JP6455241B2 - Coiled dust core - Google Patents

Description

The present invention relates to a soft magnetic metal dust core.

In recent years, electric and electronic devices have been miniaturized, and a compact and low-profile dust core that can handle a large current is required. As a material for the dust core, a ferrite core, a laminated electrical steel sheet, a soft magnetic metal core, or the like is used. Although laminated magnetic steel sheets have a high saturation magnetic flux density, when the drive frequency of the power supply circuit exceeds several tens of kHz, the iron loss increases and the efficiency decreases. The ferrite core has low high-frequency loss, but has a low saturation magnetic flux density and inferior direct current superposition characteristics. On the other hand, the soft magnetic metal core has a higher saturation magnetic flux density than the ferrite core, and the DC superposition characteristic is maintained up to a high magnetic field. Therefore, when producing a dust core corresponding to a large current, it has become the mainstream to use a soft magnetic metal core as the material of the dust core. In order to further reduce the size and height, a coil in which a coil and soft magnetic metal particles are integrally pressure-molded has been proposed. In the present specification, the inductor having such a structure is referred to as a “coil-embedded dust core”.

Although the loss at a high frequency of the soft magnetic metal core is smaller than that of the laminated electromagnetic steel sheet, it cannot be said that the loss is as low as that of the ferrite core, and reduction of the loss of the coil-embedded dust core is desired.

In order to reduce the loss of the soft magnetic metal core, it is known to reduce the coercive force of the soft magnetic metal powder constituting the core. The core loss is divided into a hysteresis loss and an eddy current loss. Since the hysteresis loss depends on the coercive force, the core loss can be reduced by reducing the coercive force.

In order to reduce the coercivity of the soft magnetic metal core, it has been attempted to heat-treat the soft magnetic metal powder at a high temperature at which the crystal grain size becomes large. For example, Patent Document 1 discloses a technique in which inorganic powder for preventing sintering is mixed with iron powder and heat-treated at a high temperature. Patent Document 2 discloses a technique in which a soft magnetic alloy powder is heat-treated at a high temperature while mixing an inorganic insulator and suppressing the adhesion of the powder.

JP-A-9-260126 JP 2002-57020 A

In the techniques of Patent Document 1 and Patent Document 2, a large amount of inorganic powder is mixed with the soft magnetic metal powder to prevent sintering, and heat treatment is performed at a high temperature. Since it is impossible to cover, it is inevitable that the powder is fixed by heat treatment at 1000 ° C. or higher. In order to unfasten the fixed powder, a pulverization process is required. However, since the powder is distorted by this, the coercive force of the resulting powder is not sufficiently reduced. The upper limit temperature of the treatment temperature not fixed by the heat treatment is 950 ° C., but the crystal growth is insufficient at this temperature. That is, in the conventional technique, the effect on the increase in the crystal grain size is insufficient, and therefore the coercive force of the obtained soft magnetic metal powder is not sufficiently reduced. There was a problem that the loss also increased.

The present invention has been devised to solve the above-described problems, and an object thereof is to provide a coil-embedded dust core with low loss.

In order to solve the above problems, a coil-embedded dust core according to claim 1 is embedded in a green compact in which a soft magnetic metal powder mainly composed of Fe and Ni and a binder are mixed, and embedded in the green compact. And a lead wire and a terminal provided outside the green compact.
In the present invention, the Ni content of the soft magnetic metal powder is 30 to 80% by mass, the total content of Fe and Ni is 90% by mass or more, and the B content in the metal particles of the soft magnetic metal powder is 10 to 10% by mass. It is preferable that it is 150 ppm.
In the present invention, an internal structure in which boron nitride is mixed in the binder in the green compact is preferable.

The coil-embedded dust core having the above configuration has a very small loss.

The coil-embedded dust core according to claim 2 is the coil-embedded dust core according to claim 1, wherein the circularity of the cross section of 90% or more of the particles constituting the soft magnetic metal powder. Is 0.80 or more.

The coil-embedded dust core using the soft magnetic metal powder having the above configuration can further reduce loss.

A coil-embedded dust core according to claim 3 is the coil-embedded dust core according to claim 1, wherein 90% or more of the particles constituting the soft magnetic metal powder are one piece. It consists of crystal grains.

The coil-embedded dust core using the soft magnetic metal powder having the above configuration can further reduce loss.

The coil-embedded dust core according to claim 4 is the coil-embedded dust core according to any one of claims 1 to 3, wherein the amount of oxygen contained in the particles of the soft magnetic metal powder is 500 ppm or less. It is characterized by being.

The coil-embedded dust core using the soft magnetic metal powder having the above configuration can further reduce loss.

The coil-embedded dust core according to claim 5 is the coil-embedded dust core according to any one of claims 1 to 4, wherein the content of nitrogen contained in the particles of the soft magnetic metal powder is It is characterized by being 2000 ppm or less.

The coil-embedded dust core using the soft magnetic metal powder having the above configuration has an extremely small loss and can adjust the magnetic permeability.

The coil-embedded dust core according to claim 6 is the coil-embedded dust core according to any one of claims 1 to 5, wherein boron nitride in the powder compact is 45 to 33000 mass%. It is characterized by.

The coil-embedded dust core using the soft magnetic metal powder having the above configuration has an extremely small loss and can adjust the magnetic permeability.

According to the present invention, a coil-embedded dust core having extremely small loss can be obtained. Furthermore, the loss can be further reduced by controlling the soft magnetic metal powder constituting the coil-embedded dust core.

Hereinafter, preferred embodiments of a coil component according to the present invention will be described with reference to the drawings.

The coil component according to the present embodiment is applied to, for example, a CPU peripheral circuit of an electronic device such as a notebook personal computer, and is applied with an alternating current having a predetermined frequency (for example, several hundred Hz). FIG. 1 is a perspective view of a coil-embedded dust core C according to this embodiment. As shown in FIG. 1, the coil-embedded dust core C includes a soft magnetic metal dust core 10, a coil conductor 20, and terminal fittings 30 and 32.

