JP5110626B2 - Wire ring parts - Google Patents

Description

  The present invention relates to a wire ring component such as a choke coil for an electronic device and a transformer suitable for use in a region of several hundred kHz or less and a maximum applied magnetic field H = 3.98 kA / m or more.

  Application destinations of these wire ring components include, for example, wire ring components for increasing voltage control and decreasing voltage control used for solar power generation, wind power generation, and the like. The implementation of concrete measures to combat global warming has become an urgent task, and competition for clean energy such as fuel cell vehicles has intensified. Furthermore, in the private sector such as home and business, the government and local governments have strengthened subsidies, and have begun to establish a decentralized power generation system that does not emit greenhouse gases such as solar power generation, small wind power generation, and fuel cell power generation. Yes.

  As element technologies common to these fuel cell vehicles and distributed power supply facilities, a DC voltage step-up / down circuit (DD converter) and a DC-AC converter circuit (inverter) are inserted in the power supply system. It is necessary not to consume power unnecessarily in this circuit.

  In the case of power conversion from direct current to alternating current by a DD converter or inverter circuit, the inductor for the filter to prevent the outflow of the harmonic current to the output system and the converter for raising and lowering the voltage instantaneously Inductors that can be stored as magnetic energy are required, and in all cases, optimum inductors that are small and light, energy-saving, resource-saving, and quiet are required.

  The conventional magnetic core has adjusted the direct current superposition characteristics by a macro gap. For this reason, leakage magnetic flux was generated and audible noise was easily generated. Moreover, the magnetic core of a closed magnetic circuit has been manufactured by press molding or injection molding in order to obtain a high magnetic permeability with a low magnetic field. However, for industrialization, investment in large-scale and expensive equipment and molds is required. In addition, as a method of manufacturing the magnetic core, there is a method of casting at a low pressure or a reduced pressure. However, since it is necessary to ensure fluidity, there is a problem that the filling rate of the magnetic powder cannot be increased so much.

  As a performance problem, when the drive frequency or standby mode frequency of a coil component is several kHz to several tens of kHz in the audible range, mutual attraction force is generated between the coil wires and between the coil and the magnetic core. Caused vibration occurs. For this reason, there is a problem of generating audible noise and beat.

  As is clear from the description in Patent Document 1, the frequency range targeted by the coil component described in Patent Document 1 is a so-called “high frequency”, which is a frequency region far exceeding the audible frequency. In fact, Patent Document 1 has a description of “several hundred kHz to MHz”, and the term “high frequency” is frequently used as a keyword.

  Even if the air gap part vibrates at a very high frequency of several hundred kHz to MHz, it will only generate sound that cannot be heard by the human ear, and it is possible that it will result in audible noise and beating as described above. Absent.

  Therefore, it is appropriate to consider a solution for audible noise and beat caused by driving in the audible frequency band, apart from the technique described in Patent Document 1. In addition, the coil component that is the target in Patent Document 1 is a coil component for a low-power system, as is clear from the size illustrated. Therefore, as a matter of course, a withstand voltage performance of several hundred volts or more or an unnecessary pulse current performance of several hundred amperes or more (resistance to unwanted current noise such as surge current) cannot be expected.

  As described above, it is appropriate to consider that it is inappropriate to use the coil component described in Patent Document 1 for high power / low frequency applications.

  In view of the above, the present invention provides a wire ring component that has high withstand voltage performance and high anti-unnecessary pulse current performance and can suppress audible noise and beat even when driven at a frequency that is in the audible frequency range. The purpose is to provide.

JP 2001-185421 A

  A need that cannot be dealt with by the prior art is a winding-integrated magnetic core without a macro gap. Even if the same soft magnetic material is used, the loss can be reduced by reducing the size of the winding as a single unit. At this time, the applied magnetic field H = N · I / le due to the magnetomotive force of the winding can be determined by the number of turns N, the maximum current I, and the effective magnetic path length le. Among them, the effective magnetic path length le can be reduced to reduce the size.

  However, since the applied magnetic field H becomes larger, it is necessary to obtain a higher magnetic permeability in the maximum applied magnetic field. In other words, even with the same material, up to which magnetic field is used, the effective cross-sectional area of the magnetic circuit differs depending on the external dimensions of the product. For this reason, the applied magnetic field and the magnetic permeability required of the material change.

  This time, the magnetic core and wire ring parts have been constructed at a lower price with a micro dispersion gap rather than a macro gap. In response to market needs, we have invented low-loss and quiet products centered on miniaturization.

  As electronic devices are becoming smaller and smaller, high-efficiency magnetic materials are required, and as choke coils used at high frequencies, ferrite cores, silicon steel plates / amorphous ribbons, dust cores, etc. are used. .

  Selection of a suitable magnetic core can be classified according to the driving frequency of the electronic device and the maximum applied magnetic field of the inductor.

  When H is less than 3.98 kA / m, ferrite having a gap is mainly used.

  Up to H = 7.96 kA / m, silicon steel plates with gaps are mainly used.

  Up to H = 15.92 kA / m, a dust core or a silicon steel plate with a gap is used.

  Furthermore, at 15.92 kA / m or more (H = 31.84 kA / m level), it is difficult to select a suitable magnetic core.

  The magnetic permeability of each soft magnetic material is determined by the winding, the maximum current, and the magnetic path length, and particularly depends on the applied magnetic field.

Area A: H = less than 3.98 kA / m The saturation magnetic flux density of the ferrite core is small. Moreover, the following problems can be pointed out in the case of a ferrite magnetic core provided with a gap. First, magnetic flux leaks to the outside of the magnetic core, generating eddy currents on the copper wire surface.

  When the litz wire is not used, the eddy current loss in the winding portion is large and the temperature rise of the inductor cannot be used remarkably. Next, as a countermeasure against eddy current loss in the winding portion due to leakage magnetic flux, a so-called litz wire in which a large number of thin copper wires are bundled is used. However, the litz wire has a lower space factor than the single wire, the direct current resistance increases, and a magnetic core having a larger size than that of the single wire is required to obtain the same inductance value. In addition, the litz wire is more expensive than the single wire.

  Ferrite has an excellent feature that its iron loss is remarkably low compared to silicon steel plates, amorphous ribbons and the like. However, when the gap is provided as described above, the advantage cannot be fully utilized due to the eddy current loss in the winding portion due to the leakage magnetic flux. Furthermore, since ferrite is made of a metal oxide, it has the disadvantages that the saturation magnetic flux density is essentially lower than that of a metal-based soft magnetic material, the magnetic flux is easily saturated, and the temperature dependence of loss is large. For this reason, the ferrite magnetic core has to prevent magnetic saturation by increasing the cross-sectional area of the magnetic core as compared with a magnetic core made of a metallic soft magnetic material, and it is difficult to reduce the size of the magnetic core.

