one element selected from the group consisting of Sr, Ba, Pb and Ca.
- Sr is selected than when Ba, Pb and Ca are selected as A.
- Ba is more advantageous depending on the application because the cost is lower.
- R is selected from the group consisting of rare earth elements including Y and Bi, and is at least one element.
- La is selected, the improvement in magnetic properties is more remarkable. For this reason, it is preferable to select La as R, but depending on the application, a low-cost one can be selected.
- n is preferably 5.2 ⁇ n ⁇ 6.2, and more preferably 5.7 ⁇ n ⁇ 6.1.
- composition ratio of each of A, R, Fe and B is based on the total amount of the elements A, R, Fe and B.
- Cobalt hydroxide 0% to 0.4% by weight
- AI 2 0 3 01% more than 5.01 or less
- C o 3 0 4 may be used in place of C O_ ⁇ .
- One element is mixed with the oxide powder, and powder of H 3 B_ ⁇ 3 or B 2 0 3 of.
- the R element can be added as an oxide powder of each element, but a powder of a compound (for example, carbonate, hydroxide, nitrate, chloride, etc.) that becomes an oxide in the subsequent calcination step Alternatively, it can be added as a solution.
- a compound composed of at least two elements selected from the group consisting of rare earth elements including Sr, Ba, Pb, Ca, and Y and Bi, Co, Cu, and Fe may be added.
- the step of preparing the raw material mixed powder means not only the case where the raw material mixed powder is prepared from the beginning as described above, but also the method of purchasing and using the raw material mixed powder prepared by a third party. In some cases, the case where powders produced by third parties are mixed is broadly included.
- the mixed raw material powder is then heated in a batch furnace, continuous furnace, rotary kiln, etc. to a temperature of 110 ° C or more and 130 ° C or less, and M-type magnetic plumbite is produced by solid phase reaction. Form a structural ferrite compound. In this specification, this process is called “calcination”, and the obtained compound is called “calcined body”.
- the calcination time may be from 1 second to 10 hours, preferably from 0.1 hour to 3 hours.
- a ferrite phase is formed by solid phase reaction with an increase in temperature, and the formation of the ferrite phase is completed at about 11 oo ° c. If the calcination step is completed at a temperature of about 11 ° C or less, unreacted J hematite will remain, and magnet properties will deteriorate.
- the calcining temperature exceeds 11 ⁇ ° C, the effect of the present invention is exhibited.However, the effect of the present invention is relatively small when the calcining temperature is 1100 ° C or more and 1150 ° C or less. It is smaller, and the effect increases as the temperature rises. However, if the calcination temperature is higher than 130 CTC, crystal grains may grow too much, which may cause inconvenience such as requiring a long time for grinding in the grinding process.
- the calcination temperature is preferably set in the range of 1100 ° C. to 1300 ° C., and more preferably 1150 ° C. to 1250 ° C.
- the calcined body obtained by these calcining steps is substantially a ferrite having an M-type magnet plumbite structure.
- the ferrite magnet powder according to the present invention can be obtained.
- the average particle size is preferably in the range from 0.5 m to 1.5.
- the powder is subjected to wet pressing, if the powder is too fine, dehydration takes time and the cost increases. For this reason, it is more preferably in the range from 0.6; um to 1.5 rn.
- a more preferable range of the average particle size is 0.8 to um or more and 1.5 m or less.
- the average particle size is determined by air permeation method (Measuring device: Shimadzu Corporation) ⁇ MODE LS S-10 ⁇ ) ⁇ Next, a method for manufacturing a ferrite magnet according to the present invention will be described.
- an M-type magnetoplumbite ferrite calcined body is manufactured by the method described above.
