Classifications

• • C—CHEMISTRY; METALLURGY
  • C01—INORGANIC CHEMISTRY
  • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
  • C01G49/00—Compounds of iron
  • C01G49/0018—Mixed oxides or hydroxides
• • C—CHEMISTRY; METALLURGY
  • C01—INORGANIC CHEMISTRY
  • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
  • C01G49/00—Compounds of iron
• • C—CHEMISTRY; METALLURGY
  • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
  • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
  • 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
• • 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
  • H01F1/12—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
  • H01F1/36—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 in the form of particles
• • 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
  • H01F1/12—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
  • H01F1/36—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 in the form of particles
  • H01F1/37—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 in the form of particles in a bonding agent
  • H01F1/375—Flexible bodies
• • C—CHEMISTRY; METALLURGY
  • C01—INORGANIC CHEMISTRY
  • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
  • C01P2002/00—Crystal-structural characteristics
  • C01P2002/60—Compounds characterised by their crystallite size

Definitions

• the present invention relates to a Ni—Zn—Cu ferrite material, and relates to a ferrite powder that can be sintered at a low temperature.
• the present invention also relates to a sintered body and a ferrite sheet using the ferrite powder. .
• inductors used in electronic circuits of electronic devices have been put into practical use from ferrite-type multilayer chip inductors, from winding types in which a copper wire having an insulation coating is wound around a magnetic core or air core bobbin to form a coil. ing.
• This multilayer chip inductor is manufactured through the following manufacturing process. That is, after a conductive pattern is formed by printing or the like using a paste containing an electrode material such as Ag or Ag-Pd on a green sheet formed by forming a paste containing ferrite powder into a sheet shape, these are laminated, It is manufactured in a step of sintering at a predetermined temperature to form an external electrode.
• a conductive pattern is formed by printing or the like using a paste containing an electrode material such as Ag or Ag-Pd on a green sheet formed by forming a paste containing ferrite powder into a sheet shape.
• Ni-based ferrite sintered body excellent in electromagnetic characteristics such as magnetic permeability as a magnetic body for a multilayer chip inductor when sintered at a temperature of 900 ° C. or lower, it is difficult to obtain a Ni-based ferrite sintered body excellent in electromagnetic characteristics such as magnetic permeability as a magnetic body for a multilayer chip inductor.
• Patent Document 1 a borosilicate glass as a sintering aid to generate a liquid phase during sintering and promoting the growth of ferrite particles
• Patent Document 2 a borosilicate glass as a sintering aid to generate a liquid phase during sintering and promoting the growth of ferrite particles
• Patent Document 3 As an application for RFID, there is a method of realizing high permeability by controlling the half width of the XRD diffraction peak of the crystal phase of Ni—Zn—Cu ferrite powder (Patent Document 4).
• Patent Documents 1 to 3 all employ a method in which liquid phase sintering is formed by adding a glass component to promote ferrite particle growth.
• the amount of these additives added is very small and difficult to disperse uniformly, and promotes non-uniform growth of ferrite particles.
• the sintering auxiliary agent is not added, it is necessary to bake at the high temperature of 1060 degreeC or more, and sintering at low temperature is not considered.
• an object of the present invention is to provide a Ni—Zn—Cu ferrite powder that can be sintered at a low temperature in order to solve the above-described problems in the prior art.
• the present invention provides Fe 2 O 3 of 49 mol% or less, NiO 5 to 25 mol%, A Ni—Zn—Cu ferrite powder containing 15 to 40 mol% ZnO, 5 to 15 mol% CuO and 0 to 3 mol% CoO, and having a crystallite size of 180 nm or less (Invention 1) ).
• the present invention is the Ni—Zn—Cu-based ferrite powder according to the present invention 1 having a strain of 0.330 or less (the present invention 2).
• the present invention also relates to the Ni—Zn—Cu ferrite powder according to the present invention 1 or 2, wherein the sintered density becomes 5.00 g / cm 3 or more when fired at 860 ° C. in the atmosphere (the present invention). 3).
• the present invention is a sintered body using the Ni—Zn—Cu based ferrite powder described in any one of the present inventions 1 to 3 (Invention 4).
• the present invention is a ferrite sheet using the Ni—Zn—Cu based ferrite powder described in any one of the present inventions 1 to 3 (Invention 5).
• the Ni—Zn—Cu ferrite powder according to the present invention has a small crystallite size, a ferrite sintered body having a high sintering density can be obtained even when sintered at a low temperature. Further, since the Ni—Zn—Cu ferrite powder according to the present invention can be sintered at a low temperature of 860 ° C., for example, when used in a multilayer inductor in which Ag and magnetic powder are simultaneously fired, the melting point is low. Ag diffusion can be suppressed, and improvement in inductor performance is expected.