Area B: H = Unless than 7.96 kA / m For example, a thin ribbon of 100 μm such as silicon steel can exhibit an advantage of particularly high μ in this range. When comparing with the same composition, the reason why the magnetic permeability is higher than that of the powdered magnetic core is that the demagnetizing factor is lowered by using a thin ribbon and the spin magnetization rotation mode having a low coercive force is used. However, due to the increase in eddy current loss due to the ribbon thickness, it can only be applied up to about 40 kHz. Although thinner ribbons are being developed, the manufacturing costs are very high. There is also a problem of processing accuracy of the macro gap portion.

Area C: Up to H = 1.92 kA / m For example, Sendust green compact is used. A dust core produced by molding soft magnetic powder has a higher saturation magnetic flux density than ferrite, which is advantageous for downsizing, but is superior to ferrite in terms of permeability and iron loss. However, it is difficult to reduce the size in that respect.

  For example, a ferrite core without a macro gap has an inductance L value that suddenly decreases with a DC superimposed current that becomes a magnetic field of about H = 1 kA / m, whereas a dust core without a macro gap has a DC superimposed current. It decreases gradually against. This is presumably because there is a distribution in the micro-dispersion gap present in the dust core. In order to ensure the permeability up to higher magnetic fields, it seems necessary to adapt the micro gap. When the microgap is increased, the magnetic permeability of the magnetic core tends to decrease.

  The core loss of a dust core usually consists of hysteresis loss and eddy current loss, but the eddy current loss increases in proportion to the square of the frequency and the square of the size through which the eddy current flows. The generation of eddy current is suppressed by covering the electrically insulating resin or the like. On the other hand, in order to increase the molding density of the dust core, it is usually necessary to apply a molding pressure of 500 MPa or more. Therefore, the hysteresis loss increases as the magnetic material increases in strain and the permeability deteriorates. It was something that would end up. In order to avoid this, a post-molding heat treatment is performed as necessary to release the strain. However, when high-temperature heat treatment is required, an insulating binder is necessary to insulate the magnetic powder and maintain the binding between the powders.

Area D: H = 31.84 kA / m level (15.92 kA / m or more)
Even in a dust core, in order to make the distribution of the magnetic flux density in a plurality of macro gaps and magnetic cores more uniform, it is an area that needs to be partially magnetized in the direction of difficult magnetization. It caused a significant increase in winding eddy current loss. In this region, it is difficult to select a suitable magnetic core.

  In order to secure the permeability in the magnetic field range to be used as described above, the present invention examines the region of the maximum applied magnetic field H = 3.98 kA / m or more to be used in an electronic device up to a frequency of several hundred kHz. An object of the present invention is to provide a wire ring component that is particularly suitable for downsizing of a magnetic core for an inductor such as a choke coil or a transformer used.

  The present inventors have found that a magnetic core having a microgap made of a mixture of a magnetic powder and a resin is preferably used as a ring component having a high current direct current superposition characteristic. In particular, since it is considered effective to increase the filling rate of the magnetic material and to make the micro gap uniform, the present invention was obtained as a result of studying the composition of the admixture for that purpose. is there.

  In the present invention, a magnetic core in which a group of molded bodies having an initial permeability of μdc = 10 or more and a gap between the groups of the molded bodies is filled with an admixture made of magnetic powder and resin and wound as a winding is used. A wire ring component is formed using a winding inclusion insulator obtained by surrounding with an insulating resin so as to exclude the end of the wire.

That is, the present invention relates to a winding inclusion insulator obtained by surrounding with an insulating resin so as to exclude the end of the winding, and an initial permeability μdc = 10 or more filled at least inside the winding inclusion insulator. And a group of the molded bodies are embedded in a solidified or cured mixture of the first magnetic powder and the second magnetic powder having a smaller diameter or the non-magnetic powder and the resin , The average particle diameter φ2 of the second magnetic powder or nonmagnetic powder is φ2 = <φ1 / 15 with respect to the average particle diameter φ1 of the first magnetic powder, and the second magnetic powder or nonmagnetic It is a wire ring part characterized by the volume fraction of body powder being 40 vol% or less of the whole .

  In the present invention, the admixture has an effective demagnetizing factor N of the first magnetic powder of 0.4 or less, and the first magnetic powder and the second magnetic powder or non-magnetic. The wire ring component is characterized in that the total filling rate with the body powder is 50 vol% or more and the relative permeability μdc is 2 or more.

  In addition, the present invention provides a wire ring component characterized in that half or less of the second magnetic powder or non-magnetic powder is a powder having a particle size of φ1 / 50 or less, preferably a substantially spherical powder. is there.

  The present invention also provides a wire ring component in which the resin or a mixture with the resin contains at least a thixotropic component.

Further, the present invention is characterized in that the winding encapsulated insulating material is impregnated with a mixture of the insulating resin and the insulating non-magnetic powder including at least the thixotropic component, it is obtained by solidifying or curing It is a wire ring part.

  The present invention also provides the wire ring component, wherein the magnetic powder is made of soft magnetic powder.

  The present invention also provides a wire ring component, wherein the magnetic powder includes at least a soft magnetic powder.

  Moreover, the present invention is a wire ring component in which a specific magnetic permeability core member having a relative magnetic permeability μdc of 1 is embedded.

  In addition, the present invention is the wire ring component further including a holding case, wherein at least a part of the mixture is solidified or hardened in the case.

  In the present invention, a group of molded bodies having a high relative permeability is used as the magnetic core, and a gap between these molded body groups is filled with a mixture of magnetic powder or the like and a resin so that a high magnetic permeability closed magnetic circuit magnet is obtained. A wick can be obtained. Conventionally, magnetic cores with a high magnetic permeability closed magnetic path have been manufactured by press molding or injection molding, but investment in large-scale and expensive equipment and molds is required, especially for large currents, Expensive investment was required for the production equipment for the ring parts. However, in the present invention, since a group of molded bodies is used as the magnetic core, a large molding apparatus is unnecessary, and capital investment can be reduced. In addition, by using a group of molded bodies, it is possible to manufacture a magnetic core having a high magnetic permeability at a lower cost than manufacturing a magnetic core using only a blend.

  Further, in the present invention, since the magnetic powder and the inorganic filler can be highly filled, heat dissipation and crack resistance are improved, and the device can be miniaturized as a wire ring part.

In the present invention, if the magnetic core of the conventional closed magnetic circuit as a wire ring component, a magnetic field that would be magnetically saturated,
H1 = 15.92 kA / m
H2 = 31.84 kA / m
H3 = 79.6 kA / m
The magnetic permeability at H = 7.96 kA / m or less could be significantly increased by using a group of molded bodies.

