JP2011035311A - Magnetic material and coil component using the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a magnetic material which provides stable and high permeability in a wide high frequency region, and also to provide a coil component using the same. <P>SOLUTION: A compound expressed by a composition formula Ba<SB>3+y</SB>Co<SB>2</SB>Fe<SB>24-x-y</SB>Sn<SB>x</SB>O<SB>41-δ</SB>is the principal component of a magnetic material. In the above composition formula, x and y denote a mole ratio and satisfy 0<x≤2.0 and 0≤y≤0.6. A wire-wound coil 1 includes a core member 2 formed of the magnetic material having the above characteristic. The core member 2 includes a winding core portion 5 and a flange portion 6 formed on an axis direction end of the winding core portion 5, and also includes a winding 4 arranged on the periphery of the winding core portion 5. <P>COPYRIGHT: (C)2011,JPO&INPIT

Description

  The present invention generally relates to a magnetic material and a coil component using the same, and more specifically, for example, a high-frequency magnetic material suitable for an inductor core member used in a high frequency region and the like. It relates to coil parts.

  In recent years, higher frequencies have been promoted as electronic devices become smaller and lighter. In response to this, it is required to cope with higher frequencies for components of electronic devices. Among such components, an inductor having a core member made of an oxide magnetic material is also required to cope with higher frequencies.

  Materials used for the core member of the inductor include a magnetic material and a dielectric material. A spinel oxide magnetic material is used as the magnetic material, and glass or dielectric ceramics is used as the dielectric.

  Spinel oxide magnetic materials are used in various inductors, power transformers, and the like because of their cubic crystal structure and relatively high magnetic permeability. In particular, a nickel-based oxide magnetic material, for example, nickel (Ni) ferrite is used for a core member of an inductor used in a high frequency region.

  However, the spinel-type oxide magnetic material has a drawback that the magnetic permeability rapidly decreases at a certain frequency or higher. Particularly in nickel ferrite, since the real part (μ ′) of magnetic permeability decreases and the imaginary part (μ ″) of magnetic permeability increases from around the frequency exceeding 100 MHz, nickel ferrite has a high frequency exceeding 100 MHz. There is a problem that it cannot be used for the core member of the inductor used in the region.

  Therefore, glass or dielectric ceramics may be used for the core member of the inductor used in the high frequency region.

  However, since glass or dielectric ceramic is a non-magnetic material, it is necessary to increase the number of windings arranged around the core member in order to obtain the required inductance in the inductor. This makes it difficult to reduce the size of the inductor.

  Therefore, as a material of the core member of the inductor, a material that is a magnetic body and does not decrease in permeability (real part) in a high frequency region is desired. A hexagonal oxide magnetic material such as a Z-type hexagonal ferrite has been studied as a material that meets such requirements.

For example, Japanese Patent Laid-Open No. 2000-235916 (hereinafter referred to as Patent Document 1) discloses a composition formula Ba ₃ Co ₂ (M _x N _x ) Fe _24-2x as a magnetic material capable of obtaining a high magnetic permeability in a high frequency region. O is represented by O ₄₁ , M is Zn, N is at least one selected from Ti, Zr, Hf, Si, Ge, Sn, Ir, and mol% x is 0 <x ≦ 3 Magnetic materials for high frequencies that are within the range have been proposed.

JP 2000-235916 A

  However, in the magnetic material disclosed in Patent Document 1, a high magnetic permeability can be obtained in a frequency region exceeding 100 MHz. However, the frequency at which the magnetic permeability starts to decrease in a high frequency region varies depending on the composition, and the frequency increases. The variation curve in which the permeability decreases also varies. For this reason, a stable high magnetic permeability cannot be obtained in a wide high frequency region. Therefore, this magnetic material is not suitable for the core member of the inductor used in the high frequency region.

  Accordingly, an object of the present invention is to provide a magnetic material capable of obtaining a stable high magnetic permeability in a wide range of high frequencies and a coil component using the magnetic material.

The magnetic material according to the present invention is mainly composed of a compound represented by the composition formula Ba _{3 + y} Co ₂ Fe _24-xy Sn _x O _41-δ , and x and y in the above composition formula represent molar ratios. And 0 <x ≦ 2.0 and 0 ≦ y ≦ 0.6, respectively.

