EP1598836A1 - Hochfrequenz-Magnetkern und Verwendung in einem Induktiven Bauelement - Google Patents

Hochfrequenz-Magnetkern und Verwendung in einem Induktiven Bauelement Download PDF

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Publication number
EP1598836A1
EP1598836A1 EP05010020A EP05010020A EP1598836A1 EP 1598836 A1 EP1598836 A1 EP 1598836A1 EP 05010020 A EP05010020 A EP 05010020A EP 05010020 A EP05010020 A EP 05010020A EP 1598836 A1 EP1598836 A1 EP 1598836A1
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Prior art keywords
powder
atomic
soft magnetic
metallic glass
glass powder
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French (fr)
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EP1598836B1 (de
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Teruhiko Fujiwara
Akiri Urata
Akihisa Inoue
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Tohoku University NUC
Tokin Corp
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Tohoku University NUC
NEC Tokin Corp
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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
    • H01F1/12—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
    • H01F1/14—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 metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni
    • 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
    • H01F1/14—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 metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15358—Making agglomerates therefrom, e.g. by pressing
    • H01F1/15366—Making agglomerates therefrom, e.g. by pressing using a binder
    • H01F1/15375—Making agglomerates therefrom, e.g. by pressing using a binder using polymers
    • 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
    • H01F1/14—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 metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15316—Amorphous metallic alloys, e.g. glassy metals based on Co
    • 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
    • H01F1/14—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 metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15325—Amorphous metallic alloys, e.g. glassy metals containing rare earths
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F17/00—Fixed inductances of the signal type 
    • H01F17/04—Fixed inductances of the signal type  with magnetic core
    • H01F17/06—Fixed inductances of the signal type  with magnetic core with core substantially closed in itself, e.g. toroid
    • H01F17/062—Toroidal core with turns of coil around it
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F17/00—Fixed inductances of the signal type 
    • H01F17/04—Fixed inductances of the signal type  with magnetic core
    • H01F2017/048—Fixed inductances of the signal type  with magnetic core with encapsulating core, e.g. made of resin and magnetic powder
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F3/00—Cores, Yokes, or armatures
    • H01F3/10—Composite arrangements of magnetic circuits
    • H01F3/14—Constrictions; Gaps, e.g. air-gaps
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
    • H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
    • H01F41/0206—Manufacturing of magnetic cores by mechanical means
    • H01F41/0246—Manufacturing of magnetic circuits by moulding or by pressing powder

Definitions

  • This invention relates to a high-frequency core mainly using a soft magnetic material and an inductance component using the core.
  • the material of a high-frequency core generally as a material of a high-frequency core, soft ferrite, high-silicon steel, an amorphous metal, a powder core, and the like have mainly been used.
  • the reason why the above-mentioned materials are used is as follows.
  • the soft ferrite the material itself has a high specific resistance.
  • the material may be formed into a thin plate or a powder so as to reduce an eddy current although the material itself has a low specific resistance.
  • the above-mentioned materials are selectively used depending upon a working frequency or an intended use.
  • the material high in specific resistance such as the soft ferrite
  • the material high in saturation magnetic flux density such as the high-silicon steel
  • a magnetic material having both of a high saturation magnetic flux density and a high specific resistance is not yet provided.
  • inductance components such as a coil and a transformer are required to be reduced in size and to have an inductance under a large direct current.
  • it is necessary to simultaneously improve a saturation magnetic flux density and a high-frequency loss characteristic of the core.
  • copper loss resulting from an electric resistance of a winding coil heat generation of the coil or the transformer is increased. Therefore, it is also desired to provide a method for suppressing temperature elevation.
  • the soft ferrite improvement of the saturation magnetic flux density is considered but, actually, no substantial improvement is made.
  • the material itself has a high saturation magnetic flux density.
  • the material in order to adapt to a high-frequency band, the material must be formed into a thinner plate as the frequency band is higher. A multilayer core using such material is lowered in space factor, which may result in decrease in saturation magnetic flux density.
  • alloy compositions used as the soft magnetic material are restricted to Fe-based alloys which are generally classified into a PePCBSiGa alloy composition and a FeSiBM (M being a transition metal) alloy composition.