  Furthermore, since thixotropic properties are imparted, a) the viscosity when the slurry is stationary is increased, so that it can be stored for a long time in a state where the filler is dispersed. B) It enables uniform mixing and uniform dispersion of the filler at the time of blending. C) During casting, the fluidity of the slurry was ensured by carrying out vibration.

  In the wire ring component, since the winding is surrounded at least by an insulator, the winding is excellent in withstand voltage characteristics and unnecessary pulse current performance, and includes at least a magnetic powder. It is embedded in the magnetic core made of a mixture of resin and resin, and the movement of the winding is fixed. For this reason, even when driven in an audible frequency band, the amplitude of vibration that causes audible noise and beat is smaller.

  In the wire ring component according to the embodiment of the present invention, the winding component is arranged in a case or a mold for mold release, filled with a molded body having a high magnetic permeability, and further, a magnetic material or the like and a resin are formed in a gap therebetween. The mixture is cast to solidify or harden the mixture.

  1 and 2 are explanatory views of the wire ring component of the present invention. As shown in FIG. 1, a winding inclusion insulator 3 is arranged as a winding component in a casting mold (not shown in this figure), and is filled with a molded body 2 having a high magnetic permeability. The mixture 4 is obtained by casting. In some cases, as shown in FIG. 2, only the cylindrical portion may be filled with the molded body 2 having a high magnetic permeability.

  Since the mixture is cast and used, it is necessary to consider environmental considerations and energy saving in the manufacturing process during solidification or curing when the size of the wire ring part is large, especially when the coil part has a certain height or more. Therefore, it is preferable to use a resin that can be cast without adding a solvent.

  As a molded article having a high magnetic permeability (μ> 10), a soft magnetic green compact having a size of several mm is suitable. The shape of the molded body may be spherical, cylindrical, or other polyhedral shape, but is selected in consideration of manufacturing the molded body and filling the casting. For example, in the case of a columnar shape, it is easy to produce a molded body, and it is possible to fill it closely. However, it is necessary to consider the damage to the insulation coating of the coil inclusion insulator when filling the molded body. In order to fill the molded body densely, vibration filling is desirable. The possibility of damage increases. Therefore, a molded article with a high permeability having an acute-angled surface damages the winding inclusion insulator, and therefore it is desirable to use a substantially spherical or spherical molded article in consideration of filling workability.

  The magnetic powder constituting the soft magnetic compact as a molded body is preferably a soft magnetic powder, more specifically, an Fe-based soft magnetic magnetic powder. More specifically, the soft magnetic powder is a powder selected from the group consisting of Fe-Si powder, Fe-Si-Al powder, Fe-Ni powder, and Fe amorphous powder. Here, the average Si content in the Fe—Si based powder is preferably 11.0% by weight or less. The average Si content in the Fe—Si—Al-based powder is preferably 11.0% by weight or less, and the average Al content is preferably 7.0% by weight or less. Further, the average Ni content in the Fe—Ni-based powder is preferably 30.0 wt% or more and 85.0 wt% or less.

  These soft magnetic powders can be molded by press molding, injection molding, etc., and subjected to heat treatment such as sintering and annealing as necessary to obtain a desired soft magnetic compact with a relative permeability μ> 10. .

  In addition, regarding the winding, the integral configuration of the winding inclusion insulator and the magnetic core according to the present invention is a configuration in which a breakdown voltage failure due to a pinhole is likely to occur. In conventional inner iron type wire ring parts, measures are taken by bobbin, varnish impregnation and powder coating, but it is desirable to carry out by a method which is less likely to contain bubbles. Since the powder coating method is performed at normal pressure, there is a surface in which voids are generated between the coil wires and pinholes are easily generated. For this reason, in the case of the present invention, for the impregnation and adhesion between the coils and between the coil pedestals, the winding inclusion insulator is used by using an impregnation / adhesive in which an inorganic filler is uniformly dispersed in a thermosetting epoxy resin. It is desirable to manufacture.

  The wire ring component of the present invention is manufactured by placing a coil-containing insulator and a specific permeability magnetic core member in a mold, and casting and curing an admixture combined with a releasable resin to produce a magnetic core. Can be manufactured by removing the mold. Moreover, the wire ring component provided with the case can also be manufactured. By using part or all of the mold as a case, it is possible to manufacture without removing the mold. When the mold is not removed, it is not necessary to consider releasability, so that it is easy to manufacture a magnetic core having a complicated shape.

  Furthermore, a case that functions as a magnetic core may be used. For example, when a case functioning as a magnetic core is used as a common part with other parts, it is effective in a case where a winding part is once formed and then the winding part is placed in a case that is a common part. This case may be formed of other magnetic materials / alloys such as Fe-Ni alloys. When the case is made of a magnetic material, in order to ensure appropriate insulation performance, it is preferable to form an insulating film on the inner surface of the case and then cast the mixture to form a magnetic core. The case may be a ceramic case such as an alumina molded body, or may be made of an aluminum alloy.

  It is possible to provide a wire ring component that includes the case as described above and in which a winding inclusion insulator and a magnetic core made of the mixture fill a space between the case.

  The production flow of the wire ring part of the present invention will be described using a specific example. FIG. 3 shows a manufacturing flow of the wire ring component of the present invention. A winding inclusion insulator is placed in a case or a mold for release, and a high permeability molded body (for example, a Fe-Si-based spherical powder molded body having a diameter of 2 mm) is filled. In this case, first, a preheated molded body is introduced into an actual casting mold preheated from 100 ° C. to 150 ° C. and subjected to vibration filling.

  Next, the casting of the filled actual machine and the filled molded body are re-preheated. Next, under vacuum, an admixture of smaller-diameter magnetic powder, non-magnetic powder and resin is cast and impregnated in the gaps of the molded body group. Further, it is cured at 80 to 200 ° C. in a heat treatment furnace.

  As shown in the manufacturing flow of FIG. 3, it is desirable to heat the casting and the molded body before casting the mixture. This is because the surface electrical insulation is lowered by the adsorbed moisture of the molded body, and the impregnation property of the admixture is lowered.

  FIG. 4 shows the relationship between the moisture content of the molded body group and the dielectric breakdown voltage. As shown in FIG. 4, a decrease in the dielectric breakdown voltage can be prevented by reducing the amount of water adsorbed on the molded body group. This shows that it is desirable to preheat the temperature of the molded body to 100 ° C. or higher.

  Further, FIG. 5 shows the relationship between the preheating temperature of the molded body group and the resin impregnation rate of the admixture. As shown in FIG. 5, it is understood that the resin impregnation rate can be increased by preheating the molded body group to around 100 ° C. Furthermore, it can be seen that the impregnation rate of the resin can be increased by treating the surface of the molded body with a coupling agent such as silica as a pretreatment. As described above, the molded body is preferably surface-treated with a coupling agent and preheated at about 100 to 150 ° C. before filling.