The soft magnetic metal dust core 10 includes a mounting surface 101 placed on the mounting substrate, a facing surface 102 facing the mounting surface 101, side surfaces 104 and 105 orthogonal to the mounting surface 101, and side surfaces 104 and 105. And opposing side surfaces 108 and 109. The side surface 104 and the side surface 105 are chamfered, whereby a side surface 106 is formed between the side surface 104 and the side surface 105. The side surface 108 and the side surface 109 are chamfered, whereby a side surface 110 is formed between the side surface 108 and the side surface 109.
Concave portions 103 and 107 are formed on the facing surface 102 of the soft magnetic metal dust core 10. The recessed portion 103 is formed from a ridge formed by the side surface 104 and the facing surface 102 toward the center of the facing surface 102. Has been. The recess 107 is formed from a ridge formed by the side surface 108 and the facing surface 102 toward the center of the facing surface 102.

Terminal fittings 30 and 32 are attached to the soft magnetic metal dust core 10. The terminal fitting 30 has a base portion 301, a joint portion 302, one clamping portion 303, and the other clamping portion 304. The base 301 is disposed along the side surface 104 of the soft magnetic metal dust core 10. A joint portion 302 extends from the base portion 301 and is disposed along the side surface 106 of the soft magnetic metal dust core 10. A fusion part 302a is formed in the joint part 302, and one lead part 202 of the conductor 20 described later and the terminal fitting 30 are welded and joined in the fusion part 302a. The sandwiching portion 303 extends from the base portion 301 and is disposed along the concave portion 103 formed on the facing surface 102 of the soft magnetic metal dust core 10. The sandwiching portion 304 extends from the base portion 301 and is disposed along the mounting surface 101.

Similar to the terminal fitting 30, the terminal fitting 32 has a base (not shown), a joint (not shown), one clamping part 323, and the other clamping part (not shown). Yes. The base of the terminal fitting 32 is disposed along the side surface 108 of the soft magnetic powder core 10. The joint portion of the terminal fitting 32 extends from the base portion of the terminal fitting 32 and is disposed along the side surface 110 of the soft magnetic powder core 10. A fusion part (not shown) is formed in the joint part, and the other lead part 203 of the conductor 20 described later and the terminal fitting 32 are welded and joined in this fusion part. One clamping part 323 of the terminal fitting 32 extends from the base of the terminal fitting 32 and is disposed along a recess 107 formed on the facing surface 102 of the soft magnetic metal dust core 10. The other sandwiching portion of the terminal fitting 32 extends from the base portion 301 and is disposed along the mounting surface 101.

A conductor 20 is embedded in the soft magnetic metal dust core 10. The conductor 20 is a round wire made of a copper wire covered with a resin film, and has a circular cross section. Examples of the resin used for the film include an epoxy-modified acrylic resin.

FIG. 2A is a plan view of the coil portion 25, and FIG. 2B is a cross-sectional view of the coil portion 25. As shown in FIGS. 1 and 2, the coil portion 25 is an air-core coil portion, and is formed by winding the conductor 20 in a plurality of layers in the radial direction and the axial direction. The coil portion 25 is disposed at substantially the center of the soft magnetic metal dust core 10 and the axial direction (the X direction shown in FIG. 2B) is parallel to the side surfaces 104 to 106 and 108 to 110. Has been placed.

FIG. 3 is a view for explaining a winding state of the coil portion 25. As shown in FIG. 3, the coil portion 25 is formed by winding the conductor 20 alpha. Therefore, the coil part 25 has two winding ends. The pair of winding ends of the coil portion 25 is located at the outer peripheral portion of the coil portion 25 and at the central portion in the axial direction of the coil portion 25, and one lead portion 202 of the conductor 20 extends from one winding end. The coil portion 25 is drawn in the radial direction, and the other lead portion 203 is drawn in the radial direction of the coil portion 25 from the other winding end. Here, the central portion in the axial direction of the coil portion 25 refers to a portion excluding both ends 201 a and 201 b in the axial direction of the coil portion 25. The lead-out positions of the one lead-out portion 202 and the other lead-out portion 203 of the conductor 20 from the coil portion 25 do not have to completely coincide with the center of the coil portion 25 in the axial direction. It may be shifted. However, the shift amount is preferably 1.5 times or less the diameter of the conductor 20. In the present embodiment, as shown in FIG. 2B, the amount of deviation of the drawing position between the one drawing portion 202 and the other drawing portion 203 is about 0.5 times the diameter of the conductor 20.

As shown in FIGS. 2 and 3, the inner portion of the coil portion 25 is formed by winding the conductor 20 in the axial direction for a plurality of turns (three turns in this embodiment). Moreover, the outer peripheral part of the coil part 25 winds the conductor 20 spirally once from the 201a side of the coil part 25 in the axial direction toward the center of the coil part 25 in the axial direction, and the coil part 25 in the axial direction. It is formed by winding spirally from the other end 201b toward the center of the coil portion 25 in the axial direction.

One lead-out portion 202 and the other lead-out portion 203 of the conductor 20 are straight without any step, and extend substantially parallel to the soft magnetic metal dust core 10 mounting surface 101 and the opposing surface 102. Yes. One lead portion 202 is exposed from the side surface 106 of the soft magnetic metal dust core 10, and the other lead portion 203 is exposed from the side surface 110 of the soft magnetic metal dust core 10. The exposed positions of the one lead portion 202 and the other lead portion 203 of the conductor 10 are the center portions of the side surfaces 106 and 110 in the height direction.

The soft magnetic metal dust core 10 is obtained by press-molding soft magnetic metal particles. A detailed description of the soft magnetic metal particles will be described later.
The soft magnetic metal dust core 10 is produced by adding and mixing a binder having an insulating property to soft magnetic metal particles, and then pressurizing under predetermined conditions. Therefore, in the soft magnetic metal dust core 10, the soft magnetic metal particles are coated with a binder. Moreover, it is preferable to add and mix a lubricant after drying the soft magnetic metal particles to which the binder has been added.

