WO2016032001A1 - MnZn系フェライトおよびその製造方法 - Google Patents
MnZn系フェライトおよびその製造方法 Download PDFInfo
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- WO2016032001A1 WO2016032001A1 PCT/JP2015/074622 JP2015074622W WO2016032001A1 WO 2016032001 A1 WO2016032001 A1 WO 2016032001A1 JP 2015074622 W JP2015074622 W JP 2015074622W WO 2016032001 A1 WO2016032001 A1 WO 2016032001A1
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- 229910000859 α-Fe Inorganic materials 0.000 title claims abstract description 64
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 25
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 25
- 239000001301 oxygen Substances 0.000 claims abstract description 25
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 20
- 229910006404 SnO 2 Inorganic materials 0.000 claims description 17
- 238000010304 firing Methods 0.000 claims description 17
- 229910015902 Bi 2 O 3 Inorganic materials 0.000 claims description 15
- 229910052718 tin Inorganic materials 0.000 claims description 15
- 230000008859 change Effects 0.000 claims description 14
- 229910052758 niobium Inorganic materials 0.000 claims description 14
- 230000004907 flux Effects 0.000 claims description 13
- 229910052715 tantalum Inorganic materials 0.000 claims description 12
- 229910020599 Co 3 O 4 Inorganic materials 0.000 claims description 11
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 11
- 239000012298 atmosphere Substances 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 229910052797 bismuth Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000000843 powder Substances 0.000 claims description 3
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 abstract 4
- ZKATWMILCYLAPD-UHFFFAOYSA-N niobium pentoxide Chemical compound O=[Nb](=O)O[Nb](=O)=O ZKATWMILCYLAPD-UHFFFAOYSA-N 0.000 abstract 4
- XOLBLPGZBRYERU-UHFFFAOYSA-N tin dioxide Chemical compound O=[Sn]=O XOLBLPGZBRYERU-UHFFFAOYSA-N 0.000 abstract 4
- VTYYLEPIZMXCLO-UHFFFAOYSA-L Calcium carbonate Chemical compound [Ca+2].[O-]C([O-])=O VTYYLEPIZMXCLO-UHFFFAOYSA-L 0.000 abstract 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract 2
- WMWLMWRWZQELOS-UHFFFAOYSA-N bismuth(iii) oxide Chemical compound O=[Bi]O[Bi]=O WMWLMWRWZQELOS-UHFFFAOYSA-N 0.000 abstract 2
- PBCFLUZVCVVTBY-UHFFFAOYSA-N tantalum pentoxide Inorganic materials O=[Ta](=O)O[Ta](=O)=O PBCFLUZVCVVTBY-UHFFFAOYSA-N 0.000 abstract 2
- 229910000019 calcium carbonate Inorganic materials 0.000 abstract 1
- UBEWDCMIDFGDOO-UHFFFAOYSA-N cobalt(II,III) oxide Inorganic materials [O-2].[O-2].[O-2].[O-2].[Co+2].[Co+3].[Co+3] UBEWDCMIDFGDOO-UHFFFAOYSA-N 0.000 abstract 1
- 229910052681 coesite Inorganic materials 0.000 abstract 1
- 229910052906 cristobalite Inorganic materials 0.000 abstract 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 abstract 1
- 239000000377 silicon dioxide Substances 0.000 abstract 1
- 229910052682 stishovite Inorganic materials 0.000 abstract 1
- 229910052905 tridymite Inorganic materials 0.000 abstract 1
- 239000013078 crystal Substances 0.000 description 26
- 238000000034 method Methods 0.000 description 17
- 239000000203 mixture Substances 0.000 description 16
- 230000008569 process Effects 0.000 description 12
- 229910021645 metal ion Inorganic materials 0.000 description 11
- 239000011029 spinel Substances 0.000 description 11
- 229910052596 spinel Inorganic materials 0.000 description 11
- 230000001747 exhibiting effect Effects 0.000 description 6
- -1 CaCO 3 Inorganic materials 0.000 description 5
- 238000001816 cooling Methods 0.000 description 5
- 238000011156 evaluation Methods 0.000 description 5
- 230000035699 permeability Effects 0.000 description 5
- 238000004804 winding Methods 0.000 description 5
- 239000011230 binding agent Substances 0.000 description 3
- 239000000460 chlorine Substances 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 230000005415 magnetization Effects 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 230000002123 temporal effect Effects 0.000 description 3
- 230000002159 abnormal effect Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
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- 239000012299 nitrogen atmosphere Substances 0.000 description 2
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- 230000000630 rising effect Effects 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- ZAMOUSCENKQFHK-UHFFFAOYSA-N Chlorine atom Chemical compound [Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 description 1
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 239000004372 Polyvinyl alcohol Substances 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 229910052801 chlorine Inorganic materials 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000005674 electromagnetic induction Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 230000020169 heat generation Effects 0.000 description 1
- 239000011019 hematite Substances 0.000 description 1
- 229910052595 hematite Inorganic materials 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- LIKBJVNGSGBSGK-UHFFFAOYSA-N iron(3+);oxygen(2-) Chemical compound [O-2].[O-2].[O-2].[Fe+3].[Fe+3] LIKBJVNGSGBSGK-UHFFFAOYSA-N 0.000 description 1