• Ni—Zn—Cu ferrite powder according to the present invention will be described.
• the Ni—Zn—Cu based ferrite powder according to the present invention contains Fe, Ni, Zn and Cu as constituent metal elements, and optionally Co.
• the Fe content of the Ni—Zn—Cu ferrite powder according to the present invention is 49 mol% or less in terms of Fe 2 O 3 . When Fe content exceeds 49 mol%, sinterability falls remarkably.
• the Fe content is preferably 48.9 mol% or less, more preferably 48.8 mol% or less.
• the lower limit is about 45 mol%.
• the Ni content of the Ni—Zn—Cu ferrite powder according to the present invention is 5 to 25 mol% in terms of NiO.
• ⁇ ′ decreases, which is not preferable.
• Curie temperature falls and the temperature range which can be used is limited, it is not preferable.
• a Ni content exceeding 25 mol% is also not preferable because ⁇ ′ decreases.
• the Ni content is preferably 6 to 24.9 mol%, more preferably 7 to 24.8 mol%.
• the Zn content of the Ni—Zn—Cu ferrite powder according to the present invention is 15 to 40 mol% in terms of ZnO.
• ⁇ ′ decreases, which is not preferable.
• Curie temperature falls and the temperature range which can be used is limited, it is not preferable.
• a Zn content exceeding 40 mol% is also not preferable because ⁇ ′ decreases.
• the Zn content is preferably 18 to 38 mol%, more preferably 20 to 35 mol%.
• the Cu content of the Ni—Zn—Cu ferrite powder according to the present invention is 5 to 15 mol% in terms of CuO.
• Cu content is less than 5 mol%, sinterability falls and it becomes difficult to manufacture a sintered compact at low temperature.
• ⁇ ′ decreases, which is not preferable.
• the Cu content is preferably 6 to 14 mol%, more preferably 7 to 13 mol%.
• the Ni—Zn—Cu ferrite powder according to the present invention may contain Co.
• the Co content is 0 to 3 mol% in terms of CoO.
• the ferrite core is a ratio of the real part ⁇ ′ to the imaginary part ⁇ ′′ of the complex permeability in the high frequency range.
• Q ( ⁇ ′ / ⁇ ′′) can be improved.
• the Co content is preferably 0 to 2.9 mol%, more preferably 0 to 2.8 mol%, and particularly preferably 0.1 to 2.8 mol%.
• the Ni—Zn—Cu ferrite powder according to the present invention has a crystallite size of 180 nm or less.
• the crystallite size exceeds 180 nm, the particle growth is promoted at the magnetic powder stage, so when the sintered body and the green sheet are fired, the sinterability is lowered and the sintering at a low temperature cannot be performed. . More preferably, it is 175 nm or less, and still more preferably 170 nm or less. The lower limit is about 100 nm.
• the crystallite size can be determined by the method of the example described later. In particular, the crystallite size can be adjusted to the above range by adjusting the BET specific surface area of Fe 2 O 3 which is an Fe raw material to be described later.
• the Ni—Zn—Cu ferrite powder according to the present invention preferably has a crystal strain of 0.330 or less. If the strain exceeds 0.330, ⁇ ′ may decrease, which is not preferable. More preferably, it is 0.325 or less, More preferably, it is 0.320 or less. The lower limit is about 0.100.
• the Ni—Zn—Cu ferrite powder according to the present invention is preferably a spinel ferrite single phase. In addition, the distortion of the crystallite can be obtained by the method of an example described later. The strain of the crystallite can be adjusted by the preliminary firing temperature and the crushing strength of the ferrite powder.
• the Ni—Zn—Cu-based ferrite powder according to the present invention may contain various elements at an impurity level in addition to the above elements as long as the characteristics are not affected.
• adding Bi has an effect of lowering the sintering temperature of ferrite.
• positive Bi addition is not preferable, and Bi is preferably not contained (0 ppm).
• the Ni—Zn—Cu ferrite powder according to the present invention may contain Si as an inevitable impurity with an upper limit of 500 ppm in terms of SiO 2 . It is preferable not to contain Sn etc. (0 ppm).
• the Ni—Zn—Cu based ferrite powder according to the present invention is prepared by mixing raw materials such as oxides, carbonates, hydroxides, oxalates and the like of each element constituting ferrite in a conventional manner.