The surface of the soft magnetic metal particles constituting the soft magnetic metal dust core 10 is coated with a binder. The binder is appropriately selected according to the required properties of the dust core. For example, various organic polymer resins, silicone resins, phenol resins, epoxy resins, water glass, etc. are used as binders. Further, these resins and inorganic substances may be used in combination. Depending on the required properties of the powder magnetic core, the amount of the binder added varies, but about 1 to 10% by mass can be added. When the added amount of the binder exceeds 10% by mass, the magnetic permeability decreases and the loss tends to increase. On the other hand, when the added amount of the binder is less than 1% by mass, there is a possibility of insulation failure. A preferable addition amount of the binder is 1.5 to 5% by mass.

The addition amount of the lubricant can be about 0.1 to 1% by mass, the preferable addition amount of the lubricant is 0.2 to 0.8% by mass, and the more preferable addition amount is 0.3 to 0.00%. 8% by mass. When the addition amount of the lubricant is less than 0.1% by mass, it is difficult to remove the mold after molding, and molding cracks are likely to occur. On the other hand, when the lubricant exceeds 1% by mass, the density is lowered and the magnetic permeability is reduced. The lubricant may be appropriately selected from, for example, aluminum stearate, barium stearate, magnesium stearate, calcium stearate, zinc stearate and strontium stearate. In view of small springback, it is preferable to use aluminum stearate as a lubricant.

A predetermined amount of a crosslinking agent can be added to the soft magnetic metal particles coated with the binder. By adding a cross-linking agent, the strength can be increased without deteriorating the magnetic properties of the soft magnetic metal dust core 10. A preferable addition amount of the crosslinking agent is 10 to 40% by mass with respect to a binder such as a silicone resin. As the crosslinking agent, an organic titanium-based one can be used.

Next, a method for manufacturing a coil-embedded dust core according to this embodiment will be described with reference to FIGS.
FIG. 3 is a flowchart showing the method for manufacturing the coil-embedded dust core according to the present embodiment. Note that the conductor 20 having the coil portion 25 is prepared in advance.

(Weighing process, mixing process, drying process, crushing process, lubricant adding process)
Each of the soft magnetic metal particles and the binder is weighed (step S201). Here, when adding a crosslinking agent, it measures in step S201.
After the weighing, the soft magnetic metal particles and the binder are mixed (step S202). When adding a crosslinking agent, soft magnetic metal particles, a binder, and a crosslinking agent are mixed in step S202. Mixing is performed using a pressure kneader or the like, preferably at room temperature for 20 to 60 minutes.
The obtained mixture is preferably dried at about 100 to 300 ° C. for 20 to 60 minutes (step S203).
Since the dried mixture is granulated into aggregates, the dried mixture is sized to obtain soft magnetic metal particles for powdered magnetic powder (step S204). The sizing is obtained by crushing using a mesh or the like.
If a lubricant is required when forming the dust core, the lubricant is added to the soft magnetic metal particles for the dust core (step S205). After adding the lubricant, it is preferably mixed for 10 to 40 minutes. Mixing can be performed using an air-fuel mixture such as a V mixer.

(Molding process)
In the molding process, the soft magnetic metal particles for the dust core and the embedded coil portion 25 are integrally formed to form a coil-embedded dust core (step S206). Here, the details of the molding process will be described with reference to FIG.
In FIG. 4A, the soft magnetic metal particles for the dust core are filled in the mold formed by the mold 5 and the lower punch 7.
In FIG. 4B, the conductor 20 is placed on the soft magnetic metal particles for the dust core in the mold. Here, it is preferable to fix the conductor 20 to the mold 5. As a result, the conductor 20 does not move during the molding and is stabilized, so that the positional variation of the conductor 20 is reduced. Moreover, since the crack will arise in the outer surface of a coil enclosure dust core if the position of the conductor 20 remove | deviates from a predetermined position, a crack is prevented by fixing the conductor 20 to the fixed position of the frame type 5. Can do. For example, the frame mold 5 divided into the upper frame mold 5A and the lower frame mold 5B is used, and the end of the conductor 20 can be fixed between the upper frame mold 5A and the lower frame mold 5B. Furthermore, it is preferable that the radial direction (Y direction shown in FIG. 2B) of the coil portion 25 of the conductor 20 is fixed so as to be parallel to the lower punch 7 and the upper punch 6. As a result, the distortion of the conductor 20 due to pressure molding is reduced, and performance degradation can be suppressed.
In FIG. 4C, the soft magnetic metal particles for the dust core are filled again into the mold so that the conductor 1 is filled.
In FIG. 4 (D), by lowering the upper punch 6, pressure is applied in the direction in which the soft magnetic metal particles for the dust core and the conductor 20 are laminated to form a molded body. .

The molding conditions in the pressure molding process are not particularly limited, and may be appropriately determined according to the shape and size of the soft magnetic metal particles and the shape, size and density of the coil-embedded dust core. Is about 100 to 2000 MPa, preferably about 100 to 1000 MPa, and the time for maintaining the maximum pressure is about 0.1 to 1 minute. If the molding pressure is too low, it is difficult to obtain sufficient characteristics and mechanical strength. On the other hand, if the molding pressure is too high, the conductor 20 may be broken or short-circuited and characteristics may not be obtained.

(Cure process, rust prevention process)
The molded body obtained in the molding step (step S206) is held at a temperature of 150 to 300 ° C. for about 15 to 60 minutes (step S207). Thereby, the binder in the molded body is cured.
After the heat treatment, a rust prevention treatment is performed (step S208). The rust prevention treatment is performed, for example, by spray coating an epoxy resin or the like on the molded body. The film thickness by spray coating is about 15 μm. After spray coating, it is desirable to perform heat treatment at 120 to 200 ° C. for 10 to 60 minutes.

(Sandblasting process)
As described above, in the coil-embedded dust core according to this embodiment, a part of the conductor 20 is used as the fusion part (302a, 302b). However, an insulating coating such as enamel is formed on the surface of the copper wire used for the conductor 20 in the first place. In the curing process (step S207), a copper oxide film is formed immediately below the insulating film, and in addition, an insulating film is formed in the anticorrosion treatment process (step S208), so a three-layer film is formed. Has been. Since this three-layer film may not be sufficiently soldered when soldering in the next step, it is necessary to remove the three-layer film.
Examples of a method for removing the three-layer coating formed on the fusion part (302a, 302b) include a method for removing corrosion by chemicals, a method for removing mechanically, a sandblasting method, and the like. Since the thickness of the fusion part (302a, 302b) of the powder magnetic core is as thin as 5 mm or less (about 0.1 to 0.3 mm), the sand blasting method is adopted in this embodiment (step S209).