  In the magnetic material of the present invention, the above y preferably satisfies 0.02 ≦ y ≦ 0.6.

  The coil component according to the present invention includes a core member made of a magnetic material having the above-described characteristics.

  In the coil component according to the present invention, the core member includes a winding core portion and a flange portion formed at an end portion in the axial direction of the winding core portion, and further includes a winding disposed around the winding core portion. Is preferred.

  In the magnetic material of the present invention, a high permeability is obtained in a frequency region exceeding 100 MHz, and the frequency at which the permeability starts to decrease in a high frequency region does not vary greatly depending on the composition, and the permeability decreases as the frequency increases. Since the change curve is substantially constant, a stable high magnetic permeability can be obtained in a wide range of high frequencies. In addition, the temperature change rate of the magnetic permeability can be reduced. Therefore, since the magnetic material of the present invention can be applied to coil components such as an inductor core member used in a high frequency region, it can contribute to miniaturization and weight reduction of electronic devices. Further, the magnetic material of the present invention can be applied to a component part incorporated in an electronic device used in an environment having a large temperature change.

It is a perspective view which shows a winding type coil as one Embodiment of the coil components to which the magnetic material of this invention is applied. It is a figure which shows the frequency characteristic of the real part (micro ') and the imaginary part (micro ") of the magnetic permeability measured in the magnetic material produced in the Example of this invention.

The magnetic material of the present invention is mainly composed of a compound represented by the composition formula Ba _{3 + y} Co ₂ Fe _24-xy Sn _x O _41-δ , and x and y in the above composition formula represent molar ratios, respectively. 0 <x ≦ 2.0 and 0 ≦ y ≦ 0.6. Preferably, y satisfies 0.02 ≦ y ≦ 0.6.

In the above composition, in the Ba ₃ Co ₂ Fe ₂₄ O ₄₁ system whose crystal structure is a Z-type ferrite phase, non-stoichiometry in which part of Fe is substituted with Sn, Ba is excessive, and Fe is insufficient. It has a composition.

  When a part of Fe is replaced with Sn in this manner, the saturation magnetization increases and the coercive force decreases, so that high permeability (real part) can be obtained in a high frequency region. On the other hand, when a part of Fe is replaced with another element, a heterogeneous phase is generated, so that the frequency at which the magnetic permeability starts decreasing in the high frequency region varies depending on the composition, and the magnetic permeability decreases as the frequency increases. The change curve that varies. However, when a part of Fe is replaced with Sn, the generation of heterogeneous phases is suppressed, so that the change curve in which the magnetic permeability decreases with increasing frequency is made almost constant, and the magnetic permeability is high in the frequency region exceeding 100 MHz. Can be obtained. Therefore, a stable high magnetic permeability can be obtained in a wide range of high frequencies. When x and y satisfy 0 <x ≦ 2.0 and 0 ≦ y ≦ 0.6, respectively, a magnetic permeability exceeding 15 can be obtained. Furthermore, when y satisfies 0.02 ≦ y ≦ 0.6, a magnetic permeability exceeding 20 can be obtained.

  Further, by substituting part of Fe with Sn, the temperature change rate of magnetic permeability is reduced. When x and y satisfy 0 <x ≦ 2.0 and 0 ≦ y ≦ 0.6, respectively, the range from room temperature (25 ° C.) to −25 ° C., from room temperature (25 ° C.) to 85 ° C. In this range, the temperature change rate of the magnetic permeability can be reduced to less than 5%. Further, when y satisfies 0.02 ≦ y ≦ 0.6, the temperature change of the magnetic permeability in the range from room temperature (25 ° C.) to −25 ° C. and in the range from room temperature (25 ° C.) to 85 ° C. The rate can be reduced to less than 3%.

Furthermore, in the Ba ₃ Co ₂ Fe ₂₄ O ₄₁ system in which the crystal structure is a Z-type ferrite phase, a non-stoichiometric composition in which Ba is excessive and Fe is insufficient is achieved. That is, the content of the Z-type ferrite phase can be increased. Thereby, high magnetic permeability can be obtained. For example, the content of the Z-type ferrite phase can be increased to 80% or more.