  • the patent document 1 uses the former, i.e., an alloy having the FePcBSiGa alloy composition and discloses that, by the use of this soft magnetic material, excellent magnetic characteristics capable of achieving a high specific resistance and a high saturation magnetic flux density are obtained. It is noted here that the latter, i.e., the FeSiBM alloy composition is also disclosed (see Japanese Unexamined Patent Application Publications (JP-A) Nos. 2002-194514 and H11-131199, hereinafter referred to as patent documents 2 and 3, respectively). Further, it is also disclosed to use the soft magnetic material for a core (see Japanese Unexamined Patent Application Publication (JP-A) No. H11-74111, hereinafter referred to as a patent document 4).
  • JP-A Japanese Unexamined Patent Application Publication
  • JP-A Japanese Unexamined Patent Application Publications
  • the patent documents 5 and 6 disclose reduction in size of the coil. However, because an existing soft magnetic metal material is used, reduction of loss is not sufficient.
  • a high-frequency core which includes a molded body obtained by molding a mixture of a soft magnetic metallic glass powder and a binder in an amount of 10% or less in mass ratio with respect to the soft magnetic metallic glass powder.
  • the soft magnetic metallic glass powder has an alloy composition represented by (Fe 1-a Co a ) 100-x-y-q-r (M 1-p M' p ) x T y B z C q Al r (0 ⁇ a ⁇ 0.50, 0 ⁇ p ⁇ 0.5, 2 atomic% ⁇ x ⁇ 5 atomic%, 8 atomic% ⁇ y ⁇ 12 atomic%, 12 atomic% ⁇ z ⁇ 17 atomic%, 0.1 atomic% ⁇ q ⁇ 1.0 atomic%, 0.2 atomic% ⁇ r ⁇ 2.0 atomic% and 25 ⁇ (x+y+z+q+r) ⁇ 30, M being at least one selected from Zr, Nb, Ta, Hf, Mo, Ti, V, Cr, and W, M' being at least one selected from Zn, Sn, and R (R being at least one element selected from rare earth metals including Y), T being at least one selected from Si and P).
  • M being at least one selected from Z
  • an inductance component which includes the high-frequency core and at least one turn of winding wound around the core.
  • an inductance component which includes the high-frequency core and at least one turn of winding coil wound around the core.
  • rare earth metals including Y represent the group consisting of lanthanum series elements, such as La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, and another element of Y It has also been found out that, if a powder core is obtained by subjecting the powder to oxidization or insulating coating and then forming the powder into a molded body by an appropriate molding method using a die or the like, the powder core is a high-permeability powder core exhibiting an excellent permeability over a wide band and an excellent performance which has never been achieved, and that, as a result, a high-frequency core made of a soft magnetic material having a high saturation magnetic flux density and a high specific resistance can be produced at a low cost.
  • lanthanum series elements such as La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu
  • an inductance component obtained by providing the high-frequency core with at least one turn of winding is inexpensive and has a high performance as never before.
  • the present inventors also found out that, by limiting a particle size of the soft magnetic metallic glass powder represented by the above-mentioned composition formula, the powder core is excellent in core loss at a high frequency.
  • an inductance component obtained by providing the high-frequency core with at least one turn of winding is inexpensive and has a high performance as never before. It is also found out that, by press forming in the state where a winding coil is embedded in a magnetic body to form an integral structure, an inductance component adapted to a high-frequency large-current application is obtained.
  • the alloy powder before molding may be subjected to oxidizing heat treatment in atmospheric air.
  • molding may be carried out at a temperature not lower than a softening point of the resin as the binder.
  • molding may be carried out in a supercooled liquid temperature range of the alloy powder.
  • the soft magnetic metallic glass powder has an alloy composition represented by a formula (Fe 1-a Co a ) 100-x-y-z-q-r (M 1-p M' p ) x T y B z C q Al r (0 ⁇ a ⁇ 0.50, 0 ⁇ p ⁇ 0.5, 2 atomic% ⁇ x ⁇ 5 atomic%, 8 atomic% ⁇ y ⁇ 12 atomic%, 12 atomic% ⁇ z ⁇ 17 atomic%, 0.1 atomic% ⁇ q ⁇ 1.0 atomic%, 0.2 atomic% ⁇ r ⁇ 2.0 atomic% and 25 ⁇ (x+y+z+q+r) ⁇ 30, M being at least one selected from Zr, Nb, Ta, Hf, Mo, Ti, V, Cr, and W, M' being at least one selected from Zn, Sn, and R (R being at least one element selected from rare earth metals including Y), T being at least one selected from Si and P).