- the calcined body CaC_ ⁇ 3, S I_ ⁇ 2, Co_ ⁇ , cobalt hydroxide, C r 2 ⁇ 3, AI 2 0 3, S r C_ ⁇ 3 and B a C 0 3 (C a C 0 3: O. 3 wt "% or more 1.5 wt%» less, S i 0 2: 0. 2 wt% or more 1.0 wt 96 hereinafter, C oO: 0 wt% or more 0.4 wt% »less, C r 2 ⁇ 3: 0 by weight% or more 5.
- the calcined body is pulverized into fine particles having an average particle size measured by an air permeation method of 0.5 m or more and 1.5 m or less. m or less (air permeation method).
- the fine grinding process consists of dry grinding (coarse grinding exceeding 1.6 m) and wet grinding (fine grinding of 1.6 m or less). It is preferable to carry out in combination.
- cobalt hydroxide During the pulverization step, it is preferable to add cobalt hydroxide to the calcined body in an amount of ⁇ to 0.4% by weight for the purpose of improving magnetic properties.
- an aqueous solvent such as water and various non-aqueous solvents can be used. Solvent and calcined powder mixed during wet grinding The resulting slurry is generated. It is preferable that various known dispersants and surfactants are added to the slurry in a solid content ratio of 0.1% by weight to 2.0% by weight.
- press molding is performed in a magnetic field or in a non-magnetic field while removing the solvent in the slurry.
- the slurry is dried, crushed, granulated, etc., and then pressed in a magnetic field or in the absence of a magnetic field.
- the ferrite magnet product is finally completed through known manufacturing processes such as a degreasing step, a sintering step, a processing step, a washing step, and an inspection step.
- the sintering step may be performed in air at a temperature of, for example, 115 ° C. or more and 1300 ° C. or less for 1 hour or more and 2 hours or less. If the average particle size of the fine particles is 0.8 m or more, grain growth will occur even if the sintering temperature is increased. Therefore, a sintering temperature of 123 ° C or more is preferred. A more preferred sintering temperature range is from 1230 ° C to 126 ° C.
- the average particle size of the sintered magnet obtained in the sintering step is, for example, from 0.0 to 2.0 ⁇ m.
- the rotating machine according to the present invention is characterized in that it has a ferrite magnet manufactured by the above method, and the specific structure itself may be the same as that of a known rotating machine.
- press forming was performed in a magnetic field while removing the solvent in the finely ground slurry (the pressing direction of the press was parallel to the magnetic field, and the magnetic field was 13 kOe).
- the molded body was sintered at 1220 ° C for 1 hour in the air to produce a sintered magnet.
- Figure 2 shows the measurement results when X2 is fixed at 0.03 and n2 is 5.9, and y is changed from ⁇ to ⁇ .15. It is clear from this figure As can be seen, excellent characteristics are obtained in the range of ⁇ . 002 ⁇ y ⁇ . 03. At this time, the amount of B is in the range of 0.03 atomic% or more and 0.5% atomic%. A more preferable range of y is ⁇ .004 ⁇ y ⁇ 0.02. At this time, the amount of B is in the range of ⁇ .06 at%> or more> .35 at%.
- Fig. 3 shows the data obtained when x was fixed at 0.3 and y was fixed at 0.1, and n was changed from 5. ⁇ to 6.5. As is clear from this figure, high characteristics are obtained in the range of 5.2 ⁇ n ⁇ 6.2.
- the dewatering time during press molding is rapidly shortened when the particle size is 0.8 or more. Dehydration is completed in about half the time required when the particle size is 0.8 m and when the particle size is 0.6 m. For this reason, if the particle size is set to ⁇ 0.8 m or more, it is possible to reduce the press cycle by half and to double the productivity compared to the case where the particle size is 0.6 m. . Considering the magnetic properties, it is clear that the range from 0.8 ⁇ to 1.5 m is good. It can be seen that the range from 0.8; ⁇ m to 1.3 m is more preferable.