  When this method is applied, as shown in Table 1, since the filling rate of the magnetic material can be increased as compared with the case where only the mixture is used without using the molded body, the thermal conductivity is improved. Thus, since heat conductivity improves, a wire ring component excellent in thermal shock resistance can be obtained. Furthermore, since the heat dissipation characteristics of heat generated by magnetic loss and the like are improved, the wire ring component can be downsized in some cases.

  In the case of using only the admixture, if the filling rate of the magnetic powder or the like is increased, the viscosity of the admixture increases, and the slurry cannot be cast, so the filling rate cannot be increased very much. Moreover, the mixture using the molded object over 1 mm in diameter is not used. On the other hand, in the present invention, the group of molded bodies is filled in advance, and the mixture is poured into the gap, so that the mixture needs to have a low viscosity as well so as not to impair the injection workability. Therefore, although the filling rate of the admixture does not change, the filling rate of the magnetic powder or the like can be increased for the group of molded products.

  FIG. 6 shows the relationship between the filling rate of magnetic powder and the thermal conductivity. FIG. 7 shows the relationship between the filling rate of magnetic powder and the linear expansion coefficient. As described above, in the wire ring part of the present invention, the filling rate of magnetic powder or the like can be increased, and as shown in FIG. 6, the thermal conductivity is about compared to the case where only the admixture is used. It can be doubled, the heat dissipation inside the part can be increased, and the temperature rise can be reduced. Furthermore, the crack resistance can be improved in combination with the low expansion coefficient effect as shown in FIG.

  As the resin, one having a high glass transition temperature and a small linear expansion coefficient may be selected as appropriate, and an epoxy resin is recommended. Since epoxy resin as a resin is required to be liquid and have low viscosity, compatibility with additives, curing agents and catalysts, and storage stability are also important characteristics that should be considered in selecting specific epoxy resins. . In consideration of such circumstances, epoxy resins such as bisphenol A type, bisphenol F type, and polyfunctional type can be used as the main agent, and aromatic polyamine type, carboxylic acid anhydride type, latent curing agent as the curing agent. A system type can be used. A typical example will be described below using a combination of a bisphenol A type epoxy resin and a solvent-free low-viscosity liquid aromatic amine curing agent.

  This resin may be another thermosetting resin such as a silicone resin, or may be cured without applying heat, such as a chemically reactive curable resin, an ultraviolet curable resin, or a photocurable resin. Resin may be used. Moreover, when it becomes press molding, the thermoplastic resin containing nylon, phenol, etc. which show the characteristic of a low viscosity at a certain pressure and temperature may be sufficient. Further, a base oil and a gelling agent having an appropriate melting point may be used. Of course, when a resin other than the thermosetting resin is used, a solidification or curing method that suits the resin may be employed.

  The magnetic powder constituting the admixture is preferably a soft magnetic powder, specifically, an Fe-based soft magnetic powder. More specifically, the Fe-based soft magnetic powder is preferably a powder selected from the group consisting of Fe-Si based powder, Fe-Si-Al based powder, Fe-Ni based powder, and Fe based amorphous powder. Here, as a particularly recommended composition range, the average Si content in the Fe—Si-based powder is preferably 11.0% by weight or less. The average Si content in the Fe—Si—Al-based powder is preferably 11.0% by weight or less, and the average Al content is preferably 7.0% by weight or less. Further, the average Ni content in the Fe—Ni-based powder is preferably 30.0 wt% or more and 85.0 wt% or less.

  In particular, it is desirable to use a substantially spherical powder as the magnetic powder used in the mixture. When a substantially spherical magnetic powder is used as the magnetic powder, the fluidity of the slurry-like admixture mixed with the resin increases, so that the filling rate of the magnetic powder in the admixture can be improved. Such a substantially spherical magnetic substance powder is obtained, for example, by a gas atomizing method. According to the gas atomization method, the particle size and shape of the magnetic powder have a certain degree of distribution, but as a guide, the average particle size D50 of the most standard magnetic powder (equivalent to 50% cumulative volume based on volume) (Indicating the diameter) is preferably 500 μm or less, and if it exceeds this, sufficient yield, characteristics and performance cannot be obtained. Further, a small particle size is desirable for filling the gaps in the molded body, and an average particle size D50 of about 100 μm is readily available, but a fine average particle size D50 of about 10 μm may be used.

  According to the gas atomization method, a non-spherical powder can be intentionally formed in addition to the substantially spherical powder as described above. Moreover, according to the water atomization method, an amorphous powder can also be obtained. In the present invention, non-spherical powder, amorphous powder, and other shapes of powder obtained by the above method can be used instead of the substantially spherical powder employed in the embodiment. The reason for employing a magnetic powder other than a substantially spherical shape is to use anisotropy due to its shape, for example. More specifically, for example, non-spherical, flat, or needle-shaped magnetic powder is mixed with a resin, and a predetermined magnetic field is applied before the resin is cured to perform anisotropic orientation of the powder group. The use method of hardening the resin after that can be considered.

  As a specific demonstration model, a method was adopted in which magnetic powder was mixed with a thermosetting epoxy resin to form a slurry and poured into a predetermined case under reduced pressure. In the slurry for the magnetic core used in this, a) optimization of the particle size of the magnetic material and b) selection of the non-magnetic powder were performed in order to obtain high filling and high superposition characteristics of the magnetic material powder. As the binder resin, a combination of a main agent and a curing agent and having a low viscosity (80 ° C., 70 mPas or less) was selected. That is, a composite magnetic material was produced by highly filling and uniformly dispersing magnetic powder in a low-viscosity epoxy.

  Conventionally, for example, in order to manufacture a wire-inner-type wire ring part having an outer volume of about 300 cc with Sendust green compact by press molding, a 1000-ton scale press facility is required. In the present invention, since several cc of the molded body is used and the casting method is selected, the cost of trial production and capital investment can be suppressed. As one means, we selected a method of filling and directly casting a product case or a separable case using a composite magnetic material having fluidity with a group of moldings. This method has sufficient advantages even if it is inferior in terms of the filling rate of magnetic powder compared with press molding, and as shown below, this method has a sufficient filling rate of composite magnetic The body can be obtained, and a wire-wrap type wire ring component with sufficient characteristics can be provided.

In the present invention, studies were conducted with the goal of finding a composite magnetic material that increases the magnetic permeability of the following magnetic field regions H1, H2, and H3.
H0 = 5A / m (Set the minimum magnetic field of the LCR meter to measure the initial permeability)
H1 = 15.92 kA / m
H2 = 31.84 kA / m
H3 = 79.6 kA / m

  The component of the magnetic core can be appropriately changed in the applied magnetic field used above. For example, in order to slightly increase the initial permeability, a high permeability thin film layer may be formed on the surface of the magnetic powder. Here, an example of the high magnetic permeability thin film is an Fe—Ni thin film. In order to avoid an electrical short circuit due to the magnetic powder, the magnetic powder may be coated with one or more insulating layers before being mixed with the resin. Here, when a high permeability thin film is formed on the surface of the magnetic powder, an insulating layer may be coated on the formed high permeability thin film.