  • M being at
  • Fe as a main component is an element contributing to magnetism and is essential in order to achieve a high saturation magnetic flux density.
  • a part of Fe may be replaced by Co in a ratio of 0 to 0.5.
  • Such substitute component has an effect of improving a glass forming performance and is further expected to have an effect of improving the saturation magnetic flux density.
  • the total amount of Fe and the substitute element is within a range not smaller than 70 atomic % and not greater than 75 atomic % with respect to a whole of the alloy powder.
  • the element M is a transition metal element necessary to improve the glass forming performance and is at least one selected from Zr, Nb, Ta, Hf, Mo, Ti, V, Cr, and W.
  • the content of the element M is not smaller than 2 atomic % and not greater than 5 atomic %.
  • the glass forming performance is decreased and the permeability and the core loss are remarkably deteriorated and, if the content exceeds 5 atomic %, the saturation magnetic flux density is decreased and the usefulness is lost.
  • the ratio of 0 to 0.5 of the element M by Zn, Sn, R (R being at least one element selected from rare earth metals including Y)
  • the ratio of Fe and Co can be increased without deteriorating the glass forming performance, so that the saturation magnetic flux density can be improved.
  • Si and B are elements which are essential in order to produce the soft magnetic metallic glass powder.
  • the amount of Si is within a range not smaller than 8 atomic % and not greater than 12 atomic %.
  • the amount of B is within a range not smaller than 12 atomic % and not greater than 17 atomic %. This is because, if the amount of Si is smaller than 8 atomic % or greater than 12 atomic % or if the amount of B is smaller than 12 atomic % or greater than 17 atomic %, the glass forming performance is degraded and a stable soft magnetic glass powder can not be produced.
  • Si may be replaced by P.
  • Al and C have an effect of forming the powder into a spherical shape upon preparing the powder by various atomizing techniques as far as these elements are used within the range of the alloy composition of this invention together with other constituent elements.
  • the amounts to be added if the amount of Al is smaller than 0.2 atomic%, the effect of forming the powder of a spherical shape is small. If the amount of Al is greater than 2.0 atomic%, amorphous forming performance is deteriorated. Similarly, if the amount of C is smaller than 0.1 atomic%, the effect of forming the powder of a spherical shape is small. If the amount of C is greater than 1.0 atomic%, amorphous forming performance is deteriorated. Al and C may be used alone or in combination.
  • the soft magnetic metallic glass powder is produced by water atomization or gas atomization.
  • at least 50% of particle sizes are not smaller than 10 ⁇ m.
  • the water atomization is established as a method of producing the alloy powder at a low cost and in a large amount.
  • To be able to produce the powder by this method is a very large advantage in industrial application.
  • the alloy powder of 10 ⁇ m or more is crystallized so that the magnetic characteristics are significantly deteriorated. As a result, the product yield is seriously deteriorated so that the industrial application is prevented.
  • the soft magnetic metallic glass powder according to this invention is easily vitrified (amorphized) if the particle size is 150 ⁇ m or less.
  • the soft magnetic metallic glass powder of this invention is highly advantageous in view of the cost.
  • an appropriate oxide coating film is already formed on a powder surface. Therefore, by mixing a resin with the alloy powder and molding the mixture to form a molded body, a core having a high specific resistance is easily obtained.
  • an eddy current loss can be reduced by the use of a metal powder having a very small particle size.
  • an alloy composition known in the art oxidation of the powder during production is remarkable if the average diameter is 30 ⁇ m or less. Therefore, predetermined characteristics are difficult to obtain in the powder produced by a typical water atomization apparatus.
  • the metallic glass powder is excellent in corrosion resistance of the alloy and is therefore advantageous in that the powder reduced in amount of oxygen and having excellent characteristics can relatively easily be produced even if the powder is very small.
  • a binder such as a silicone resin in an amount of 10 % in mass ratio is mixed with the soft magnetic metallic glass powder.