- Example 1 In the composition of (1-x) S r O (x / 2) L a 2 0 3 n (F e 2 0 3 ) y (B 2 0 3 ), x 2 0.3, y 2 0. ⁇ 1 (Sintered body analysis ⁇ ), Example 1 was repeated except that various raw material powders were blended to obtain n-5.9, and the temperature was changed from 1200 ° C to 1260 ° C. Similarly, a sintered body was produced, and the Jr and Hc ⁇ of the obtained sintered magnet were measured.
- Example 1 As comparative sample (Comparative Example 1), in the set configuration of (1 one X) S r O ⁇ (X / 2) L a 2 0 3 ⁇ n (F e 2 ⁇ 3) 'y (B 2 0 3), Example 1 except that various raw material powders were blended so as to obtain X20, y20, and n25.9, and the sintering temperature was changed from 12 ° C to 126 ° C. A sintered body was produced in the same manner as described above. As apparent from FIG. 6, the sintering temperature towards the present invention is that see that high Takakutechi H c j. It can also be seen that even if the sintering density is high, HcJ does not easily decrease. In particular, it can be seen that high characteristics are obtained at 1230 ° C or higher.
- composition of various raw material powders is such that x ⁇ , y 0 0. ⁇ 1 (analytical value of sintered body), n n A sintered body was prepared in the same manner as in Example 1 except that the sintering temperature was changed from 1200 C to 126 CTC, and the Hk / Hej of the obtained sintered magnet was measured.
- H cj is high when the particle size of the raw material of iron oxide is in the range of ⁇ .5 m to ⁇ .8 m.
- a part of Sr, Ba, Pb or Ca of hexagonal M-type magnet plumbite structure ferrite should be replaced with La, and an appropriate amount of B should be added. Due to the high sintering temperature, H There is little decrease in j, and high density and high magnetization can be obtained. Also, by setting the crushed particle size to ⁇ .8 m or more, dehydration during press molding can be accelerated while improving the magnet performance, so that a high-performance ferrite magnet is provided at low manufacturing cost. It becomes possible.
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Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
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US10/381,133 US6902685B2 (en) | 2001-05-24 | 2002-05-21 | Oxide magnetic material |
KR1020027015461A KR100909702B1 (ko) | 2001-05-24 | 2002-05-21 | 산화물 자성재료 |
EP02771767.7A EP1389785B1 (en) | 2001-05-24 | 2002-05-21 | Oxide magnetic material |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2001156085A JP4576751B2 (ja) | 2001-05-24 | 2001-05-24 | 酸化物磁性材料 |
JP2001-156085 | 2001-05-24 |
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WO2002095772A1 true WO2002095772A1 (fr) | 2002-11-28 |
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PCT/JP2002/004922 WO2002095772A1 (fr) | 2001-05-24 | 2002-05-21 | Materiau magnetique en oxyde |
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US (1) | US6902685B2 (ja) |
EP (1) | EP1389785B1 (ja) |
JP (1) | JP4576751B2 (ja) |
KR (1) | KR100909702B1 (ja) |
CN (1) | CN1264172C (ja) |
WO (1) | WO2002095772A1 (ja) |
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JP5332185B2 (ja) * | 2007-11-16 | 2013-11-06 | ソニー株式会社 | 磁性粉の製造方法、磁性シートの製造方法及びアンテナモジュールの製造方法 |