(Soldering process)
The fusion part 302a and the metal fitting 30 are soldered and welded (step S).
210). Thereafter, crushing is performed, and bending is performed along the recess 103. Similarly, the fusion part 302b and the metal fitting 32 are soldered and welded, then crushed, and bent along the recess 107.

Next, the soft magnetic metal powder that is a component of the coil-embedded dust core according to the present embodiment will be described.

In order to reduce the loss of the coil-embedded dust core, it is known to reduce the coercive force of the soft magnetic metal particles constituting the coil-embedded dust core. And it is known that the larger the crystal grain size in the soft magnetic metal particles, the lower the coercive force. As a method for producing such a soft magnetic metal particle having a large crystal grain size, for example, there is a method of growing the crystal grain size by performing heat treatment. In order to obtain a sufficiently large crystal grain size, it is necessary to perform heat treatment at a high temperature of 1200 ° C. or higher, for example, depending on the composition of the metal particles. However, when heat treatment is performed at 1000 ° C. or higher, there is a problem in that adjacent metal particles adhere to each other during the treatment and cause a sintering reaction.

On the other hand, for example, there is a method of adding an anti-sintering material during high-temperature heat treatment, but in this case, the mixed oxide and nitride fine particles are unevenly distributed without covering the surface of the metal particles. However, the heat treatment at a high temperature of 1000 ° C. or more has a problem that the metal particles are fixed to each other and a powder cannot be obtained. Therefore, in order to improve this, a technique for coating the entire surface of the soft magnetic metal powder particles with a boron nitride film having a high melting point and extremely low reactivity with a metal at a high temperature was studied, and the present invention was reached. .

The problem with coating the entire surface of the soft magnetic metal particles is the technique of forming boron nitride (powder or coating) on the outside of the soft magnetic metal powder. In the method of adhering to the surface or the method of forming a film with boron nitride powder, it is inevitable that the boron nitride distribution becomes non-uniform. In view of this, it was considered that a uniform and stable sintering-preventing layer could be formed by forming directly on the outside of the soft magnetic metal powder particles.
In the present invention, raw material powder containing Fe and Ni as main components and containing B is prepared, and this raw material powder is subjected to high-temperature heat treatment in a non-oxidizing atmosphere containing nitrogen. By this high-temperature heat treatment, B in the raw material powder particles diffuses to the particle surface and reacts with nitrogen at the particle surface portion to form boron nitride. After the high-temperature heat treatment, it becomes a soft magnetic metal powder having a structure having boron flakes on the particle surface and containing 10 to 150 ppm of B inside the particle (metal portion excluding boron nitride on the surface).

Among soft magnetic metal materials containing Fe as a main component, B is known as an amorphous forming element. When an amorphous metal material is produced, 3 mass% or more with respect to the soft magnetic metal material containing Fe. A large amount of B is added. Further, in the case of producing a soft magnetic metal material having a nanocrystalline structure, a large amount of B is added because it is necessary to make an amorphous structure once in the manufacturing method. However, when B is added to a soft magnetic metal material containing general crystalline Fe, which is not an amorphous metal material or a soft magnetic metal material having a nanocrystalline structure, the magnetocrystalline anisotropy of Fe ₂ B, FeB, etc. Addition of B was avoided because a large heterogeneous phase was formed and the coercive force was increased. However, in the present invention, it was found that a soft magnetic metal powder having a low coercive force can be obtained by adding B to a soft magnetic metal material containing crystalline Fe.

By adding B to the raw material powder containing Fe and heat-treating it in a nitrogen atmosphere, flaky boron nitride is formed in a film shape on the entire particle surface of the raw material powder. Due to the effect of the boron nitride flake film, high-temperature heat treatment was possible, and further, the B content inside the raw material powder particles was adjusted to 10 to 150 ppm to promote crystal grain growth and to obtain a low coercive force. State what is assumed as the reason.

When heat treatment is performed in a nitrogen atmosphere, B present in the vicinity of the surface of the raw material powder is nitrided to form a thin film of boron nitride flakes, and thus a uniform and free film is formed on the surface of the raw material powder particles. . This has the effect of preventing contact between the surfaces of the raw powder particles during the high temperature heat treatment. Since boron nitride has high chemical stability to metals and boron nitride itself is a hardly sinterable substance, even if high temperature heat treatment is performed, boron nitride does not react with each other. There is no sticking through the boron nitride. Furthermore, since boron nitride has a lower density than the raw material powder that is a metal, the formation of boron nitride flakes on the surface portion of the raw material powder particles has the effect of increasing the surface distance between adjacent raw material powders. This action also has an effect of preventing sintering of the raw material powder particles. Due to the above effects, heat treatment can be performed at a high temperature of 1000 ° C. or higher, which has been impossible in the past, and the coercive force can be reduced.

Another effect of obtaining low coercive force by containing B in the raw material powder particles will be described.
B existing inside the raw material powder particles diffuses toward the particle surface of the raw material powder during the heat treatment. The diffusion of B facilitates the movement of crystal grain boundaries in the direction of the particle surface of the raw material powder, and therefore has the effect of promoting crystal grain growth. However, when there is an intermetallic compound such as Fe ₂ B inside the particles of the raw material powder, the intermetallic compound such as Fe ₂ B is unevenly distributed at the crystal grain boundary, and therefore, accompanying the diffusion of B in the particle surface direction Grain boundary movement is hindered, and crystal grain growth does not progress much. When the B content in the particles of the soft magnetic metal powder is 10 to 150 ppm, the effect of promoting the crystal grain growth can be confirmed. Therefore, in a very small amount of B content in which an intermetallic compound such as Fe ₂ B is not formed. This is considered to be a remarkable effect. The B that has moved to the particle surface is nitrided to form new boron nitride flakes.
From the above, by including B in the particles of the raw material powder, the effect of forming a good anti-sintering film that can withstand high temperatures and the effect of promoting crystal grain growth, a double effect is obtained, It becomes possible to obtain a soft magnetic metal powder having an extremely low coercive force.