- 230000005381 magnetic domain Effects 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 229920002451 polyvinyl alcohol Polymers 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000011802 pulverized particle Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
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- 230000007480 spreading Effects 0.000 description 1
- 238000003892 spreading Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000036962 time dependent Effects 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
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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
- H01F1/12—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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- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
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- C01G45/02—Oxides; Hydroxides
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- C01G49/00—Compounds of iron
- C01G49/02—Oxides; Hydroxides
- C01G49/06—Ferric oxide [Fe2O3]
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- 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
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- C04B2235/6583—Oxygen containing atmosphere, e.g. with changing oxygen pressures
- C04B2235/6584—Oxygen containing atmosphere, e.g. with changing oxygen pressures at an oxygen percentage below that of air
Definitions
- the present invention relates to a MnZn-based ferrite used for electronic parts such as transformers, inductors, reactors, choke coils, and the like used in various power supply apparatuses and a method for manufacturing the same.
- Electric vehicles such as EVs (Electric Vehicles) and PHEVs (Plug-in Hybrid Electric Vehicles), which are rapidly spreading in recent years, are equipped with devices such as high-power electric motors and chargers. They use electronic components that can withstand high voltages and large currents.
- the electronic component is basically composed of a coil and a magnetic core, and the magnetic core is made of a magnetic material such as MnZn ferrite.
- MnZn-based ferrites that are designed to have a minimum core loss (also called power loss) of 100 ° C. or less are used.
- a minimum core loss also called power loss
- Pcv minimum temperature of the core loss Pcv at a high temperature exceeding 100 ° C.
- low core loss is also required over a wide temperature range.
- the core loss Pcv of ferrite consists of hysteresis loss Ph, eddy current loss Pe, and residual loss Pr.
- the hysteresis loss Ph increases in proportion to the frequency due to the DC hysteresis
- the eddy current loss Pe increases in proportion to the square of the frequency due to the electromotive force generated by the eddy current generated by the electromagnetic induction action.
- the residual loss Pr is a remaining loss caused by domain wall resonance or the like, and becomes apparent at a frequency of 500 kHz or more. That is, the hysteresis loss Ph, the eddy current loss Pe, and the residual loss Pr vary depending on the frequency, and the ratio of the total core loss varies depending on the frequency band.
- the magnetic core loss of MnZn-based ferrite has temperature dependence, and the hysteresis loss is small at a temperature where the magnetocrystalline anisotropy constant K1 is 0, and has a minimum value with respect to the temperature. Further, since the initial permeability ⁇ i becomes maximum at that temperature, it is also called a secondary peak of the initial permeability ⁇ i. Since the core loss has a minimum value with respect to temperature, the temperature at which the core loss is minimized is usually adjusted by the magnetocrystalline anisotropy constant K1 in anticipation of heat generation due to the core loss, and the temperature is exposed to the electronic component. The temperature is set slightly higher than the ambient temperature to prevent the ferrite from losing its magnetism due to thermal runaway.
- the temperature at which the magnetic core loss is minimized is mainly a metal exhibiting a positive magnetocrystalline anisotropy constant K1 among the metal ions constituting the spinel in the MnZn-based ferrite.
- the amount of ions and the amount of metal ions exhibiting a negative magnetocrystalline anisotropy constant K1 can be appropriately adjusted and varied depending on the sum.
- Metal ions constituting spinel include Fe 2+ and Co 2+ as metal ions exhibiting positive K1, and Fe 3+ , Mn 2+ , Ni 2+ and the like as metal ions exhibiting negative K1.
- Patent Document 1 includes Fe 2 O 3 : 52.0 to 55.0 mol%, MnO: 32.0 to 44.0 mol%, ZnO: 4.0 to 14.0 mol% as main components, An MnZn-based ferrite having CaO: 200 to 1000 ppm, SiO 2 : 50 to 200 ppm, Bi 2 O 3 : 500 ppm or less, Ta 2 O 5 : 200 to 800 ppm, CoO: 4000 ppm or less is disclosed.
- Bi 2 O 3 is added to obtain a MnZn-based ferrite having a low magnetic core loss in a wider temperature range.