  • the molded body is obtained.
  • the molded body serves as a high-frequency core having a powder filling rate of 50 % or more, a magnetic flux density of 0.5 T or more upon application of a magnetic field of 1.6 x 10 4 A/m, and a specific , resistance of 1 x 10 4 cm.
  • the amount of the binder is 10 % or less in mass ratio. This is because, if the amount exceeds 10 %, the saturation magnetic flux density becomes equivalent to or lower than that of ferrite and the usefulness of the core is lost.
  • the molded body may be obtained by preparing a mixture of the soft magnetic metallic glass powder and the binder in an amount of 5 % or less in mass ratio with respect to the soft magnetic metallic glass powder and compression-molding the mixture using a die.
  • the molded body has a powder filling rate of 70 % or more, a magnetic flux density of 0.75 T or more when a magnetic field of 1.6 x 10 4 A/m is applied, and a specific resistance of 1 ⁇ cm or more.
  • the magnetic flux density is 0.75 T or more and the specific resistance is 1 ⁇ m or more, the characteristics are more excellent as compared with a Sendust core and the usefulness is further improved.
  • the molded body may be obtained by preparing a mixture of the soft magnetic metallic glass powder and the binder in an amount of 3 % or less in mass ratio with respect to the soft magnetic metallic glass powder and compression-molding the mixture using a die under a temperature condition not higher than a softening point of the binder.
  • the molded body has a powder filling rate of 80 % or more, a magnetic flux density of 0.9 T or more when a magnetic field of 1.6 x 10 4 A/m is applied, and a specific resistance of 0.1 ⁇ cm or more.
  • the magnetic flux density is 0.9 T or more and the specific resistance is 0.1 ⁇ m or more, the characteristics are more excellent as compared with any powder core commercially available at present and the usefulness is further improved.
  • the molded body may be obtained by preparing a mixture of the soft magnetic metallic glass powder and the binder in an amount of 1 % or less in mass ratio with respect to the soft magnetic metallic glass powder and compression-molding the mixture in a supercooled liquid temperature range of the soft magnetic metallic glass powder.
  • the molded body has a powder filling rate of 90 % or more, a magnetic flux density of 1.0 T or more when a magnetic field of 1.6 x 10 4 A/m is applied, and a specific resistance of 0.01 ⁇ cm or more.
  • the magnetic flux density is 1.0 T or more and the specific resistance is 0.01 ⁇ m or more
  • the magnetic flux density is substantially equivalent to that of a multilayer core including an amorphous metal and a high-silicon steel plate in a practical region.
  • the molded body herein obtained is small in hysteresis loss and high in specific resistance so that the core loss characteristic is much superior.
  • the usefulness as a core is further improved.
  • the molded body as the high-frequency core may be subjected to heat treatment under a temperature condition not higher than the Curie point as a strain-relieving heat treatment.
  • the core loss is further reduced and the usefulness as a core is further improved.
  • SiO 2 is contained at least in a part of an intermediate material between particles of the alloy powder in order to maintain insulation between the particles (alternatively, all of the intermediate material may be SiO 2 ).
  • an inductance component is produced by providing the above-mentioned high-frequency core with at least one turn of winding after a gap is formed at a part of a magnetic path if necessary, a product exhibiting high permeability in a high magnetic field and having excellent characteristics is produced.
  • a powder core is produced by molding a mixture of a soft magnetic metallic glass powder having the above-mentioned metallic glass composition and having the maximum particle size of 45 ⁇ m or less in mesh size and the average diameter of 30 ⁇ m or less and a binder in an amount of 10 % or less in mass ratio with respect to the soft magnetic metallic glass powder, the powder core exhibits an extremely low loss characteristic at a high frequency and has an excellent performance never before achieved.
  • the inductance component excellent in Q characteristic is obtained.
  • the reason why the powder particle size is defined will be described in detail. If the maximum particle size exceeds 45 ⁇ m in mesh size, the Q characteristic in a high-frequency region is deteriorated. Further, unless the average diameter is 30 ⁇ m or less, the Q characteristic at 500 kHz or more does not exceed 40. Further, unless the average diameter is 20 ⁇ m or less, the Q value at 1 MHz or more is not 50 or more.