(About the characteristic of the soft magnetic metal powder of this embodiment)
The soft magnetic metal powder of the present embodiment is a soft magnetic metal powder containing B and containing Fe and Ni as main components, and the B content in the particles of the soft magnetic metal powder is 10 to 150 ppm. It has flaky boron nitride on the metal particle surface. By setting the B content of the soft magnetic metal powder particles to 10 to 150 ppm, the coercive force becomes sufficiently small. When 150 ppm or more of B is present in the metal particles, a ferromagnetic phase such as Fe ₂ B having a large magnetocrystalline anisotropy is formed and crystal grain growth is inhibited, which causes an increase in coercive force. About several ppm of B is dissolved in the bcc phase of the parent phase of the soft magnetic metal powder particles, and the diffusion rate decreases as the B concentration in the particles decreases. It is difficult to make B 10 ppm or less. The content of Ni in the soft magnetic metal powder is 30 to 80% by mass. When the Ni content is less than 30% by mass, the magnetocrystalline anisotropy and the magnetostriction constant are increased, so that good soft magnetic properties cannot be obtained. When the Ni content is more than 80% by mass, the coercive force is increased, so that good soft magnetic properties cannot be obtained.

The B content in the particles of the soft magnetic metal powder can be quantified using ICP emission spectroscopy analysis (Inductively Coupled Plasma Atomic Emission Spectroscopy). At this time, by completely removing boron nitride adhering to the surface of the soft magnetic metal powder, the amount of B in the grains can be accurately quantified. Therefore, when measuring the B content, the boron nitride adhering to the surface of the soft magnetic metal powder is scraped off using a ball mill or the like, or the surface of the soft magnetic metal powder is slightly dissolved with an acid to nitride the surface of the soft magnetic metal powder. After liberating boron, the boron nitride is separated from the soft magnetic metal powder by washing away, and the remaining soft magnetic metal powder is quantified by ICP.

The soft magnetic metal powder of the present embodiment is a soft magnetic metal powder having a smaller coercive force when the circularity of the cross section of 90% or more of the particles constituting the soft magnetic metal powder is 0.80 or more. Can be obtained. The obtained soft magnetic metal powder is fixed with a cold embedding resin, the cross section is cut out and mirror-polished, whereby the cross-sectional shape of the particles can be observed. At least 20 (preferably 100 or more) cross sections of the particles thus prepared are observed at random, and the circularity of each particle is obtained. As an example of circularity, Wadell's circularity can be used, which is defined by the ratio of the diameter of a circle equal to the projected area of the particle cross section to the diameter of the circle circumscribing the particle cross section. In the case of a perfect circle, Wadell's circularity is 1, and the closer to 1, the higher the roundness, and if it is 0.80 or more, it can be regarded as a substantially spherical appearance. An optical microscope or SEM (Scanning Electron Microscope) can be used for observation, and image analysis can be used for calculation of circularity.

The soft magnetic metal powder of this embodiment is a soft magnetic metal powder in which 90% or more of the particles constituting the soft magnetic metal powder are composed of one crystal grain, thereby obtaining a soft magnetic metal powder having a smaller coercive force. Can do. By performing a high temperature heat treatment exceeding 1000 ° C., 90% or more of the particles constituting the soft magnetic metal powder can be made into a soft magnetic metal powder composed of one crystal grain. The obtained soft magnetic metal powder is fixed with a cold embedding resin, a cross section is cut out, mirror-polished, and then etched with nital (ethanol + 1% nitric acid), whereby crystal grain boundaries can be observed. When the cross-section of the particles prepared in this way is observed at least 20 randomly, preferably 100 or more, and the number of particles in which no crystal grain boundary is observed is counted as particles consisting of one crystal grain, 90% or more consists of one crystal grain. In some cases, there are grains incomplete grain growth by heat treatment, so that all grains do not consist of one crystal grain. An optical microscope or SEM can be used for observation.

The soft magnetic metal powder of this embodiment can obtain a soft magnetic metal powder having a smaller coercive force by setting the amount of oxygen contained in the particles to 500 ppm or less. By performing heat treatment in a reducing atmosphere, the amount of oxygen contained in the particles can be reduced to 500 ppm or less.

The soft magnetic metal powder of this embodiment can obtain a soft magnetic metal powder having a smaller coercive force by setting the amount of nitrogen contained in the particles to 2000 ppm or less. When heat treatment is performed in a nitrogen atmosphere, it reacts with B in the particles, so nitrogen does not penetrate into the particles, but if excessive nitriding is performed, a heterogeneous phase such as FeN is generated in the particles, resulting in deterioration of characteristics. The amount of nitrogen is 2000 ppm or less.

The average particle size of the soft magnetic metal powder of the present embodiment is preferably 1 to 200 μm. When the average particle size is less than 1 μm, the magnetic permeability of the soft magnetic metal dust core decreases. On the other hand, if the average particle size exceeds 200 μm, the intra-grain eddy current loss of the soft magnetic metal dust core increases.

(About raw material powder)
A method for producing the raw material powder of the soft magnetic metal powder is not particularly limited, and for example, a method such as a water atomizing method, a gas atomizing method, or a casting pulverization method can be used. When the raw material powder produced by the gas atomization method is used, it becomes easy to obtain a soft magnetic metal powder in which the circularity of the cross section of 90% or more of the particles constituting the soft magnetic metal powder is 0.80 or more. .

The raw material powder is a metal powder made of an Fe alloy mainly composed of Fe and Ni, and contains B. The Ni content of the raw material powder is adjusted to 30 to 80% by mass, and the total content of Fe and Ni is adjusted to 90% by mass or more. The B content of the raw material powder is preferably 0.1% by mass or more and 2.0% by mass or less. This is because if the content is less than 0.1% by mass, the B content is too small to form a boron nitride film that is uniform and has no gaps, and the particles are sintered when subjected to high-temperature heat treatment. The higher the B content of the raw material powder, the greater the load of heat treatment for setting the B content in the soft magnetic metal powder particles to 150 ppm or less.