- Patent Literature 2 and Patent Literature 3 disclose controlling the atmospheric oxygen concentration during firing. Firing is basically performed by a temperature raising process, a high temperature holding process, and a temperature lowering process. In Patent Document 2 and Patent Document 3, the atmospheric oxygen concentration in the high temperature holding process and the temperature lowering process is strictly controlled.
- Patent Document 1 does not describe the temporal change in magnetic characteristics.
- the atmospheric oxygen concentration It has been found that attempts to suppress changes over time in magnetic properties by control may increase the core loss. Therefore, an object of the present invention is to provide a MnZn-based ferrite having a low magnetic core loss, further suppressing a change in magnetic characteristics with time under a high temperature environment, and suppressing an increase in magnetic core loss, and a method for manufacturing the same.
- the first invention includes Fe, Mn, and Zn as main components, Si, Ca, Co, and Bi as subcomponents, at least one of Ta or Nb, and at least one of Ti or Sn.
- Is composed of Fe 2 O 3 , ZnO, and MnO the total amount is 100 mol%
- Fe is 53.25 mol% to 54.00 mol% in terms of Fe 2 O 3
- Zn is in terms of ZnO 2.50 mol% or more and 8.50 mol% or less
- Mn as the balance in terms of MnO, Si in excess of 0.001 mass% in terms of SiO 2 and less than 0.02 mass%
- Ca in the form of CaCO 3 .
- Co is less than 0.5 mass% in terms of Co 3 O 4 (0 is not included)
- Bi is less than 0.05 mass% in terms of Bi 2 O 3 (0 is included) not
- (including 0) in terms of TiO 2 less than 0.3 wt% of Ti Sn in the terms of SnO 2
- the total amount of Ta 2 O 5 and Nb 2 O 5 that satisfy less than 0.3% by mass (including 0) is less than 0.05% by mass (not including 0), and the converted TiO 2 And SnO 2 is less than 0.3% by mass (excluding 0), and the core loss (Pcv130A) at 130 ° C.
- the MnZn-based ferrite is characterized in that the change rate Ps of the core loss represented by the following formula is 5% or less using the core loss (Pcv130B) at 130 ° C. after being held at 96 ° C. for 96 hours.
- Ps (%) [(Pcv130B ⁇ Pcv130A) / Pcv130A] ⁇ 100
- Si is 0.003 to 0.015 mass% in terms of SiO 2
- Ca is 0.06 to 0.3 mass% in terms of CaCO 3
- Co is Co 3 O 4.
- Bi in the range of 0.0075 mass% or more and 0.04 mass% or less in terms of Bi 2 O 3 and containing Ta or Nb alone
- Ta is Ta 2 O 5 0.04 mass% or more 0.015% by mass in terms of less
- the core loss between 100 ° C. and 150 ° C. is preferably 500 kW / m 3 or less, and the minimum temperature of the core loss is preferably between 110 ° C. and 150 ° C.
- the magnetic core loss (Pcv130B) at 130 ° C. after being held at 200 ° C. for 96 hours is preferably 400 kW / m 3 or less.
- the second invention is a method for producing an MnZn-based ferrite, and includes a firing step of firing the compact by molding the main component and subcomponent oxide powders defined in the first invention into a compact.
- the firing step includes a temperature raising step, a high temperature holding step, and a temperature lowering step, wherein the temperature in the high temperature holding step is between 1250 ° C. and 1400 ° C., and the oxygen concentration in the atmosphere in the high temperature holding step is set to 0.00% by volume.
- the MnZn-based ferrite manufacturing method is characterized in that the oxygen concentration at 1200 ° C. is 0.5% or less and the oxygen concentration at 1100 ° C. is 0.1% or less in the temperature lowering step.
- a MnZn-based ferrite having a low magnetic core loss and capable of suppressing an increase in magnetic core loss by suppressing a change with time in magnetic characteristics under a high temperature environment and a method for manufacturing the same.
- the MnZn-based ferrite according to an embodiment of the present invention a magnetic core using the same, and a manufacturing method thereof will be described in detail.
- the present invention is not limited to this, and can be appropriately changed within the scope of the technical idea.
- composition of MnZn ferrite In order to reduce the magnetic core loss Pcv at a desired temperature, the composition is optimized so that the metal ion exhibiting the positive magnetocrystalline anisotropy constant K1 and the metal ion exhibiting the negative magnetocrystalline anisotropy constant K1 that constitute the spinel. It is necessary to adjust the amount of the above as appropriate. However, the degree of freedom in selecting the composition is small because of limitations due to required magnetic characteristics other than the core loss Pcv, such as the saturation magnetic flux density Bs, the Curie temperature Tc, and the initial permeability ⁇ i.
- Fe 2 O 3 is 53.25 mol% or more and 54.00 mol% or less as a main component so that the minimum temperature of magnetic core loss is between 110 ° C. and 150 ° C.