  An example of a coil component configured using the magnetic material having the above characteristics will be described.

  As shown in FIG. 1, the wound coil 1 includes a core member 2, an electrode portion 3, and a winding 4. The core member 2 includes a core portion 5 and two flange portions 6 formed at both ends in the axial direction of the core portion 5. The core part 5 has a rectangular cross section as a cross section orthogonal to the axial direction, for example, and is configured from a columnar rectangular parallelepiped elongated in the axial direction. The flange portion 6 has a rectangular cross section that is larger than the rectangular cross section of the core portion 5 as a transverse cross section perpendicular to the axial direction. A recess 7 is formed so as to have An electrode portion 3 is provided on one peripheral wall surface of the flange portion 6. A lead portion 41 that is an end portion of the winding 4 disposed around the core portion 5 is connected to the electrode portion 3 by, for example, soldering.

  In the wound coil 1 configured as described above, the magnetic material of the present invention is applied as the material of the core member 2.

  Hereinafter, examples in which the magnetic material of the present invention was produced will be described.

Samples of magnetic materials of sample numbers 1 to 17 having the compositions shown in Table 1 were prepared. In Table 1, the sample numbers marked with * are the composition formula Ba _{3 + y} Co ₂ Fe _24-xy Sn _x O _41-δ , where x and y are 0 <x ≦ 2.0, 0 ≦ y. ≦ 0.6 indicates that the sample does not satisfy the composition, and the sample numbers marked with ** indicate that x and y are 0 <x ≦ 2.0, 0.02 ≦ y ≦ 0.6 It shows that it is a sample which has a composition which does not satisfy | fill.

[Preparation of Sample Nos. 1-17]
BaCO ₃ (specific surface area is 10-15 m ² / g), SnO ₂ (specific surface area is 3-8 m ² / g), Co ₃ O ₄ (specific surface area is 10-15 m ² / g), Fe ₂ O ₃ (ratio) The raw material powder having a surface area of 5 to 10 m ² / g) was weighed so as to have the composition formula Ba _{3 + y} Co ₂ Fe _24-xy Sn _x O _41-δ at the molar ratio shown in Table 1. The weighed powder was mixed with a ball mill and then calcined in the atmosphere at a temperature of 1200 to 1300 ° C. for 10 hours. These calcined powders were pulverized by a ball mill and then calcined in the atmosphere at a temperature of 1200 to 1300 ° C. for 10 hours. After calcining the calcined powder obtained by the calcining twice with a ball mill, polyvinyl alcohol (PVA) was added as a binder, spray granulated, and press molded. The obtained molded body was fired at a temperature of 1200 to 1350 ° C. to obtain a sintered body.

[Measurement of permeability]
As shown in the annex of JIS standard C-2560-2, each sample is processed into a ring shape having an outer diameter of 10 mm, an inner diameter of 6 mm, and a thickness of 2 mm, and the sintered body of each sample is transparent. The magnetic susceptibility was measured. The magnetic permeability μ ′ (real part) and μ ″ (imaginary part) of each sample was measured using an impedance analyzer (model number HP4291A) manufactured by Agilent Technologies. Magnetic permeability μ ′ at a frequency of 250 MHz. Table 1 shows the measurement results of Q and Q (= μ ′ / μ ″). FIG. 2 shows the frequency characteristics of the magnetic permeability μ ′ and μ ″ for the samples when x is 0, 1.0, and 2.0 (μ ′: thick line, μ ″: thin line).

[Measurement of temperature change rate of permeability]
The rate of change in temperature of the magnetic permeability μ ′ is the rate of change in μ ′ in the temperature range of −25 ° C. to 25 ° C. and 25 ° C. to 85 ° C. using an impedance analyzer (model number HP4291A) manufactured by Agilent Technologies. (25 ° C. standard) was determined from the following equation. Table 1 shows the calculation result of the temperature change rate of the magnetic permeability μ ′.