(About heat treatment)
The raw material powder containing B is subjected to high-temperature heat treatment in a non-oxidizing atmosphere containing nitrogen. This heat treatment releases the strain and increases the crystal grain size. In order to obtain a sufficiently low coercive force, the heat treatment is performed in a non-oxidizing atmosphere containing nitrogen at a rate of temperature increase of 5 ° C./min or less, a temperature of 1000 to 1400 ° C., and a holding time of 30 to 600 min. By performing this heat treatment, nitrogen in the atmosphere reacts with B in the raw material powder to form a thin film of boron nitride on the particle surface and to grow crystal grains of the raw material powder particles. The soft magnetic metal powder obtained by performing this heat treatment is composed of one crystal grain of 95% or more of the particles constituting the soft magnetic metal powder, that is, single crystal particles that are ideal for low coercivity It becomes the state of. When the heat treatment temperature is less than 1000 ° C., the nitriding reaction of B in the raw material powder becomes insufficient, and a ferromagnetic phase such as Fe ₂ B remains and the coercive force is not sufficiently lowered. Furthermore, the crystal grain growth of the raw material powder becomes insufficient. When the heat treatment temperature exceeds 1400 ° C., nitridation proceeds promptly to complete the reaction, and crystal grain growth also proceeds promptly to form a single crystal. Therefore, even if the temperature is raised further, there is no effect. The high temperature heat treatment is performed in a non-oxidizing atmosphere containing nitrogen. The heat treatment is performed in a non-oxidizing atmosphere to prevent the soft magnetic metal powder from being oxidized. If the temperature rising rate is too high, the raw material powder particles reach a temperature at which the raw material powder particles are sintered before a sufficient amount of boron nitride is produced, and the raw material powder is sintered. The following.

The raw material powder is loaded into a container such as a crucible or a mortar. The material of the container is required not to be deformed at a high temperature of 1500 ° C. and not to react with a metal. As an example, alumina can be used. As the heat treatment furnace, a continuous furnace such as a pusher furnace or a roller hearth furnace, a box furnace, or a batch furnace such as a tubular furnace or a vacuum furnace can be used.

(About soft magnetic metal dust core)
Since the soft magnetic metal powder obtained in this embodiment shows a low coercive force, the loss is reduced when it is used for a soft magnetic metal dust core. Therefore, the loss is reduced even when the coil-embedded dust core integrated with the coil conductor is used.

When a soft magnetic powder core is produced using the soft magnetic metal powder of this embodiment, a part of the boron nitride flakes coated on the surface of the soft magnetic metal powder falls off. Although this does not cause any problems in the performance as a coil-embedded dust core, the insulating property of the binder is further improved by diffusing the insulating boron nitride flakes into the binder. Contributes to improving the properties of the metal core. Also, unlike the method of attaching a sintering inhibitor from the outside of the particle, the boron nitride flakes generated from the particle surface of the soft magnetic metal powder are strongly bonded to the particle surface. The metal surface is not exposed from the surface of the magnetic metal particles. Therefore, since an insulating part can be formed between adjacent soft magnetic metal particles, the DC superposition characteristics of the soft magnetic metal core are improved.
The boron nitride contained in the coil-embedded dust core of this embodiment is preferably 45-33000 ppm. When boron nitride exceeds 33000 ppm, the binding strength of the resin is lowered, the strength of the molded product is lowered, and cracks are likely to occur. Further, boron nitride adhering to the surface of the soft magnetic metal powder can be scraped off using a ball mill or the like, but enormous time is required to make it less than 45 ppm, resulting in high costs and distortion caused by scraping. Since the coercive force increases, the lower limit is 45 ppm.

The preferred embodiment of the present invention has been described above, but the present invention is not limited to the above embodiment. The present invention can be variously modified without departing from the gist thereof.

<Examples 1-1 to 6, Comparative Example 1-1>
Each raw material powder shown in Table 1 produced by the atomizing method was prepared. The raw material powder was adjusted in particle size by sieving to have an average particle size of 75 μm. This powder was loaded into an alumina crucible, placed in a tubular furnace, and subjected to high-temperature heat treatment for 60 minutes in a nitrogen atmosphere. The B content in the metal particles of the obtained soft magnetic metal powder was quantified using ICP. The average particle size is a numerical value measured by a laser diffraction particle size measuring device (HELOS, manufactured by JEOL).

<Comparative Examples 1-2-5>
Each raw material powder shown in Table 1 produced by the atomizing method was prepared. The raw material powder was adjusted in particle size by sieving to have an average particle size of 75 μm. As shown in Table 1, 1.5% by mass of a sintering inhibitor was added to the powder, and then mixed with a V mixer for 30 minutes. Next, the raw material powder was loaded into an alumina crucible, placed in a tubular furnace, and subjected to high temperature heat treatment for 60 minutes in a nitrogen atmosphere. As the sintering inhibitor, boron nitride powder having an average particle diameter of 1 μm was used.

<Comparative Example 1-6>
The raw material powder shown in Table 1 produced by the atomizing method was prepared. The raw material powder was adjusted in particle size by sieving to have an average particle size of 75 μm. The raw material powder was loaded into an alumina crucible, placed in a tubular furnace, and subjected to high temperature heat treatment at 1300 ° C. for 60 minutes in a nitrogen atmosphere.

<Comparative Example 1-7>
The raw material powder shown in Table 1 produced by the atomizing method was prepared. The raw material powder was adjusted in particle size by sieving to have an average particle size of 75 μm.

For each soft magnetic metal powder shown in Table 1, the boron nitride flakes can be reduced. The boron nitride flake reduction treatment is performed by putting soft magnetic metal powder in a plastic bottle, adding 3 mm diameter zirconia balls and ethanol, treating with a ball mill for 5 to 1200 minutes, scraping the boron nitride on the particle surface, and removing the powder from the plastic bottle. The boron nitride peeled from the particle surface was washed away with ethanol. By reducing the amount of boron nitride flakes, the characteristics of the coil-embedded dust core can be arbitrarily adjusted, which is effective.