- ZnO was selected from the range of 2.50 mol% to 8.50 mol%, with the balance being MnO.
- the main component mainly refers to the elements and compounds constituting spinel ferrite, while the subcomponent refers to the elements and compounds that are used auxiliary to the formation of the spinel ferrite. Containing elements.
- the constituents of spinel ferrite, such as Co have a smaller content than the main component and are used as subcomponents.
- the MnZn-based ferrite of the present invention contains Fe, Mn, and Zn as main components, Si, Ca, Co, and Bi as subcomponents, at least one of Ta or Nb, and at least one of Ti or Sn.
- Si and Ca are in a predetermined range, a ferrite sintered body (for example, a magnetic core) formed by firing MnZn-based ferrite, high-resistance Si and Ca are present in the crystal grain boundaries, By insulating the crystal grains, the volume resistivity ⁇ is increased and the relative loss coefficient tan ⁇ / ⁇ i is reduced.
- a ferrite sintered body for example, a magnetic core
- SiO 2 and Si including less than 0.04 mass percent 0.4 wt% of Ca in terms of CaCO 3.
- it is 0.003 to 0.015 mass% Si in terms of SiO 2 and 0.06 to 0.3 mass% Ca in terms of CaCO 3 . More preferably, Ca is more than 0.06 mass% and 0.3 mass% or less in terms of CaCO 3 .
- Si is segregated exclusively at the crystal grain boundary and its triple point, but Ca is dissolved in the spinel phase in the course of the firing process, and a part of the Ca may be dissolved and remain in the crystal grain after firing.
- Increasing the amount of Ca dissolved in the spinel phase increases the resistance in the crystal grains and increases the volume resistivity ⁇ , but relatively decreases the Ca at the grain boundaries.
- appropriately adjust Ca dissolved in the spinel phase and Ca segregated at the crystal grain boundary to increase the resistance in the crystal grain and increase the resistance. It is effective to form a grain boundary. Such adjustment can be performed by controlling the firing temperature and firing atmosphere described later.
- Co to be added is set to be less than 0.5 mass% (excluding 0) in terms of Co 3 O 4 . More preferably, it contains 0.16 mass% or more and 0.4 mass% or less of Co in terms of Co 3 O 4 . More preferably, Co is 0.16% by mass or more and less than 0.4% by mass in terms of Co 3 O 4 .
- Bi segregates exclusively at the crystal grain boundary and its triple point, and contributes to the formation of a high-resistance crystal grain boundary. Moreover, it functions as a sintering accelerator and densifies the crystal structure. In addition, the crystal grain size increases, the hysteresis loss is reduced, and the magnetic core loss is reduced. Bi is included in an amount of less than 0.05% by mass (not including 0) in terms of Bi 2 O 3 . If it is too much, abnormal sintering is caused and the core loss is increased. Preferably it is 0.0075 mass% or more and 0.04 mass% or less Bi in terms of Bi 2 O 3 . More preferably, Bi is 0.01% by mass or more and less than 0.04% by mass in terms of Bi 2 O 3 .
- Ta and Nb are Va group elements, and these components appear in the crystal grain boundary layer together with Si and Ca, and contribute to increasing the resistance of the grain boundary layer and thereby reducing the loss.
- Ta and Nb may be included singly or both. If containing alone respectively Ta 2 O 5, Nb 2 O 5 in terms is less than 0.05 mass%, in the case of including both the Ta and Nb, in terms have been of Ta 2 O 5 and Nb 2 O 5
- the total amount is preferably less than 0.05% by mass (excluding 0). More preferably, when Ta or Nb is contained alone, Ta 2 O 5 and Nb 2 O 5 are each 0.015% by mass or more and 0.04% by mass or less, and both Ta and Nb are contained.
- the total amount of Ta 2 O 5 and Nb 2 O 5 is 0.015 mass% or more and 0.04 mass% or less.
- Nb is contained alone, it is more preferably 0.015% by mass or more and less than 0.04% by mass in terms of Nb 2 O 5 .
- the amount exceeds the predetermined amount, the magnetic core loss is increased, and when the amount is small, it is difficult to obtain the effect of reducing the core loss.
- the core loss is further improved in synergy with other subcomponents including Bi, and the magnetic properties in a high temperature environment are improved. Changes over time can be suppressed.
- Sn and Ti are tetravalent stable metal ions which can be dissolved in the crystal grains to increase the volume resistivity ⁇ and reduce the core loss Pcv.
- Ti and Sn exist exclusively in the crystal grains, but some of them may exist in the crystal grain boundaries. When contained alone, Ti is preferably contained in an amount of less than 0.3% by mass in terms of TiO 2 and Sn is contained in an amount of less than 0.3% by mass in terms of SnO 2 .