  • the metallic glass powder is advantageous in that, since the specific resistance of the alloy itself is twice to ten times higher than conventional materials, the Q characteristic is high even at the same particle size . If the same Q characteristic is sufficient, a usable particle size range is widened so as to reduce a powder production cost.
  • Fig. 5 is an external perspective view of a basic structure of a high-frequency inductance component according to yet another embodiment of this invention.
  • the inductance component 103 as an integral structure is obtained by press-molding in the state where a winding coil 7 obtained by winding a long plate material 5 formed by the above-mentioned soft magnetic powder is embedded in a magnetic body 8.
  • An entire surface of a winding portion of the plate material 5 is provided with an insulating coating 6.
  • a powder preparing step pure metal element materials including Fe, Si, B, Nb, Al, C, and substitute elements therefor or, if desired, various mother alloys were weighed so as to obtain predetermined compositions.
  • various kinds of soft magnetic alloy powders were produced by water atomization generally used.
  • a misch metal is a mixture of rare earth metals.
  • a mixture of 30 % La, 50 % Ce, 15 % Nd, and the balance other rare earth element or elements was used.
  • the permeability was obtained from the inductance value at 100 kHz by the use of an LCR meter. Further, by the use of a d.c. magnetic characteristics measuring instrument, measurement was made of the saturation magnetic flux density when a magnetic field of 1.6 x 10 4 A/m was applied. In addition, upper and lower surfaces of each core were polished and measurement by X-ray diffraction (XRD) was carried out to observe a phase. The results shown in Table 1 were obtained.
  • Table 1 shows composition ratios of the samples. Further, an XRD pattern obtained by XRD measurement is judged as a glass phase if only a broad peak specific to the glass phase was detected, as a (glass + crystal) phase if a sharp peak attributable to a crystal was observed together with a broad peak, and as a crystal phase if only a sharp peak was observed without a broad peak.
  • ⁇ Tx Tx - Tg, where Tx represents crystallization temperature, and Tg represents glass transition temperature.
  • the specific resistance was measured for the molded bodies (cores) by two-terminal d.c. measurement. As a result, it was confirmed that all samples exhibited excellent specific resistances not lower than 1 ⁇ cm.
  • the temperature elevation rate of DSC was 40 K/min. From the examples 1 to 3 and the comparative examples 1 and 2, it is understood that the core having a glass phase is obtained if the amount of Nb is 3 to 6 %.
  • the magnetic flux density is as low as 0.70 T or less in the comparative example 2 where the amount of Nb is 6 %.
  • the core having a glass phase is obtained if the amount of Si is 8 to 12, the amount of B is 12 to 17, and the amount of Fe is 70 to 75.
  • An alloy powder having a composition of (Fe 0.8 Co 0.2 ) 73 Si 9 B 14.5 Nb 2 Al 1.0 C 0.5 was prepared by water atomization. The powder thus obtained was classified into those having a size of 75 ⁇ m or less. XRD measurement was carried out to confirm a broad peak specific to a glass phase.
  • the specific resistance has a value as high as ⁇ 10 4 comparable to that of a ferrite core when the amount of the binder exceeds 5%. Because no special effect is obtained even If the molding temperature is elevated, molding at the room temperature is sufficient. Next, when the amount of the binder is equal to 5%, the specific resistance as high as 100 ⁇ cm or more is obtained and molding at the room temperature is sufficient. Next, it is understood that, when the content of the binder is equal to 2.5%, the powder filling rate is dramatically improved, the magnetic flux density is high, and the specific resistance of 10 ⁇ cm or more is obtained if molding is carried out at 150 °C.
  • an alloy powder having a composition of Fe 72 Si 9 B 14.5 Nb 3 Al 1.0 C 0.5 was prepared by water atomization. Thereafter, the powder thus obtained was classified into those having a particle size of 75 ⁇ m or less. Then, XRD measurement was carried out to confirm a broad peak specific to a glass phase.
  • thermal analysis by DSC was carried out to measure a glass transition temperature and a crystallization temperature to confirm that a vitrification start temperature range or a supercooled liquid temperature range ⁇ Tx was 35K. Then, the powder was kept at a temperature condition of 450 °C lower than the glass transition temperature and heat treated for 0.5 hour in atmospheric air to form oxide on the surface of the powder.