To 100% by mass of each soft magnetic metal powder shown in Table 1, 2.4% by mass of a silicone resin (SR2414LV manufactured by Toray Dow Corning Silicone) was added, and after mixing them for 30 minutes with a pressure kneader, 110% in air. Dry at 30 ° C. for 30 min. The dried soft magnetic metal particles for the dust core are sized with a 355 μm mesh, and then 0.2 mass% aluminum stearate (SA-1000 manufactured by Sakai Chemical Industry Co., Ltd.) is added to the V mixer. For 15 min. This was molded by the procedure shown in FIG. 4 to produce a molded body of 100 mm square and 60 mm height. Molding was performed at a molding pressure of 980 MPa. The coil used was a 7 mm diameter circular copper wire wound three times. The obtained molded body was cured in a belt furnace. The curing conditions were 160 ° C. and 30 minutes in a nitrogen atmosphere. The obtained coil-embedded dust core was evaluated for magnetic permeability, loss, and inductance. The magnetic permeability and loss were measured using an LCR meter (4285A manufactured by Agilent Technologies) under the conditions of a frequency of 50 kHz and a measurement magnetic flux density of 50 mT. Inductance was measured using an LCR meter. The results are shown in Table 1. In Table 1, L0 indicates an inductance in a state where no DC current is superimposed, and L15 indicates an inductance in a state where a DC current of 15A is superimposed.

From Table 1, when the raw material powder to which B was added was heat-treated at a temperature of 1000 ° C. or higher as in Examples 1 to 6, the amount of B in the soft magnetic metal powder was 150 ppm or less, compared with Comparative Example 1-7. The coercivity was sufficiently small.
In Comparative Example 1-1, the same raw material powder to which B was added as in Example 1 was used. However, since the heat treatment temperature was low, the crystal grain size in the soft magnetic metal powder particles was not increased, and sufficient coercive force was obtained. It was not obtained.
Comparative Examples 1-2 to 5 were performed by a method in which a sintering inhibitor was attached to the particle surface of the soft magnetic metal powder. However, since adhesion occurred in some adjacent particles, crushing was necessary, and the coercive force Was not sufficiently small as compared with Examples 1-6.
In Comparative Example 1-6, since the sintering inhibitor or B was not added, the entire soft magnetic metal powder after the heat treatment was sintered, and the powder could not be obtained.
Comparative Example 1-7 has a large coercive force because it has not been heat-treated.
From Table 1, the loss of Examples 1-1 to 6 is sufficiently lower than that of Comparative Example 1-7. Similarly, Examples 1-1 to 6 have high magnetic permeability and excellent DC superposition characteristics. Moreover, even if it compares with the loss of Comparative Examples 1-1-6, it turns out that the loss of Examples 1-1-6 is low enough.

Next, the coil-embedded dust core of Example 1-6 was fixed with cold embedding resin, cut out, and mirror-polished. Then, structure | tissue observation was performed using SEM (scanning electron microscope), and elemental mapping by EPMA (Electron Probe Micro Analyzer) was performed. FIG. 6 shows mapping data of (a) SEM image, (b) nitrogen and (c) B.
From the mapping data, nitrogen and B were strongly detected from different sites from the soft magnetic metal powder and the pores, and the portion where both nitrogen and B were detected from the image analysis was judged to be boron nitride. From FIG. 6, nitrogen and B are not detected in the soft magnetic metal particle portion. Therefore, it can be seen that boron nitride is mixed in the binder. The amount of boron nitride in the green compact in Table 1 was calculated from the value detected by EPMA.
When similar evaluation was performed on the coil-embedded dust cores of Examples 1-1 to 5, it was confirmed that boron nitride was mixed in the binder. When the same evaluation was performed for the coil-embedded dust core of Comparative Example 1-7, no boron nitride could be confirmed in the binder.

<Examples 2-1 to 6>
Subsequently, each coil-embedded dust core shown in Table 2 was fixed with cold embedding resin, a cross section was cut out, and mirror polishing was performed. 100 cross sections of the particles were observed at random, the Wadell circularity of each particle was measured, and the proportion of particles having a circularity of 0.80 or more was calculated. The results are shown in Table 2.
Further, after the mirror-polished particle cross section was etched with nital (ethanol + 1% nitric acid), the crystal grain boundaries of 100 randomly selected particles were observed, and the ratio of particles consisting of one crystal grain was calculated. The results are shown in Table 2.

From the results of Table 2, when the ratio of particles having a circularity of the cross section of the particles of 0.80 or more is 90% or more, 90% or more of the particles constituting the soft magnetic metal powder are formed from one crystal grain. As a result, the loss of the coil-embedded dust core is reduced. This is because the coercive force of the soft magnetic metal powder constituting the coil-embedded dust core is sufficiently small.

<Examples 3-1 to 4 and Comparative Examples 3-1 to 4>
A soft magnetic metal powder was produced in the same manner as in Example 1-1 except that the heat treatment time was changed. The heat treatment temperature was 1300 ° C. About the obtained soft magnetic metal powder, B content and coercive force were measured. Next, a coil-embedded dust core was produced in the same manner as in Example 1-1. The magnetic permeability and loss of the obtained coil-embedded dust core were evaluated. Further, the coil-embedded dust core is fixed with cold embedding resin, the cross section is cut out, mirror polishing is performed, and the ratio of particles having a circularity of 0.80 or more and the ratio of particles composed of one crystal grain Calculation was performed. The results are shown in Table 3.

From Table 3, when the heat treatment time is shorter than 30 minutes, the diffusion of B becomes insufficient, and B in the particles of the soft magnetic metal powder cannot reach the particle surface and remains. Further, since the crystal growth in the particles is insufficient, the coercive force of the soft magnetic metal powder does not decrease. Therefore, the loss of the coil-embedded dust core does not decrease. When the heat treatment time was 30 min or more, the B content in the soft magnetic metal powder was 150 ppm or less, and the coercive force was sufficiently low. Moreover, the coil-embedded dust core produced using this soft magnetic metal powder had a sufficiently low loss. The coil-embedded dust core should be composed of 90% or more of particles having a circularity of 0.80 or more and 90% or more of particles composed of one crystal grain. Observed.