- the total amount of TiO 2 and SnO 2 converted is preferably less than 0.3% by mass (not including 0). More preferably, when Ti or Sn is contained alone, Ti and Sn are 0.02% by mass or more and 0.2% by mass or less in terms of TiO 2 and SnO 2 , respectively, even when both Ti and Sn are contained.
- the total amount of TiO 2 and SnO 2 is 0.02 mass% or more and 0.2 mass% or less.
- the raw materials constituting the MnZn-based ferrite may include sulfur S, chlorine Cl, phosphorus P, boron B, etc. as impurities.
- these impurities are not particularly defined, but it is empirically known that reduction in magnetic core loss and improvement in magnetic permeability can be obtained by reducing them.
- S a compound with Ca is generated and segregated as a foreign substance at the crystal grain boundary, thereby reducing the volume resistivity ⁇ and increasing the eddy current loss.
- impurities are reduced.
- S is 0.03% by mass or less
- Cl is 0.01% by mass or less
- P is 0.001% by mass or less
- B is reduced.
- the content is preferably 0.0001% by mass or less.
- MnZn-based ferrite After weighing the raw materials so as to have a predetermined composition amount as MnZn-based ferrite, Fe 2 O 3 , MnO (using Mn 3 O 4 ) and ZnO as the main components are calcined and pulverized, and then the auxiliary components SiO 2 , CaCO 3 , Co 3 O 4 , Bi 2 O 3 , Ta 2 O 5 or Nb 2 O 5 and TiO 2 or SnO 2 are appropriately added and mixed, and a binder is added to granulate and mold After that, it is subjected to firing.
- the fired MnZn-based ferrite may be referred to as a ferrite sintered body.
- the firing step includes a high temperature holding step for holding in a predetermined temperature range, a temperature rising step before the high temperature holding step, and a temperature lowering step subsequent to the high temperature holding step, and any one of room temperature to 750 ° C. to 950 ° C.
- the temperature raising process during the course of temperature is performed in the atmosphere, and is replaced with N 2 at any temperature between 750 ° C. and 950 ° C., and is set at any temperature between 1250 ° C. and 1400 ° C.
- the oxygen concentration is preferably controlled in the range of 0.2% to 0.7%
- the N 2 atmosphere is preferably set from the equilibrium oxygen partial pressure.
- the temperature increase rate in a temperature rising process suitably according to the carbon residual state in a binder removal, and a composition.
- it is in the range of 50 to 200 ° C./hr.
- Ca is segregated at the grain boundary as the oxygen concentration is increased, and solid solution in the spinel phase occurs in a low oxygen partial pressure to N 2 atmosphere at a high temperature exceeding 1100 ° C. Therefore, in the present invention, it is preferable to adjust the oxygen partial pressure to segregate Ca to the grain boundary and to appropriately control the solid solution in the crystal grains to reduce the core loss.
- the temperature reduction rate control according to the composition is adopted as the firing condition, and the cooling rate from the high temperature holding temperature to 1000 ° C. is preferably 50 to 150 ° C./hr, 1000 ° C. to 900 ° C.
- the cooling rate is from 50 to 300 ° C./hr, and the cooling rate from 900 ° C. to 600 ° C. is from 150 to 500 ° C./hr.
- b is large, the oxygen concentration decreases and wustite precipitates, and neither the crystal grains nor the grain boundary layer is sufficiently oxidized, resulting in a low resistance. More preferably, a is 6.4 to 11.5, b is 10,000 to 18000, the oxygen concentration in the high temperature holding step is 0.7% or less, the oxygen concentration at 1200 ° C. is 0.5% or less, and at 1100 ° C. By controlling the oxygen concentration to 0.1% or less, it is possible to further reduce the time-dependent change in magnetic characteristics under a high temperature environment.
- the average crystal grain size of the MnZn-based ferrite is appropriately set depending on the frequency of use of the electronic component using the MnZn-based ferrite. However, if the frequency is 500 kHz or higher, the eddy current loss is reduced to 5 ⁇ m or less and the crystal grain It is preferable to subdivide the magnetic domain to reduce loss due to domain wall resonance, and if the frequency is less than 500 kHz, the coercive force Hc is reduced to more than 5 ⁇ m and not more than 30 ⁇ m to reduce hysteresis loss. Is preferred.
- the MnZn-based ferrite was weighed so as to have compositions with different amounts of Bi 2 O 3 and TiO 2 shown in Table 1.
- Fe 2 O 3 , MnO (using Mn 3 O 4 ), and ZnO were used as raw materials for the main components, and these were wet-mixed, dried, and calcined at 900 ° C. for 3 hours.