CN104575910B (zh) * | 2015-02-06 | 2017-05-24 | 江苏新旭磁电科技有限公司 | 电气工程用磁性材料 |
JP7087465B2 (ja) * | 2018-03-07 | 2022-06-21 | Tdk株式会社 | フェライト焼結磁石の製造方法、フェライト粒子の製造方法、及びボンド磁石の製造方法 |
JP7087464B2 (ja) * | 2018-03-07 | 2022-06-21 | Tdk株式会社 | フェライト焼結磁石の製造方法、フェライト粒子の製造方法、及びボンド磁石の製造方法 |
JP7358758B2 (ja) * | 2019-03-27 | 2023-10-11 | Tdk株式会社 | フェライト焼結磁石及びこれを備える回転電気機械 |
WO2023153399A1 (ja) * | 2022-02-10 | 2023-08-17 | 戸田工業株式会社 | 電磁波吸収用フェライト粒子粉末、その製造方法、及びそれを用いた樹脂組成物 |
CN116621572A (zh) * | 2023-04-04 | 2023-08-22 | 宜宾四川大学产业技术研究院 | 经济型复合永磁铁氧体的制备方法 |
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JPH05275221A (ja) * | 1992-03-25 | 1993-10-22 | Sumitomo Special Metals Co Ltd | フェライト磁石及びその製造方法 |
JP2001076919A (ja) * | 1999-07-07 | 2001-03-23 | Tdk Corp | フェライト磁石およびその製造方法 |
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JPS63186402A (ja) | 1987-01-28 | 1988-08-02 | Sumitomo Special Metals Co Ltd | 高抗磁力を有するフェライト磁石の製造方法 |
DE3726667A1 (de) * | 1987-08-11 | 1989-02-23 | Bayer Ag | Feinteilige magnetische borhaltige hexaferritpigmente, verfahren zu ihrer herstellung sowie deren verwendung |
JPH01283802A (ja) | 1988-05-10 | 1989-11-15 | Minebea Co Ltd | Sr系フェライト磁石 |
JP2897871B2 (ja) * | 1995-08-11 | 1999-05-31 | ティーディーケイ株式会社 | 磁石粉末、焼結磁石、ボンディッド磁石および磁気記録媒体 |
JP2922864B2 (ja) | 1996-11-18 | 1999-07-26 | 日立金属株式会社 | フェライト磁石およびその製造方法 |
WO1998038654A1 (fr) * | 1997-02-25 | 1998-09-03 | Tdk Corporation | Materiau magnetique a base d'oxyde, particule de ferrite, aimant obtenu par frittage, aimant issu d'une liaison, support d'enregistrement magnetique et moteur |
JPH11307331A (ja) | 1998-04-24 | 1999-11-05 | Hitachi Metals Ltd | フェライト磁石 |
JP4194013B2 (ja) * | 1999-10-06 | 2008-12-10 | Tdk株式会社 | フェライト磁石の製造方法 |
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2001
- 2001-05-24 JP JP2001156085A patent/JP4576751B2/ja not_active Expired - Lifetime
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2002
- 2002-05-21 WO PCT/JP2002/004922 patent/WO2002095772A1/ja active Application Filing
- 2002-05-21 EP EP02771767.7A patent/EP1389785B1/en not_active Expired - Lifetime
- 2002-05-21 US US10/381,133 patent/US6902685B2/en not_active Expired - Lifetime
- 2002-05-21 CN CNB028012054A patent/CN1264172C/zh not_active Expired - Lifetime
- 2002-05-21 KR KR1020027015461A patent/KR100909702B1/ko active IP Right Grant
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JPH05275221A (ja) * | 1992-03-25 | 1993-10-22 | Sumitomo Special Metals Co Ltd | フェライト磁石及びその製造方法 |
JP2001076919A (ja) * | 1999-07-07 | 2001-03-23 | Tdk Corp | フェライト磁石およびその製造方法 |
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See also references of EP1389785A4 * |
Also Published As
Publication number | Publication date |
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EP1389785A1 (en) | 2004-02-18 |
KR100909702B1 (ko) | 2009-07-29 |
EP1389785B1 (en) | 2016-11-30 |
KR20030025229A (ko) | 2003-03-28 |
JP2002353020A (ja) | 2002-12-06 |
CN1264172C (zh) | 2006-07-12 |
US6902685B2 (en) | 2005-06-07 |
EP1389785A4 (en) | 2010-08-25 |
CN1461487A (zh) | 2003-12-10 |
US20040026654A1 (en) | 2004-02-12 |
JP4576751B2 (ja) | 2010-11-10 |
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