  Furthermore, it is preferable to add a non-magnetic powder to the mixture of the magnetic powder and the resin in order to ensure a high relative permeability in a higher magnetic field. Non-magnetic powders include, for example, inorganic powders made of silica powder, alumina powder, titanium oxide powder, quartz glass powder, zirconium powder, calcium carbonate powder, aluminum hydroxide powder, glass fiber, and granular resin. Can be mentioned. Further, a hollow glass sphere may be used as the nonmagnetic powder. Further, in order to extend the direct current superposition characteristics well into a higher magnetic field, a small amount of permanent magnet powder may be added to apply a magnetic bias to the magnetic core.

  Next, the admixture, particularly the magnetic powder will be described in detail. As the magnetic powder, 6.5% Si—Fe powder having an average particle diameter D50 = 160 μm was used, and silane coupling treatment was performed. The amount of silane coupling at this time was set to the minimum amount that can be slurried with a solidifying resin described later. This is because a silane coupling agent that does not contribute to bonding causes a decrease in adhesive strength, glass transition temperature, and the like.

  Next, using a thermosetting low-viscosity epoxy resin, it is mixed and degassed to produce a slurry that is a base of a composite magnetic body having a temperature of 80 ° C. and a viscosity of 30 P (poise), an inner diameter of 15 mm, an outer diameter of 27 mm, and a high It was cast into an 11 mm thick silicone mold and then cured at 115 ° C. for 4 hours. After measuring the density of the toroidal core of the cured product, 23 turns were wound with a φ1.5 mm wire, and the direct current superposition characteristics were confirmed. The viscometer (HADV-I +, manufactured by Brookfield) was a screw head type (PC-1TL, manufactured by VISCOMETER).

  Here, the composition of the magnetic powder was 6.5% Si—Fe powder having the highest magnetostriction and the highest saturation magnetic flux density, but the difference in particle shape was examined using powders having different production methods. When water atomized powder, gas atomized powder and pulverized powder are compared as production methods, the gas atomized powder has the highest filling rate. Regarding the filling rate that can be made into a slurry, the filling rate of the pulverized powder was only 58.6 vol%, and the filling rate of the gas atomized powder having the same average particle diameter was 63.6 vol%. Since the gas atomized powder is spherical, in the case of the casting type, it was possible to increase the filling rate by using the spherical powder.

  Further, in order to investigate the relationship between the filling rate and the powder particle size distribution for the magnetic powder, the powder with an average particle diameter D50 of 160 μm increased by gas atomization is classified by a sieve having 150 μm and 75 μm openings, Two types of powders having a particle size of 150 to 75 μm were prepared. The cumulative frequency and frequency distribution of the mother powder used for this are shown in FIGS.

  In both powders with a particle size of 150 μm or more and powders with a particle size of 75 to 150 μm, the amount of resin added was increased and the filling rate was reduced to 60 vol%, but it became a high-viscosity paste and could be slurried. There wasn't. The reason for this is thought to be that narrowing the particle size distribution caused a decrease in the filling rate.

  As shown in FIG. 9, the mother powder has a D25 (cumulative frequency 25% equivalent diameter from the volume-based small diameter side) = 110 μm peak distribution and D75 (cumulative frequency 75% equivalent diameter from the volume-based small diameter side) = It can be considered as the distribution sum with the distribution of the 230 μm peak.

  FIG. 10 shows the relationship between the particle size ratio, the mixing ratio, and the filling rate in a large and small two-component particle mixed packed bed as an example of a true sphere packed model. FIG. 10 is data presented by Michitaka Suzuki: Himeji Institute of Technology, Powder and Particle Engineering Laboratory. When the large particles and the small particles are mixed and filled, the small particles enter the gaps between the large particles, so the gaps are reduced and the particles are packed densely. As shown in FIG. 10, the larger the particle diameter ratio, the larger the filling rate. Moreover, there is a peak in which the filling rate increases on the side where the mixing ratio of the small particle size powder is smaller as the particle size ratio is larger. Therefore, in order to obtain a high filling rate, it is effective to add a small amount of fine powder having greatly different particle sizes. In other words, it is effective to widen the particle size distribution. In the case of the above classified powder, it is considered that the particle size distribution was narrowed, which led to a decrease in the filling rate.

  In this case, the filling rate that can actually be made into a slurry is 63.6 vol%, which is less than the filling rate of about 74% that is expected when it is composed of only ideal primary spheres. Thus, it is considered that the fact is that the sphericity variation of the atomized powder and the width of the particle size distribution actually exist. In addition, since the surface of the magnetic powder surface is not smooth, agglomeration and bridges are likely to occur between a certain particle and a plurality of particles. In order to reduce the probability of occurrence, a low viscosity (low friction) is required in the process of uniform dispersion and molding.

  The present invention relates to a magnetic core for inductors such as choke coils and transformers used in electronic equipment up to several hundred kHz. As an example, it is determined whether or not there is a problem of eddy current loss of the inductor at the drive frequency f = 10 kHz. Here, the driving frequency f = 10 kHz of the product, the relative permeability μ of the powder composition μ = 1000, and the specific resistance ρ = 80 μΩcm of the powder composition bulk are used as constants.

When the skin depth δmm = (2 / (2πfμσ)) ^0.5 is calculated, the skin depth is 0.14 mm, and the corresponding particle diameter is 0.28 mm. The average particle diameter D50 of the currently used dust material is 0.16 mm, and the particle diameter D90 (equivalent diameter of 90% from the small diameter side on the volume basis) is about 0.28 mm. I think that the. Further, the frequency characteristic of μ does not decrease at 10 kHz, and the influence of the skin effect is sufficiently small, but the particle size of 280 μm or more may be affected. Thus, it is desirable that the maximum particle size of the magnetic powder is appropriately selected according to the drive frequency.

  Highly filled and highly superimposed magnetic cores can be obtained by adding secondary and tertiary particles of small diameter spheres. Here, the secondary and tertiary particles of the small-diameter sphere can be classified into a case where magnetic powder is used and a case where nonmagnetic powder is used.

  First, when using a second magnetic powder having a smaller diameter, that is, as an example of high packing only with magnetic powder, adding magnetic powders having different particle sizes as secondary particles and tertiary particles at various blending ratios. Tried. The particle size of the additive powder is a spherical powder with secondary particles D50 = 9.8 μm and tertiary particles D50 = 1.0 μm. All the powders used are substantially spherical. The result is shown in FIG. FIG. 11 shows the filling rate when secondary particles (D50 = 9.8 μm) and tertiary particles (D50 = 1.0 μm) are added to primary particles (D50 = 160 μm) at various blending ratios. is there.