• the obtained raw material mixture or a coprecipitate obtained by precipitating each element in an aqueous solution is obtained by calcination in the air at a temperature range of 650 to 950 ° C. for 1 to 20 hours and then pulverizing. be able to.
• the pre-baking temperature is preferably 700 to 940 ° C.
• the sintering temperature is preferably 900 ° C. or lower, and therefore the temporary firing temperature is lower (less than 900 ° C.). Is preferred.
• the Fe raw material Fe 2 O 3 preferably has a BET specific surface area of 6.0 m 2 / g or more.
• the BET specific surface area of Fe 2 O 3 is more preferably 6.5 to 40.0 m 2 / g, and even more preferably 7.0 to 30.0 m 2 / g.
• BET specific surface area of Fe 2 O 3 for example, can be controlled such as by regulating or adjusting the particle size in the synthesis stage of Fe 2 O 3, or to adjust the firing temperature, and the crushing strength.
• the sintering aid is not added during the production of the Ni—Zn—Cu ferrite powder, the uneven growth of particles can be suppressed.
• the sintered density of the ferrite sintered body is preferably a high sintered density even at low temperature sintering, and is preferably 5.00 g / cm 3 or more even at low temperature firing at about 860 ° C., for example.
• the upper limit of the sintered density is about 5.40 g / cm 3 .
• the Ni—Zn—Cu based ferrite sintered body according to the present invention has a Ni—Zn—Cu based ferrite powder according to the present invention of 0.3 to 3.0 ⁇ 10 4 t / m 2 using a mold. It is obtained by a so-called green sheet method in which a green body containing a Ni-Zn-Cu ferrite powder according to the present invention is laminated, or a molded body obtained by a so-called powder pressure molding method that pressurizes with pressure.
• the laminated body can be obtained by sintering at 840 to 1050 ° C. for 1 to 20 hours, preferably 1 to 10 hours.
• a molding method a known method can be used, but the above-mentioned powder pressure molding method and the green sheet method are preferable.
• the sintering temperature is lower than 840 ° C.
• the sintered density is lowered, so that sufficient electromagnetic characteristics cannot be obtained, and the mechanical strength of the sintered body is lowered.
• the sintering temperature exceeds 1050 ° C.
• the sintered body is likely to be deformed, making it difficult to obtain a sintered body having a desired shape.
• an electrode material such as Ag or Ag-Pd and a laminate of ferrite are fired at the same time, so the electrode disconnection and the inherent properties of ferrite deteriorate due to the interfacial reaction (interdiffusion) between the electrode and ferrite.
• a more preferable sintering temperature is 860 to 1040 ° C.
• the sintering temperature is preferably 900 ° C. or lower.
• the Ni—Zn—Cu ferrite powder of the present invention is used. Is not co-fired with an electrode material such as Ag or Ag—Pd, the upper limit of the sintering temperature can be 1050 ° C.
• Ni—Zn—Cu-based ferrite sintered body according to the present invention can be used as a magnetic material for multilayer chip inductors, inductance elements, and other electronic components by taking a predetermined shape according to the application.
• a green sheet is a paint by mixing the Ni—Zn—Cu ferrite powder with a binder, a plasticizer, a solvent, etc., and the paint is formed to a thickness of several ⁇ m to several hundred ⁇ m using a doctor blade type coater or the like. The sheet is formed after being formed and then dried. After this sheet is stacked, a laminated body is formed by applying pressure, and the laminated body is sintered at a predetermined temperature according to the application, whereby a laminated chip inductor, an inductance element, and other electronic components can be obtained.
• the green sheet in the present invention contains 2 to 20 parts by weight of the binder and 0.5 to 15 parts by weight of the plasticizer with respect to 100 parts by weight of the Ni—Zn—Cu ferrite powder according to the present invention.
• the binder contains 4 to 15 parts by weight and the plasticizer 1 to 10 parts by weight.
• the solvent may remain due to insufficient drying after film formation.
• you may add well-known additives, such as a viscosity modifier, as needed.
• binding materials are polyvinyl butyral, polyacrylic acid ester, polymethyl methacrylate, vinyl chloride, polymethacrylic acid ester, ethylene cellulose, abietic acid resin, and the like.
• a preferred binding material is polyvinyl butyral.
• the binding material When the binding material is less than 2 parts by weight, the green sheet becomes brittle, and in order to have strength, a content exceeding 20 parts by weight is not necessary.
• Plasticizers include benzyl-n-butyl phthalate, butyl butyl phthalyl glycolate, dibutyl phthalate, dimethyl phthalate, polyethylene glycol, phthalate ester, butyl stearate, methyl agitate and the like.