  • the powder with oxide formed thereon was mixed with, in mass ratio, 10%, 5%, 2.5%, 1%, and 0.5% silicone resin as a binder.
  • these powders were molded by applying a pressure of 1.18 GPa (about 12t/cm 2 ) as a molding pressure under three different temperature conditions, i.e., at a room temperature, at 150 °C higher than a softening temperature of the resin, and at 550 °C in a supercooled liquid temperature range of the soft magnetic metallic glass powder, so that the height was equal to 5 mm.
  • a pressure of 1.18 GPa about 12t/cm 2
  • the specific resistance has a value as high as ⁇ 10 4 comparable to that of a ferrite core when the amount of the binder (the amount of the resin) exceeds 5%. It is understood that no special effect is obtained even if the molding temperature is elevated and that the molding condition around the room temperature is sufficient. Further, it is understood that, when the amount of the resin is equal to 5%, the specific resistance as high as 100 ⁇ cm or more is obtained and that molding at the room temperature is similarly sufficient
  • the amount of the resin when the amount of the resin is equal to 2.5%, the powder filling rate is dramatically improved, the magnetic flux density is high, and the specific resistance of 10 ⁇ cm or more is obtained if molding is carried out at 150 °C.
  • the amount of the resin when the amount of the resin is 1% and 0.5%, the powder filling rate is dramatically improved, the saturation magnetic flux density is high, and the specific resistance of 0.1 ⁇ cm or more is obtained if molding is carried out at 550 °C.
  • the inductance characteristic was measured in comparison with various core materials. Further, a core prepared by the use of the same alloy powder and the same production process was heat treated at 500 °C for 0.5 hour in a nitrogen atmosphere to obtain another sample. The inductance characteristic of this sample is also shown. For standardization of the inductance value, the permeability was obtained for comparison.
  • the core materials compared were Sendust, 6.5% silicon steel, and an iron-based amorphous metal.
  • the inductance component of this invention has a magnetic flux density equivalent to that of the inductance component using the amorphous metal and exhibits a core loss characteristic lower than that of the inductance component using Sendust. Therefore, the inductance component of this invention can be used as a very excellent inductance component. It has been confirmed that, in the inductance component using the heat-treated core, the permeability and the core loss are further improved.
  • an inductance component was produced by the use of a material corresponding to the sample No. 12 in the example 28. Further, another inductance component was prepared using a high-frequency core produced by the same alloy powder and the same production process and heat treated at 500 °C for 0.5 hour in a nitrogen atmosphere. Further, for comparison, inductance components (including the structure having a gap at a part of a magnetic path as shown in Fig. 4) were produced by the use of Sendust, 6.5 % silicon steel, and a Fe-based amorphous metal as core materials, respectively. For those inductance components, the magnetic flux density (at 1.6 x 10 4 A/m) by d.c. magnetic characteristics measurement, the d.c.
  • the inductance component of this invention has a magnetic flux density substantially equivalent to that of the inductance component using the Fe-based amorphous metal as a core and yet exhibits a core loss lower than that of the inductance component using Sendust as a core. Therefore, the inductance component of this invention has a very excellent characteristic. It has been confirmed that, in the inductance component using the heat-treated core, the permeability and the core loss are further improved and more excellent characteristics are achieved.
  • an alloy powder having a composition of Fe 72 Si 9 B 14.5 Nb 3 Al 1.0 C 0.5 was prepared by water atomization. Thereafter, the powder thus obtained was classified into those having a particle size of 45 ⁇ m or less. Then, XRD measurement was carried out to confirm a broad peak specific to a glass phase.
  • a silicone resin as a binder was mixed in an amount of 1.5% in mass ratio.
  • heat treatment was carried out in Ar at 500 °C.
  • the inductance component of this invention is improved in powder filling rate by adding to the metallic glass powder the soft magnetic powder smaller in particle size, and is consequently improved in permeability.
  • the added amount exceeds 50%, the improving effect is weakened and the core loss characteristic is significantly degraded. Therefore, it is understood that the added amount is preferably 50% or less.
  • alloy powders having a composition of Fe 73.5-q-r Si 9 B 14.5 Nb 3 C q Al r in which the ratio of q and r were variously changed were prepared by water atomization.