  The particle size was selected with the aim of achieving an effect that the filled powder dispersed in the epoxy resin was rearranged to facilitate high filling. From FIG. 11, the change of the filling rate with respect to the added amount of secondary particles shows a tendency to have one maximum value in a small proportion of fine particles as shown in FIG. However, the effect of adding the tertiary particles tends to have two peaks. In the mixing experiment of the powder having a sharp particle size in FIG. 10, it is shown that the effect of improving the filling rate is more remarkable when the particle size ratio is larger, that is, by adding finer particles. It seems that the degree of this effect is different in the powder having a broad particle size actually used. However, as shown in FIG. 11, it can be seen that an admixture with a high filling rate can be obtained by adjusting the particle size distribution.

  The inductance and its direct quantity superposition characteristics were evaluated at three representative locations in the region shown in FIG. Table 2 shows the blending ratio and results of the magnetic powder. In this specification, the blending ratio of powders and the like is expressed in vol%. As a reference for the vol%, the mixture obtained by mixing and curing the powder and the resin is set to 100 vol%, and the volume percentage of each powder and the like is calculated. As shown.

  As a result of the three types of blending, the magnetic permeability was measured as Sample No. A in the A region. 1, μ (H0) = 43.4, μ (H1) = 22.4, sample No. 2 gave a value of μ (H2) = 18.9. That is, the composite magnetic material that can be further miniaturized by the magnetic fields H0 = 5 A / m and H1 = 15.92 kA / m is the A region, and the composite magnetic material that can be further miniaturized by the magnetic field H2 = 31.84 kA / m is the B region. It is obtained with.

  Sample No. B in the B region As shown in FIG. 3, the reachable packing ratio with only the primary particles (D50 = 160 μm) is 63.6 vol%. Next, in order to perform gap filling, the filling rate can be made 74.6 vol% by adding 11 vol% of secondary particles (D50 = 10 μm). Furthermore, secondary particles (D50 = 10 μm) and 14 vol% of tertiary particles (D50 = 10 μm) are added together with 13 vol%, so that the filling rate can be 78.6 vol%.

  As described above, the magnetic field H0 = 5 A / m, H1 = 15.92 kA / m, H2 = by using the second magnetic powder having a smaller diameter (secondary and tertiary particles made of a magnetic powder having a small sphere). The magnetic permeability of the magnetic core at 31.84 kA / m can be increased.

  Next, as another example capable of obtaining a magnetic core having high filling and high superposition characteristics, when using a non-magnetic powder having a smaller diameter, that is, using a non-magnetic powder as secondary and tertiary particles of a small sphere Is described. First, the first magnetic powder and nonmagnetic powder were selected. The nonmagnetic powder used was an inorganic powder such as silica or alumina whose particle size can be changed over a wide range.

  First, as the first magnetic substance powder, the same 6.5% Si—Fe powder having an average particle diameter D50 of 160 μm as described above was used and subjected to silane coupling treatment.

  Next, as an inorganic powder silica, the sintering powder is an agglomerated particle when viewed with an electron microscope SEM, and has a specific surface area of 7 times or more compared to the spherical powder, and the resin component is easily absorbed. It is thought that the component will decrease. For this reason, although the powder for sintering is low-cost, it is difficult to obtain the effect of improving the filling rate of the present application.

  Furthermore, three kinds of other spherical powder, roundish powder and pulverized powder were compared. These powders were added in 3, 5, and 10 vol%, respectively, and the first magnetic powder amount was adjusted so that the total amount with the magnetic powder was 60 vol%. As a result, both the roundish powder and the pulverized powder could not be slurried. Therefore, it can be seen that it is desirable to use spherical powder in order to obtain the effect of improving the filling rate.

The results using spherical silica powder are shown below.
Table 3 shows the results obtained by selecting spherical silica having an average particle diameter D50 = 2.5 μm as secondary particles and spherical silica having an average particle diameter D50 = 2.5 μm as secondary particles, and adding these selected silicas in combination. Shown in

  It was confirmed that the relative magnetic permeability μ changes depending on the particle size and the added amount of the fine powder. The permeability of the sample No. 4 gave a value of μ (H3) = 7.6.

  That is, the magnetic permeability at the magnetic field H0 = 5 A / m, H1 = 15.92 kA / m, and H2 = 31.84 kA / m after the addition is smaller than before the nonmagnetic powder addition (sample No. 3). Show. However, it can be seen that the magnetic field H3 = 79.6 kA / m exhibits a higher magnetic permeability.

  Furthermore, the sample No. As shown in FIG. 4, the secondary particles (D50 = 2.5 μm) are 5.5 vol% and the tertiary particles (D50 = 0.5 μm) are 5.5 vol% with respect to the primary particles (D50 = 160 μm). By adding them together, the filling rate can be 72.2 vol%.

  Sample No. B in the B region The result of examining the density distribution of the molded body of No. 3 will be described. In order to confirm the non-uniformity, the method and results of measuring the upper and lower density distribution of the cured product are shown. As a method, the slurry is cured in a syringe having a depth of about 45 mm and a diameter of 23 mm, and two portions of about 5 mm from the bottom and the surface of the cured product are cut into three cylinders. The weight of each cylinder, the average diameter, The average height was measured, and the average density of each cylinder was calculated from the weight and volume.

As a result, the density of the portion about 5 mm from the surface was low and the density of the portion about 5 mm from the bottom was high as described below.
a) A portion approximately 5 mm from the surface 5.17 g / cc (5% lower than the center ratio)
b) Center portion 5 to 37 mm portion 5.44 g / cc
c) About 5 mm from the bottom 5.71 g / cc (5% higher than the center)

  This phenomenon is caused by the particles being settled before the resin matrix of the admixture reaches heat curing, and the filling rate is locally improved, resulting in a heterogeneous structure of the magnetic core. This indicates that the direct current superimposition characteristic may be deteriorated. That is, from the results so far, it is considered essential to suppress precipitation of magnetic particles or non-magnetic particles in order to further improve the direct current superposition characteristics.

This will be discussed in more detail.
With respect to the target direct current superposition characteristics, it can be expected that the size of the micro gap formed between the individual particles varies depending on the location even if the filling rate of the magnetic powder is the same. FIG. 12 is a schematic view showing a dispersed state of the magnetic powder. A circle indicates a magnetic powder. In other words, if the magnetic powder (circles) as shown in FIG. 12 is uniformly dispersed, the average demagnetizing field should not be reduced, and a characteristic that is difficult to cause magnetic saturation should be obtained. is there. However, if the filling rate of magnetic powder (marked with ○) that indicates inappropriate is locally increased, the microgap between particles in such a place becomes smaller, resulting in a smaller demagnetizing field and a tendency to magnetic saturation. Become. Therefore, it is considered that eliminating such non-uniform distribution of the magnetic powder leads to higher characteristics. As one of the measures, it is considered effective to suppress the sedimentation of the magnetic powder that occurs during resin curing.