• the plasticizer When the plasticizer is less than 0.5 parts by weight, the green sheet becomes hard and cracks are likely to occur. When the plasticizer exceeds 15 parts by weight, the green sheet becomes soft and difficult to handle.
• the solvent is out of the above range, so that the multilayer chip inductor, inductance element, and other electronic components obtained by sintering the sheet are likely to have variations in characteristics.
• Solvent types are acetone, benzene, butanol, ethanol, methyl ethyl ketone, toluene, propyl alcohol, isopropyl alcohol, n-butyl acetate, 3methyl-3methoxy-1-butanol, and the like.
• the lamination pressure is preferably 0.2 ⁇ 10 4 to 0.6 ⁇ 10 4 t / m 2 .
• a Ni—Zn—Cu ferrite sintered body can be used in the form of a plate to form a ferrite sheet.
• the thickness of the plate-like ferrite sintered body in the present invention is preferably 0.01 to 1 mm. More preferably, it is 0.02 to 1 mm, and still more preferably 0.03 to 0.5 mm.
• an adhesive layer can be provided on at least one surface of the ferrite sintered plate.
• the thickness of the adhesive layer is preferably 0.001 to 0.1 mm.
• a protective layer can be provided on at least one surface of the ferrite sintered plate.
• the thickness of the protective layer is preferably 0.001 to 0.1 mm.
• a double-sided adhesive tape can be mentioned. It does not restrict
• an adhesive layer, a flexible and stretchable film or sheet, an adhesive layer, and a release sheet may be sequentially laminated on one side of the ferrite sintered plate.
• the protective layer in the present invention can enhance the reliability and durability against powder falling when the sintered ferrite plate is divided by providing this.
• the protective layer is not particularly limited as long as it is a resin that extends without breaking when the ferrite sheet is bent, and examples thereof include a PET film.
• the ferrite sheet according to the present invention starts with at least one groove provided in advance on at least one surface of the sintered ferrite plate in order to adhere and adhere to the bent portion and prevent cracking during use.
• the ferrite sintered plate may be configured to be separable.
• the groove may be continuous or intermittently formed, and can be substituted for the groove by forming a large number of minute recesses.
• the groove is preferably U-shaped or V-shaped in cross section.
• the ferrite sheet according to the present invention it is preferable to divide the ferrite sintered plate into small pieces in advance so that the ferrite sheet adheres and adheres to the bent portion and prevents cracking during use.
• the ferrite sintered plate is divided in advance from at least one groove provided on at least one surface of the ferrite sintered plate, or the ferrite sintered plate is divided into small pieces without forming a groove. Either method may be used.
• the ferrite sintered plate is divided into triangles, quadrilaterals, polygons of any size or combinations thereof by grooves.
• the length of one side of a triangle, quadrilateral, or polygon is usually 1 to 12 mm, and when the adhesion surface of the adherend is a curved surface, it is preferably 1 mm or more and 1/3 or less of the radius of curvature thereof, More preferably, it is 1 mm or more and 1/4 or less.
• the groove When the groove is formed, it can be intimately or substantially adhered to a cylindrical side curved surface and a surface with some unevenness as well as a flat surface without cracking indefinitely at a place other than the groove.
• the width of the opening of the groove formed in the ferrite sintered plate is usually preferably 250 ⁇ m or less, more preferably 1 to 150 ⁇ m. When the width of the opening exceeds 250 ⁇ m, the decrease in the magnetic permeability of the ferrite sintered plate becomes large, which is not preferable.
• the depth of the groove is usually 1/20 to 3/5 of the thickness of the ferrite sintered plate. In the case of a thin sintered ferrite plate having a thickness of 0.1 mm to 0.2 mm, the depth of the groove is preferably 1/20 to 1/4 of the thickness of the sintered ferrite plate, more preferably 1 / 20 to 1/6.
• Crystallite size, strain, lattice constant The crystallite size, strain, and lattice constant of the ferrite were measured in the same manner as in the X-ray diffraction using the TOPAS software Ver. It was evaluated at 4.
• the initial magnetic permeability of the ring core was measured at frequencies of 100 kHz and 1 MHz using an impedance / material analyzer E4991A (manufactured by Agilent Technologies).
• the sintered density of the above-described ferrite sintered body for measuring magnetic properties was determined by calculating the outer diameter, inner diameter dimension and weight.