- the calcined powder and SiO 2 , CaCO 3 , Co 3 O 4 , Ta 2 O 5 , Bi 2 O 3 and TiO 2 are added to the ball mill until the average pulverized particle size becomes 1.2 to 1.5 ⁇ m. Crushed and mixed.
- Polyvinyl alcohol is added as a binder to the resulting mixture, granulated with a spray dryer, and then molded into a predetermined shape to obtain a ring-shaped molded body, which is fired to have an outer diameter ⁇ 25 mm ⁇ inner diameter ⁇ 15 mm ⁇ thickness 5 mm.
- Magnetic core ferrite sintered body
- FIG. 1 shows the temperature conditions for the firing step. Firing was carried out in the air in the temperature raising step from room temperature to 800 ° C., and N 2 was substituted at the temperature.
- the oxygen concentration was set to the value shown in the column of O 2 concentration in Table 1, and the holding time was 4 hours.
- the equilibrium oxygen partial pressure was from 1300 ° C. (high temperature holding temperature) to 900 ° C., and the cooling rate was 100 ° C./hr, and after 900 ° C., the cooling rate was 300 ° C./hr.
- the magnetic core obtained was evaluated for magnetic core loss Pcv, saturation magnetic flux density Bs, and average crystal grain size.
- the evaluation method is as follows.
- Core loss Pcv For the core loss Pcv, a BH analyzer (SY-8232) manufactured by Iwasaki Tsushinki Co., Ltd. was used, and the primary side winding and the secondary side winding were wound around the magnetic core for 5 turns, respectively, with a frequency of 100 kHz and a maximum magnetic flux density of 200 mT.
- the core loss at room temperature (23 ° C.) to 150 ° C. was measured. Furthermore, it is kept in a high-temperature bath at 200 ° C. for 96 hours and left in a high-temperature environment. After that, it is taken out from the high-temperature bath and the temperature of the magnetic core is lowered to room temperature.
- the change rate Ps of the core loss was calculated from the core loss at 130 ° C. before and after being left in the high temperature environment by the following equation.
- Ps (%) [(Pcv130B ⁇ Pcv130A) / Pcv130A] ⁇
- Pcv130A is a magnetic core loss at 130 ° C. before being left in a high temperature environment
- Pcv 130B is a magnetic core loss at 130 ° C. after being left in a high temperature environment.
- the magnetic core is placed in a thermostat adjusted to an atmosphere of a maximum of 150 ° C. for about 10 to 15 minutes when the temperature of the magnetic core stabilizes. Substantially no change in magnetic properties including the magnetic core occurred.
- the saturation magnetic flux density (Bs) is obtained by winding a primary side winding and a secondary side winding around a magnetic core 40 times, applying a magnetic field of 1.2 kA / m, and making a DC magnetization measurement test device (Metron Giken Co., Ltd.) SK-110 type) at 130 ° C.
- the average grain size is determined by thermal etching (1100 ° C. ⁇ 1 hr, N 2 medium treatment) of the crystal grain boundary on the mirror polished surface of the ferrite sintered body, and photographing the surface with an optical microscope at a magnification of 400 times. It calculated by the quadrature method in a 140 ⁇ m ⁇ 105 ⁇ m rectangular region on the photograph.
- Table 2 shows the evaluation results of the core loss Pcv, the saturation magnetic flux density Bs, and the average crystal grain size. In the mean crystal grain size, “ ⁇ ” indicates that it has not been evaluated.
- the core losses of the MnZn ferrites of the examples shown in Nos. 9, 10, 12, and 13 are all low, the core loss at 130 ° C. before leaving the high temperature environment is 380 kW / m 3 or less, the core loss after leaving the high temperature environment ( Pcv 130B) was 400 kW / m 3 or less, the core loss between 100 ° C. and 150 ° C. was 430 kW / m 3 or less, and the minimum temperature of the core loss was between 110 ° C. and 150 ° C. Further, as shown in No. 11 and No. 12, by controlling the oxygen concentration so as to suppress the temporal change of the core loss, the increase rate of the core loss (Pcv130A) at 130 ° C.
- FIG. 2 shows the core loss before and after leaving the MnZn-based ferrite shown in No. 8, No. 10, and No. 12 to 14 in a high temperature environment.
- the solid line shows the core loss before leaving the high temperature environment
- the broken line shows the core loss after leaving the high temperature environment. It can be seen that the magnetic core loss is minimal with respect to the amount of Bi 2 O 3 .
- the MnZn-based ferrite was weighed so as to have compositions with different amounts of TiO 2 and SnO 2 shown in Table 3. Since other process conditions are the same as those in the first embodiment, description thereof is omitted.
- the magnetic core obtained was evaluated for magnetic core loss Pcv, saturation magnetic flux density Bs, and average crystal grain size. Since the evaluation method is the same as that of Example 1, the description thereof is omitted. The results are shown in Table 4.