  As a measure for reducing the sedimentation rate of the particles, it is conceivable to increase the viscosity of the slurry. It is thought that it can be achieved simply by adding a thickener. However, since the casting method requires an operation of pouring the slurry into the mold, it is necessary that the viscosity is sufficiently lowered during the casting operation. Therefore, it is desirable to be able to utilize a property such as thixotropic in which the viscosity is reduced by applying shear or vibration. Therefore, a thixotropic agent is preferably used for uniform dispersion of the magnetic powder.

  Nano-sized fine particle anhydrous silica called nano silica is widely used in the adhesive industry as a highly active filler for increasing viscosity and imparting thixotropic properties. Silanol groups on the surface of nanosilica having a primary particle size of several nanometers are linked to the surface of the adjacent nanosilica by hydrogen bonding, form a three-dimensional network structure, and exhibit excellent viscosity. This hydrogen bond is a relatively weak bond, and by applying a slight shearing force (for example, vibration and stirring), the network structure is broken, broken up in units of chain-bonded particles, and loses viscosity. Due to this decrease in viscosity, good filling properties and rearrangement of fillers can be performed. On the other hand, in a stationary state, the mesh structure is regenerated, the viscosity is restored, and the sedimentation rate can be suppressed.

  These phenomena are called thixotropy phenomena and are important characteristics that improve the production and storage of magnetic slurries, as well as process capability and product properties.

  The thixotropic nature mainly depends on the resin used. For this reason, as a result of trying nano silica with different surface treatments, the most effective ones were those with a particle size of 4-7 nm and surface treatment with hydrophobic dimethyl silicone oil, which provided thixotropic properties. It was. The results using this nanosilica are shown in Table 4.

  As a result of three levels of nanosilica addition, nanosilica 0.27 vol%, and nanosilica 0.53 vol%, the permeability was 0.27 vol% of nanosilica and μ (H0) = 13.7, μ (H1) = 13 .Mu. (H2) = 12.0, nanosilica added at 0.58 vol%, a value of .mu. (H3) = 9.0 was obtained.

  That is, when the magnetic fields H0 = 5 A / m, H1 = 15.92 kA / m, and H2 = 31.84 kA / m, the composite magnetic material that can be made smaller is 0.27 vol% nanosilica (sample No. 5 in the A region). In addition, in the magnetic field H3 = 79.6 kA / m, the composite magnetic material that can be further miniaturized is one with 0.58 vol% nano silica added (sample No. 6 in the A region). In particular, the value of μ (H3) = 9.0 is the maximum value obtained by experiments in the magnetic field H3 = 79.6 kA / m.

  Thus, regarding the direct current superposition characteristics in the high magnetic field H3, the effect by adding nano silica is great. However, with respect to the filling rate, the presence or absence of the addition of nano silica is not so large. As shown in Table 3, the filling rate is 71.1 vol% with addition of 0.27 vol% of nanosilica and 68.4 vol% with addition of 0.58 vol% of nanosilica with respect to 72.2 vol% without addition of nanosilica. .

  As described above, the magnetic permeability of the magnetic field H3 = 79.6 kA / m can be increased by using non-magnetic powder (silica) as the secondary and tertiary particles of the small-diameter sphere and further using nano silica. That is, by adding nano silica, thixotropic properties are imparted, and the non-uniform distribution of the magnetic powder can be eliminated and the magnetic permeability can be improved by the sedimentation suppressing effect.

  When nanosilica is added, thixotropic properties are exhibited. Therefore, when casting is performed, it is preferable to perform casting while applying an appropriate stirring energy and vibrating. In principle, the hydrogen bond of nano silica is a relatively weak bond and loses its viscosity by applying a slight shearing force (for example, vibration, stirring).

  For this reason, the stirring conditions of the slurry were changed to 5 minutes, 15 minutes, and 20 minutes at a high speed stirring of 2000 rpm, which is considered to be the upper limit from the viewpoint of wear of the blades (diameter 50 mm) during mass production. As a result, it can be seen that Δμ / μ0, which is an index of DC current superposition characteristics, takes a substantially constant value for 15 minutes or more, and the stirring condition may be adopted for 15 minutes or more.

  The casting was performed in a vacuum of 2700 Pa after deaeration of the stirred slurry at 50 Pa. Moreover, casting was performed while applying 50 Hz vibration with a vibrator (av-02: manufactured by Murata Seiko Co., Ltd.). Stop vibration and release to atmosphere after casting. Immediately after that, it was cured by heat treatment in a stationary state.

  FIG. 13 shows a similar system of flow / viscosity curves of an epoxy resin whose thixotropy is improved by adding nano silica. This is the result of measuring the ease of flowing at 50 ° C. isothermally during curing of the epoxy resin. A Brookfield rotational viscometer rotating at 2.5 rpm and a vibrator as a shearing force source are used. From this result, it can be seen that it is necessary to cast while applying a shear rate for uniform rearrangement of magnetic powder. In this study, it can be seen that by setting the vibration frequency of the vibrator to 50 Hz, the viscosity is substantially minimized and the rearrangement of the particles is facilitated. In addition, the shear rate is quickly reduced to zero after the slurry magnetic body is filled. By doing in this way, the viscosity of the slurry magnetic body shows a maximum value, and the sedimentation speed can be minimized.

  In the present invention, using the above technique, a group of molded bodies having a high filling rate, such as a powder sintered body, and a high magnetic permeability are arranged in a casting container, and the mixture is poured. Therefore, it is possible to manufacture a magnetic core having a higher filling rate of the magnetic powder.

  The characteristic of the magnetic core in the Example of this invention product is shown. First, a wire ring part as shown in FIG. 1 was manufactured. 7. Using a mixture having a relative permeability μdc of 20 in a 96 kA / m magnetic field, a group of molded bodies having high permeability is placed in the magnetic core. Here, when a group of moldings having a relative permeability μdc of 30 in a 7.96 (kA / m) magnetic field is arranged over the entire magnetic core, the magnetic core of the present embodiment is in a 7.96 kA / m magnetic field. The relative magnetic permeability μdc increased from 20 to 28 for the admixture alone.

  Similarly, a group of high permeability moldings is placed in the magnetic core using an admixture having a relative permeability μdc of 20 in a 3.98 kA / m magnetic field. Here, when a group of molded bodies having a relative permeability μdc in a magnetic field of 3.98 kA / m of 70 is arranged over the entire magnetic core, the ratio of the magnetic core of the present embodiment in a magnetic field of 3.98 kA / m. The permeability μdc increased from 20 to 66 for the blend alone.