• Example 1 Each oxide raw material was weighed so that the composition of Ni—Zn—Cu ferrite was a predetermined composition, wet mixed, and then the mixed slurry was filtered and dried to obtain a raw material mixed powder (Fe 2 As the O 3 raw material, iron oxide (1) in Table 1 was used).
• the calcined product obtained by firing the raw material mixed powder in the atmosphere at 750 to 850 ° C. for 2 hours was pulverized with a vibration mill to obtain the Ni—Zn—Cu ferrite powder according to the present invention.
• the composition, crystallite size, strain and lattice constant of the obtained powder are shown in Table 2.
• Ni—Zn—Cu ferrite powder was formed into a molded body by the method described above.
• Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body obtained by sintering this molded body in the atmosphere at a sintering temperature of 860 to 920 ° C. for 2 hours.
• Examples 2 and 3 A Ni—Zn—Cu ferrite powder was obtained in the same manner as in Example 1 except that the composition range was variously changed.
• Table 2 shows the composition, crystallite size and strain of the obtained Ni—Zn—Cu ferrite powder.
• Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body produced in the same manner as in Example 1 using the obtained Ni—Zn—Cu ferrite powder.
• Examples 4, 5 A Ni—Zn—Cu—Co ferrite powder was obtained in the same manner as in Example 1 except that the composition range was changed and Co was added. The composition, crystallite size and strain of the obtained Ni—Zn—Cu—Co ferrite powder are shown in Table 2. Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body produced in the same manner as in Example 1 using the obtained Ni—Zn—Cu—Co ferrite powder.
• Comparative Example 1 A Ni—Zn—Cu ferrite powder was obtained in the same manner as in Example 1 except that the composition range was variously changed.
• Table 2 shows the composition, crystallite size and strain of the obtained Ni—Zn—Cu ferrite powder.
• Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body produced in the same manner as in Example 1 using the obtained Ni—Zn—Cu ferrite powder.
• Comparative Example 2 A Ni—Zn—Cu ferrite powder was obtained in the same manner as in Example 1 except that the iron oxide raw material (2) shown in Table 1 was used as the Fe 2 O 3 raw material. Table 2 shows the composition, crystallite size and strain of the obtained Ni—Zn—Cu ferrite powder. Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body produced in the same manner as in Example 1 using the obtained Ni—Zn—Cu ferrite powder.
• Comparative Example 3 A Ni—Zn—Cu ferrite powder was obtained in the same manner as in Example 1 except that the iron oxide raw material (3) shown in Table 1 was used as the Fe 2 O 3 raw material.
• Table 2 shows the composition, crystallite size and strain of the obtained Ni—Zn—Cu ferrite powder.
• Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body produced in the same manner as in Example 1 using the obtained Ni—Zn—Cu ferrite powder.
• Comparative Example 4 A Ni—Zn—Cu ferrite powder was obtained in the same manner as in Example 1 except that the iron oxide raw material (4) shown in Table 1 was used as the Fe 2 O 3 raw material.
• Table 2 shows the composition, crystallite size and strain of the obtained Ni—Zn—Cu ferrite powder.
• Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body produced in the same manner as in Example 1 using the obtained Ni—Zn—Cu ferrite powder.
• Comparative Example 5 A Ni—Zn—Cu—Co ferrite powder was obtained in the same manner as in Example 4 except that the iron oxide raw material (2) shown in Table 1 was used as the Fe 2 O 3 raw material. The composition, crystallite size and strain of the obtained Ni—Zn—Cu—Co ferrite powder are shown in Table 2. Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body produced in the same manner as in Example 1 by using the obtained Ni—Zn—Cu—Co ferrite powder.
• Comparative Example 6 A Ni—Zn—Cu—Co ferrite powder was obtained in the same manner as in Example 5 except that the iron oxide raw material (2) shown in Table 1 was used as the Fe 2 O 3 raw material. The composition, crystallite size and strain of the obtained Ni—Zn—Cu—Co ferrite powder are shown in Table 2. Table 2 shows the sintered density and initial permeability (100 kHz, 1 MHz) of a ferrite sintered body produced in the same manner as in Example 1 by using the obtained Ni—Zn—Cu—Co ferrite powder.
• the Ni—Zn—Cu ferrite powder according to the present invention has a sintered density of 5.00 g / cm 3 or more even when sintered at a low temperature such as 860 ° C., and the magnetic permeability at 100 kHz and 1 MHz is as follows. When compared at the same sintering temperature, it is higher than in the comparative example. Therefore, it is suitable as a precursor of a ferrite sintered body and a ferrite sheet, and is also suitable as a magnetic powder for multilayer chip inductors, inductance elements, and other electronic components.

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• 2019
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