- FIG. 3 shows the core loss before and after leaving the MnZn ferrites No. 5 and No. 15 to 24 in a high temperature environment.
- solid circles indicate the core loss before leaving the high temperature environment of Nos. 5 and 15 to 19 with the TiO 2 amount varied, and the broken line similarly indicates the core loss after leaving the high temperature environment.
- the solid line in the triangle indicates the core loss before leaving the high temperature environment of No. 20 to 24 with the SnO 2 amount changed, and the broken line similarly indicates the core loss after leaving the high temperature environment. It can be seen that the magnetic core loss is minimal with respect to the amounts of TiO 2 and SnO 2 .
- the magnetic core loss Pcv and the saturation magnetic flux density Bs were evaluated for the obtained magnetic core. Since the evaluation method is the same as in Example 1, the description thereof is omitted. The results are shown in Table 6. The magnetic core losses of the MnZn ferrites of the examples were all low, and excellent magnetic properties were obtained.
- the magnetic core loss Pcv and the saturation magnetic flux density Bs were evaluated for the obtained magnetic core. Since the evaluation method is the same as in Example 1, the description thereof is omitted. The results are shown in Table 8.
- the magnetic core losses of the MnZn ferrites of the examples were all low, and excellent magnetic properties were obtained. Further, the temperature at which the magnetic core loss Pcv is minimized varies depending on the composition amount of Fe 2 O 3 , MnO, and ZnO. In the example, the minimum temperature of the magnetic core loss was between 110 ° C. and 150 ° C. The temperature was over 150 ° C. for No55.
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Abstract
Description
Ps(%)=〔(Pcv130B-Pcv130A)/Pcv130A〕×100
所望の温度での磁心損失Pcvを低減するには組成を適正化して、スピネルを構成する正の結晶磁気異方性定数K1を示す金属イオンと負の結晶磁気異方性定数K1を示す金属イオンの量を適宜調整することが必要である。しかしながら飽和磁束密度Bs、キュリー温度Tc、初透磁率μiなどの磁心損失Pcv以外の要求磁気特性による制限から、組成選択の自由度は少ない。またFe2O3が多い組成では、外部磁場印加によって得られる磁化曲線が原点付近でくびれ、いわゆるパーミンバー型となりやすく、磁心損失が増加する。そこで以上の観点から、磁心損失の極小温度が110℃から150℃の間にあるように、本発明では、主成分としてFe2O3が53.25モル%以上54.00モル%以下、ZnOが2.50モル%以上8.50モル%以下、残部がMnOの組成範囲を選択した。なお本発明においては、主成分とは主としてスピネルフェライトを構成する元素、化合物を言い、対して副成分とはその形成に補助的に用いられる元素、化合物を言い、一部がスピネルフェライトに固溶する元素を含む。また、Coのようにスピネルフェライトを構成するものも、前記主成分と比べて含有量が少なく副成分としている。
MnZn系フェライトとして所定の組成量となるように原料を秤量した後、主成分であるFe2O3、MnO(Mn3O4を使用)、ZnOを仮焼成し、解砕した後、副成分であるSiO2、CaCO3、Co3O4、Bi2O3と、Ta2O5又はNb2O5と、TiO2又はSnO2とを適宜添加混合し、バインダを加えて造粒、成形の後、焼成に供する。本発明においては焼成後のMnZn系フェライトをフェライト焼結体と呼ぶ場合がある。
log(PO2)=a-b/(T+273) ・・・式