  • powders having aspect ratios shown in Table 7 were prepared. Thereafter, the powders thus obtained were classified into those having a particle size of 45 ⁇ m or less.
  • XRD measurement was carried out to confirm a broad peak specific to a glass phase. Further, thermal analysis by DSC was carried out to measure a glass transition temperature and a crystallization temperature to confirm that a supercooled liquid temperature range ⁇ Tx was 35K.
  • a silicone resin as a binder was mixed in an amount of 3.0% in mass ratio.
  • these powders were molded at a room temperature by applying a pressure of 1.47 GPa (15t/cm 2 ) so that the height was equal to 5 mm.
  • heat treatment was carried out in Ar at 500 °C.
  • the inductance component of this invention is improved in permeability by increasing the aspect ratio of the metallic glass powder.
  • the aspect ratio of the powder is preferably 2 or less.
  • the inductance and the resistance were measured at various frequencies by the use of an LCR meter. From the measurements, the inductance value at 1 MHz, the peak frequency of Q, and the peak value of Q were obtained. The results shown in Table 8 were obtained.
  • the peak frequency of Q was 500 kHz or more and its value was 40 or more. At that time, the power conversion efficiency was as excellent as 80% or more.
  • the peak frequency of Q was 1 MHz or more and its value was 50 or more. At that time, the power conversion efficiency was as more excellent as 85% or more. Further, it is understood that, by heat treating the inductance component, the conversion efficiency is further improved.
  • an alloy composition of (Fe 1-a Co a ) 100-x-y-z-q-r (M 1-p M' p ) x T y B z C q Al r (0 ⁇ a ⁇ 0.50, 0 ⁇ p ⁇ 0.5, 2 atomic% ⁇ x ⁇ 5 atomic%, 8 atomic% ⁇ y ⁇ 12 atomic%, 12 atomic% ⁇ z ⁇ 17 atomic%, 0.1 atomic% ⁇ q ⁇ 1.0 atomic%, 0.2 atomic% ⁇ r ⁇ 2.0 atomic% and 25 ⁇ (x+y+z+q+r) ⁇ 30, M being at least one selected from Zr, Nb, Ta, Hf, Mo, Ti, V, Cr, and W, M' being at least one selected from Zn, Sn, and R (R being at least one element selected from rare earth metals including Y), T being at least one selected from Si and P) is selected
  • the metallic glass powder having a maximum particle size of 45 ⁇ m or less in mesh size and an average diameter of 30 ⁇ m or less, more desirably 20 ⁇ m or less is used, a powder core having an extremely low loss characteristic at a high frequency is obtained.
  • An inductance component comprising the high-frequency core with at least one turn of winding wound therearound is extremely excellent in Q characteristic so that the power supply efficiency can be improved.
  • this invention is very useful in industrial application.
  • the metallic glass powder having a maximum particle size of 45 ⁇ m or less in mesh size and an average diameter of 30 ⁇ m or less, more desirably 20 ⁇ m or less is press-molded with a winding coil embedded in a magnetic body to form an integral structure.
  • a winding coil embedded in a magnetic body in addition to the excellent core characteristics specific to the metallic glass, heat generation resulting from an electric current flowing through the winding coil is radiated through the metal magnetic body.
  • the synergetic effect thereof it is possible to obtain an inductance component increased in rated current for the same shape.
  • the temperature of the strain-relieving heat treatment of the metallic glass powder is lower than a temperature above 600 °C which is believed as an upper limit of the allowable temperature for a copper wire and a coating material used in the winding coil. Therefore, by the heat treatment at a temperature not higher than 600 °C, it is possible to obtain a coil remarkably reduced in loss. Therefore, as the powder forming the core having an integral structure of the winding coil and the powder, the alloy composition of this invention is very suitable.
  • the high-frequency core according to this invention is economically obtained by the use of the soft magnetic metallic glass material having a high saturation magnetic flux density and a high specific resistance. Further, the inductance component obtained by providing the core with the winding is excellent in magnetic characteristics in a high-frequency band as never before. Thus, a high-permeability powder core low in cost and high in performance as never before can be produced and is suitably used in a power supply component, such as a choke coil and a transformer, of various electronic apparatuses.