<Examples 4-1 to 4 and Comparative Example 4-1>
A soft magnetic metal powder was produced in the same manner as in Example 3-1, except that the amount of B added to the raw material powder was changed. About the obtained soft magnetic metal powder, B content and coercive force were measured. Next, a coil-embedded dust core was produced in the same manner as in Example 1-1. The magnetic permeability and loss of the obtained coil-embedded dust core were evaluated. Further, the coil-embedded dust core is fixed with cold embedding resin, the cross section is cut out, mirror polishing is performed, and the ratio of particles having a circularity of 0.80 or more and the ratio of particles composed of one crystal grain Calculation was performed. The results are shown in Table 4.

From Table 4, when B is added excessively, the crystal grain growth in the particles becomes insufficient, and the coercive force of the soft magnetic metal powder does not decrease. When the B content was 150 ppm or less, the crystals in the grains were sufficiently grown, so that the coercive force was sufficiently low. Moreover, the coil-embedded dust core produced using this soft magnetic metal powder had a sufficiently low loss. The coil-embedded dust core should be composed of 90% or more of particles having a circularity of 0.80 or more and 90% or more of particles composed of one crystal grain. Observed.

<Examples 5-1 to 5 and Comparative Examples 5-1 to 2>
A soft magnetic metal powder was produced in the same manner as in Example 3-1, except that the amount of Ni added to the raw material powder was changed. Next, a coil-embedded dust core was produced in the same manner as in Example 1-1. The magnetic permeability and loss of the obtained coil-embedded dust core were evaluated. Further, the coil-embedded dust core is fixed with cold embedding resin, the cross section is cut out, mirror polishing is performed, and the ratio of particles having a circularity of 0.80 or more and the ratio of particles composed of one crystal grain Calculation was performed. The results are shown in Table 5.

From Table 5, the soft magnetic metal powder in which Ni is in the range of 30 to 80% by mass has a sufficiently low coercive force, and the loss of the coil-embedded dust core using the soft magnetic metal powder is also low. If Ni is lower than 30% by mass or exceeds 80% by mass, the coercive force of the soft magnetic metal powder does not decrease. In the coil-embedded dust core in which Ni is in the range of 30 to 80% by mass, the proportion of particles having a circularity of 0.80 or more is 90% or more, and the proportion of particles composed of one crystal grain is 90%. It was observed that it was composed of more than%.

<Examples 6-1 to 6>
Soft magnetic metal powder was produced in the same manner as in Example 3-1, but the amount of oxygen and the amount of nitrogen were adjusted by adjusting the nitrogen atmosphere of the heat treatment. Using the obtained soft magnetic metal powder, a coil-embedded dust core was produced in the same manner as in Example 1-1. The magnetic permeability and loss of the obtained coil-embedded dust core were evaluated. Further, the coil-embedded dust core is fixed with cold embedding resin, the cross section is cut out, mirror polishing is performed, and the ratio of particles having a circularity of 0.80 or more and the ratio of particles composed of one crystal grain Calculation was performed. The results are shown in Table 6. The amount of oxygen and the amount of nitrogen were quantified using an oxygen-nitrogen analyzer (manufactured by LECO, TC600).

From Table 6, the soft magnetic metal powder having an oxygen content of 500 ppm or less and a nitrogen content of 2000 ppm or less has a sufficiently low coercive force, and the loss of the coil-embedded dust core using the soft magnetic metal powder is also low. Further, these coil-embedded dust cores are configured such that the ratio of particles having a circularity of 0.80 or more is 90% or more and the ratio of particles made of one crystal grain is 90% or more. It was observed that Even if the amount of oxygen exceeds 500 ppm or the amount of nitrogen exceeds 2000 ppm, the coercive force of the soft magnetic metal powder decreases, but the effect is small.

As described above, according to the present invention, it is possible to obtain a coil-embedded dust core with extremely low loss. Therefore, since high efficiency can be realized, it can be widely and effectively used for electric / magnetic devices such as power supply circuits.

It is a perspective view of the coil enclosure dust core in this embodiment. It is the top view and sectional drawing of a coil with which the coil enclosure dust core shown in FIG. 1 is provided. It is a figure for demonstrating the winding state of the coil shown in FIG. It is process drawing which shows the manufacturing process of the coil enclosure dust core in this embodiment. It is a figure which shows the formation process of the coil enclosure dust core in this embodiment. It is the SEM image and element mapping data of the cut surface of the coil enclosure dust core in this embodiment.

  C: Coiled powder magnetic core, 5 ... Formwork, 6 ... Upper punch, 7 ... Lower punch, 10 ... Molded body, 11 ... Lower core, 12 ... Upper core, 20 ... Conductor, 101 ... Mounting surface, 102 ... Opposing surfaces, 104 to 106, 108 to 110, side surfaces, 25, coil portions, 202, one drawing portion, 203, the other drawing portion,

Claims (6)

A green compact in which a soft magnetic metal powder mainly composed of Fe and Ni and a binder are mixed and pressed, and a coil embedded in the green compact, around which a conductor having an insulation coating is wound. A pair of lead wires respectively drawn out from the coil to the outside of the green compact; and a terminal fitting connected to the lead wire outside the green compact; and the Ni content of the soft magnetic metal powder Is 30 to 80% by mass, the total content of Fe and Ni is 90% by mass or more, the B content in the metal particles of the soft magnetic metal powder is 10 to 150 ppm, and the binder in the green compact A coil-embedded dust core having an internal structure in which boron nitride is mixed. The coil-embedded dust core according to claim 1, wherein 90% or more of the particles constituting the soft magnetic metal powder have a circularity of a cross section of 0.80 or more. Coiled dust core. The coil-embedded dust core according to any one of claims 1 and 2, wherein 90% or more of the particles constituting the soft magnetic metal powder are composed of one crystal grain. Magnetic core. The coil-embedded dust core according to any one of claims 1 to 3, wherein the amount of oxygen contained in the particles of the soft magnetic metal powder is 500 ppm or less. . The coil-embedded dust core according to any one of claims 1 to 4, wherein the amount of nitrogen contained in the particles of the soft magnetic metal powder is 2000 ppm or less. . The coil-embedded dust core according to any one of claims 1 to 5, wherein boron nitride in the compact is 45 to 33000 ppm.

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