なお、a、bは定数であり、aは3.1~12.8、bは6000~20000であるのが好ましい。aは高温保持工程の温度と酸素濃度から規定される。また、bが所定の範囲よりも小さいと温度が下がっても酸素濃度が高く酸化が進み、スピネルからヘマタイトが析出する場合がある。また、bが大きいと酸素濃度が低下しウスタイトが析出したりして、結晶粒や粒界層とも十分に酸化されずに抵抗が小さくなる。より好ましくは、aは6.4~11.5、bは10000~18000であり、高温保持工程における酸素濃度を0.7%以下、1200℃における酸素濃度を0.5%以下、1100℃における酸素濃度を0.1%以下に制御することにより、高温環境下での磁気特性の経時変化をより一層低減することが可能となる。
磁心損失Pcvは岩崎通信機株式会社製のB-Hアナライザ(SY-8232)を用い、磁心に一次側巻線と二次側巻線とをそれぞれ5ターン巻回し、周波数100kHz、最大磁束密度200mTで、室温(23℃)~150℃における磁心損失を測定した。
更に高温槽にて200℃の雰囲気で96時間保持して高温環境に放置し、その後、高温槽から取り出して磁心の温度が室温まで下がってから、磁心損失を同様の条件で130℃にて評価し、高温環境放置前後の130℃における磁心損失から次式にて磁心損失の変化率Psを算出した。
Ps(%)=〔(Pcv130B-Pcv130A)/Pcv130A〕×100
なおPcv130Aは高温環境放置前の130℃における磁心損失であり、Pcv130Bは高温環境放置後の130℃における磁心損失である。なお、高温環境放置前の磁心損失の測定においては、磁心の温度が安定する10分から15分程度、磁心を最高で150℃の雰囲気に調整された恒温槽内におくが、以降の実施例の磁心を含めて磁気特性の経時変化は実質的に生じなかった。
飽和磁束密度(Bs)は、磁心に一次側巻線と二次側巻線とをそれぞれ40回巻回し、1.2kA/mの磁場を印加し、直流磁化測定試験装置(メトロン技研株式会社製SK-110型)を用いて130℃において測定した。
平均結晶粒径は、 フェライト焼結体の鏡面研磨面にて結晶粒界をサーマルエッチング(1100℃×1hr、N2中処理)し、その表面を光学顕微鏡で400倍にて写真撮影し、この写真上の140μm×105μm長方形領域において求積法により算出した。
Claims (5)
- 主成分としてFe、Mn及びZnと、副成分としてSi、Ca、Co、及びBiと、Ta又はNbの少なくとも一種と、Ti又はSnの少なくとも一種とを含み、
前記主成分がそれぞれFe2O3、ZnO、MnOで構成されるとしたときの総量を100モル%として、FeをFe2O3換算で53.25モル%以上54.00モル%以下、ZnをZnO換算で2.50モル%以上8.50モル%以下、及びMnをMnO換算で残部とし、
SiをSiO2換算で0.001質量%超0.02質量%未満、CaをCaCO3換算で0.04質量%超0.4質量%未満、CoをCo3O4換算で0.5質量%未満(0は含まず)、BiをBi2O3換算で0.05質量%未満(0は含まず)、TaをTa2O5換算で0.05質量%未満(0を含む)、NbをNb2O5換算で0.05質量%未満(0を含む)、TiをTiO2換算で0.3質量%未満(0を含む)、SnをSnO2換算で0.3質量%未満(0を含む)を満たし、ただし換算されたTa2O5とNb2O5の総量は0.05質量%未満(0は含まず)であり、換算されたTiO2とSnO2の総量は0.3質量%未満(0は含まず)であって、
周波数100kHzで最大磁束密度が200mTにおいて130℃での磁心損失(Pcv130A)が400kW/m3以下であり、200℃にて96時間保持した後の130℃での磁心損失(Pcv130B)を用いて下記式で表される磁心損失の変化率Psが5%以下であることを特徴とするMnZn系フェライト。
Ps(%)=〔(Pcv130B-Pcv130A)/Pcv130A〕×100 - 請求項1に記載のMnZn系フェライトであって、
SiをSiO2換算で0.003質量%以上0.015質量%以下、CaをCaCO3換算で0.06質量%以上0.3質量%以下、CoをCo3O4換算で0.16質量%以上0.4質量%以下、BiをBi2O3換算で0.0075質量%以上0.04質量%以下で、Ta又はNbを単独で含む場合、TaをTa2O5換算で0.015質量%以上0.04質量%以下、NbをNb2O5換算で0.015質量%以上0.04質量%以下、Ti又はSnを単独で含む場合、TiをTiO2換算で0.02質量%以上0.2質量%以下、SnをSnO2換算で0.02質量%以上0.2質量%以下含み、TaとNbとを両方含む場合、換算されたTa2O5とNb2O5の総量は0.04質量%以下であり、TiとSnとを両方含む場合、換算されたTiO2とSnO2の総量は0.2質量%以下であることを特徴とするMnZn系フェライト。 - 請求項1又は2に記載のMnZn系フェライトであって、
100℃から150℃の間での磁心損失が500kW/m3以下で、磁心損失の極小温度が110℃から150℃の間にあることを特徴とするMnZn系フェライト。 - 請求項3に記載のMnZn系フェライトであって、
200℃にて96時間保持した後の130℃での磁心損失(Pcv130B)が400kW/m3以下であることを特徴とするMnZn系フェライト。 - MnZn系フェライトの製造方法であって、
請求項1に規定する主成分及び副成分の酸化物粉末を成形して成形体とし、前記成形体を焼成する焼成工程を有し、前記焼成工程は昇温工程と高温保持工程と降温工程とを備え、高温保持工程における温度は1250℃から1400℃の間であり、高温保持工程における雰囲気中の酸素濃度を体積百分率で0.7%以下とし、前記降温工程において1200℃における酸素濃度を0.5%以下、1100℃における酸素濃度を0.1%以下としたことを特徴とするMnZn系フェライトの製造方法。
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