  • the high-frequency core obtained by molding the powder having a fine particle size in this invention By the use of the high-frequency core obtained by molding the powder having a fine particle size in this invention, a higher-performance inductance component at a high frequency can be produced. Further, in the high-frequency core obtained by molding the powder having a fine particle size, press-molding may be carried out with the winding coil embedded in the magnetic body to form an integral structure.
  • the inductance component small in size and adapted to a large current can be produced and is suitably used as an inductance component such as a choke coil and a transformer.

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  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Chemical & Material Sciences (AREA)
  • Dispersion Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Power Engineering (AREA)
  • Soft Magnetic Materials (AREA)
EP05010020A 2004-05-17 2005-05-09 Hochfrequenz-Magnetkern und Verwendung in einem Induktiven Bauelement Expired - Fee Related EP1598836B1 (de)

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DE102006032517A1 (de) * 2006-07-12 2008-01-24 Vaccumschmelze Gmbh & Co. Kg Verfahren zur Herstellung von Pulververbundkernen und Pulververbundkern
EP2555210A4 (de) * 2010-03-26 2017-09-06 Hitachi Powdered Metals Co., Ltd. Massekern und herstellungsverfahren dafür

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US7170378B2 (en) * 2003-08-22 2007-01-30 Nec Tokin Corporation Magnetic core for high frequency and inductive component using same
JP4849545B2 (ja) * 2006-02-02 2012-01-11 Ｎｅｃトーキン株式会社 非晶質軟磁性合金、非晶質軟磁性合金部材、非晶質軟磁性合金薄帯、非晶質軟磁性合金粉末、及びそれを用いた磁芯ならびにインダクタンス部品
CN100457955C (zh) * 2007-04-16 2009-02-04 安泰科技股份有限公司 铁基大块非晶合金材料
CN101896982B (zh) * 2007-12-12 2012-08-29 松下电器产业株式会社 电感部件及其制造方法
US11355276B2 (en) * 2009-02-27 2022-06-07 Cyntec Co., Ltd. Choke
TWI407462B (zh) 2009-05-15 2013-09-01 Cyntec Co Ltd 電感器及其製作方法
CN102509603B (zh) * 2011-12-31 2015-10-07 青岛云路新能源科技有限公司 铁基非晶态软磁材料及其制备方法
JP5919144B2 (ja) * 2012-08-31 2016-05-18 株式会社神戸製鋼所 圧粉磁心用鉄粉および圧粉磁心の製造方法
CN104036905A (zh) * 2014-05-28 2014-09-10 浙江大学 一种软磁复合材料及其制备方法
CN104021910A (zh) * 2014-06-26 2014-09-03 天津理工大学 一种用于高频条件且具有高初始磁导率的软磁合金
JP6651082B2 (ja) * 2015-07-31 2020-02-19 Ｊｆｅスチール株式会社 軟磁性圧粉磁芯の製造方法
KR101808176B1 (ko) * 2016-04-07 2018-01-18 (주)창성 연자성몰딩액을 이용한 코일매립형인덕터의 제조방법 및 이를 이용하여 제조된 코일매립형인덕터
KR20180082211A (ko) * 2017-01-10 2018-07-18 엘지이노텍 주식회사 자성 코어 및 이를 포함하는 코일 부품
CN113436875B (zh) * 2021-06-25 2022-04-19 广东精密龙电子科技有限公司 低成型压力电感材料、制备方法及一体成型电感

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DE102006032517A1 (de) * 2006-07-12 2008-01-24 Vaccumschmelze Gmbh & Co. Kg Verfahren zur Herstellung von Pulververbundkernen und Pulververbundkern
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DE102006032517B4 (de) * 2006-07-12 2015-12-24 Vaccumschmelze Gmbh & Co. Kg Verfahren zur Herstellung von Pulververbundkernen und Pulververbundkern
EP2555210A4 (de) * 2010-03-26 2017-09-06 Hitachi Powdered Metals Co., Ltd. Massekern und herstellungsverfahren dafür

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DE602005012020D1 (de) 2009-02-12
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EP1598836B1 (de) 2008-12-31
CN1700369A (zh) 2005-11-23

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