Δμ ′ / μ ′ (−25 to 25 ° C.) = {Μ ′ (−25 ° C.) − Μ ′ (25 ° C.)} / Μ ′ (25 ° C.) × 100 (%)
Δμ ′ / μ ′ (85-25 ° C.) = {Μ ′ (85 ° C.) − Μ ′ (25 ° C.)} / Μ ′ (25 ° C.) × 100 (%)

[Measurement of Z-type ferrite phase content]
The degree of synthesis of the Z-type ferrite phase, that is, the content of the Z-type ferrite phase, was estimated by determining the relative strength ratio of the Z-type ferrite phase using an X-ray diffraction method. The results are shown in Table 1 for the Z phase content.

From the results shown in Table 1, when Ba _3.2 Co ₂ Fe _23.8-x Sn _x O _41-δ whose crystal structure is a Z-type ferrite phase is replaced with Sn at a part of the Fe site, 250 MHz It can be seen that the magnetic permeability μ ′ at a frequency of is high. However, from the data of Sample No. 8 shown in Table 1, it can be seen that when the Sn substitution amount (x) exceeds 2 mol, the permeability μ ′ is lowered due to the decrease in sinterability. That is, it can be seen that when x and y satisfy 0 <x ≦ 2.0 and 0 ≦ y ≦ 0.6, respectively, a magnetic permeability exceeding 15 can be obtained. Furthermore, it can be seen that when y satisfies 0.02 ≦ y ≦ 0.6, a magnetic permeability exceeding 20 can be obtained.

  It can also be seen that when Sn is substituted for a part of the Fe site, the temperature change rate of the magnetic permeability μ ′ decreases. However, from the data of sample number 8 shown in Table 1, it can be seen that the rate of change in temperature of the magnetic permeability μ ′ increases when the substitution amount of Sn exceeds 2 mol. That is, when x and y satisfy 0 <x ≦ 2.0 and 0 ≦ y ≦ 0.6, respectively, a range from room temperature (25 ° C.) to −25 ° C., a room temperature (25 ° C.) to 85 ° C. It can be seen that the temperature change rate of the magnetic permeability can be reduced to less than 5% in the range up to ° C. Further, when y satisfies 0.02 ≦ y ≦ 0.6, the temperature change of the magnetic permeability in the range from room temperature (25 ° C.) to −25 ° C. and in the range from room temperature (25 ° C.) to 85 ° C. It can be seen that the rate can be reduced to less than 3%.

Further, from the data of sample number 9 and other sample numbers in Table 1, in the Ba ₃ Co ₂ Fe ₂₄ O ₄₁ system whose crystal structure is a Z-type ferrite phase, Ba is excessive and Fe is insufficient. It can be seen that by using the stoichiometric composition, the degree of synthesis of the Z-type ferrite phase, that is, the content of the Z-type ferrite phase is improved, and the magnetic permeability μ ′ is increased. That is, it can be seen that the content of the Z-type ferrite phase can be increased to 80% or more.

  It should be considered that the embodiments and examples disclosed herein are illustrative and non-restrictive in every respect. The scope of the present invention is shown not by the above embodiments and examples but by the scope of claims, and is intended to include all modifications and variations within the meaning and scope equivalent to the scope of claims. .

  Since the magnetic material of the present invention can be applied to coil components such as a core member of an inductor used in a high frequency region, it can contribute to miniaturization and weight reduction of an electronic device. In addition, the magnetic material of the present invention can be applied to a component part incorporated in an electronic device used in an environment with a large temperature change.

1: winding type coil, 2: core member, 3: electrode part, 4: winding, 5: core part, 6: collar part, 7: recessed part, 41: lead-out part, 70: curved surface part.

Claims (4)

The main component is a compound represented by the composition formula Ba _{3 + y} Co ₂ Fe _24-xy Sn _x O _41-δ, where x and y indicate molar ratios, and 0 <x ≦ 2.0 and 0 ≦, respectively. A magnetic material satisfying y ≦ 0.6.   The magnetic material according to claim 1, wherein y satisfies 0.02 ≦ y ≦ 0.6.   A coil component comprising a core member made of the magnetic material according to claim 1.   The core member includes a winding core portion and a flange portion formed at an end portion in the axial direction of the winding core portion, and further includes a winding disposed around the winding core portion. The coil component described.

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