  Next, a wire ring part as shown in FIG. 2 was manufactured. 7. A group of high-permeability moldings is arranged in a part of the magnetic core using an admixture having a relative permeability μdc of 20 in a magnetic field of 7.96 kA / m. Here, when a group of molded bodies having a relative permeability μdc of 30 in a magnetic field of 7.96 kA / m is arranged in a columnar shape that is half the total magnetic core volume, 7.96 kA / m of the magnetic core of the present example. The relative permeability μdc in the magnetic field increased from 20 to 23 for the admixture alone.

  Similarly, a group of high magnetic permeability moldings is arranged in a part of the magnetic core using an admixture having a relative permeability μdc of 20 in a 3.98 kA / m magnetic field. Here, when a group of molded bodies having a relative permeability μdc of 70 in a 3.98 kA / m magnetic field is arranged in a columnar shape that is half the total magnetic core volume, the magnetic core of the present embodiment has a 3.98 kA / m. The relative permeability μdc in the magnetic field increased from 20 to 30 with the admixture alone.

  In this embodiment, simply selecting the shape of the casting container for filling the group of moldings and the mixture, the composite magnet has the required shape and high permeability even in a high magnetic field. A body core can be manufactured. The degree of freedom of shape during the production of this casting container is very large compared to press-molding molds. Manufacturable if necessary.

  Further, by inserting a specific permeability magnetic core member having a low permeability of about 1 to 10 in the magnetic path, the inductance of the wire ring component is less likely to be saturated to a higher magnetic field. Is possible. The resin used for the specific permeability magnetic core member in this case is desirably the same resin as the insulating resin used for the winding inclusion insulator. The specific permeability magnetic core member having a lower magnetic permeability is also preferably, for example, the same resin as the insulating resin used for the winding inclusion insulator, or the same resin mixed with a nonmagnetic filler. In addition, the high magnetic resistance member is, for example, a predetermined amount with respect to the same resin as the insulating resin used for the winding inclusion insulator (as a result, the magnetic resistance of the high magnetic resistance member is higher than the mixture). It may be formed of a mixture of magnetic powder.

  What is necessary is just to select the thing of a required magnetic permeability and a shape suitably for the specific magnetic permeability magnetic core member incorporated in a part of magnetic core according to the magnetic field to be used. Although any shape can be selected as the magnetic core shape, it goes without saying that a toroidal magnetic core shape having a uniform magnetic path is ideal in theory. Such a uniform magnetic path shape is advantageous in terms of reducing leakage magnetic flux and ensuring permeability.

  The wire ring component of the present invention is manufactured by placing a coil-containing insulator and a specific permeability magnetic core member in a mold, and casting and curing an admixture combined with a releasable resin to produce a magnetic core. Can be manufactured by removing the mold. Moreover, the wire ring component provided with the case can also be manufactured. By using part or all of the mold as a case, it is possible to manufacture without removing the mold. When the mold is not removed, it is not necessary to consider releasability, so that it is easy to manufacture a magnetic core having a complicated shape.

  Furthermore, a case that functions as a magnetic core may be used. For example, when a case functioning as a magnetic core is used as a common part with other parts, it is effective in a case where a winding part is once formed and then the winding part is placed in a case that is a common part. This case may be formed of other magnetic materials / alloys such as Fe-Ni alloys. When the case is made of a magnetic material, in order to ensure appropriate insulation performance, it is preferable to form an insulating film on the inner surface of the case and then cast the mixture to form a magnetic core. The case may be a ceramic case such as an alumina molded body, or may be made of an aluminum alloy.

  It is possible to provide a wire ring component that includes the case as described above and in which a winding inclusion insulator and a magnetic core made of the mixture fill a space between the case.

Explanatory drawing of the wire ring components of this invention. Explanatory drawing of the wire ring components of this invention. The manufacturing flow of the wire ring components of this invention. Relationship between the moisture content of the molded body group and the dielectric breakdown voltage. The relationship between the preheating temperature of the molded body group and the resin impregnation rate of the admixture. Relationship between filling rate of magnetic powder and thermal conductivity. Relationship between filling rate of magnetic powder and coefficient of linear expansion. Cumulative particle size distribution of mother powder based on volume. Frequency distribution of the volume-based particle size of the mother powder. The relationship between the particle size ratio, the mixing ratio, and the filling rate in the large and small two-component particle mixed packed bed. This figure is the data released by Michitaka Suzuki: Himeji Institute of Technology. Filling rate when secondary particles (D50 = 9.8 μm) and tertiary particles (D50 = 1.0 μm) are added to primary particles (D50 = 160 μm) in various mixing ratios. The schematic diagram which shows the dispersion state of a magnetic body powder. Similar to flow / viscosity curve of epoxy resin with improved thixotropy by adding nanosilica.

Explanation of symbols

1 Wire ring component 2 Molded body 3 Winding inclusion insulator 4 Admixture

Claims (9)

A winding inclusion insulator obtained by surrounding with an insulating resin so as to exclude the end of the winding; and a group of molded bodies having an initial permeability μdc = 10 or more filled at least inside the winding inclusion insulator; Embedded in the solidified or hardened mixture of the first magnetic powder and the second magnetic powder having a smaller diameter or the non-magnetic powder and the resin, and the first magnetic body The average particle diameter φ2 of the second magnetic powder or nonmagnetic powder is φ2 = <φ1 / 15 with respect to the average particle diameter φ1 of the powder, and the volume fraction of the second magnetic powder or nonmagnetic powder Is a wire ring part characterized by being 40 vol% or less of the whole .   In the admixture, the effective demagnetizing factor N of the first magnetic powder is 0.4 or less, and the total of the first magnetic powder and the second magnetic powder or non-magnetic powder. The wire ring component according to claim 1, wherein a filling rate is 50 vol% or more and a relative permeability μdc is 2 or more. Senwa component according to claim 1 or 2 less than half of the second magnetic powder or nonmagnetic powder is characterized in that it is a .phi.1 / 50 or less of the particle diameter of the powder. The wire ring component according to any one of claims 1 to 3 , wherein the resin or a mixture with the resin includes at least a thixotropic component. The winding encapsulated insulating material is impregnated with a mixture of the insulating resin and the insulating non-magnetic powder including at least the thixotropic component, in claim 4, characterized in that is obtained by solidifying or curing The wire ring component described. The powdered magnetic material, Senwa component according to any one of claims 1 to 5, characterized in that it consists of soft magnetic powder. The wire ring component according to any one of claims 1 to 5 , wherein the magnetic powder includes at least a soft magnetic powder. The wire ring component according to any one of claims 1 to 5 , wherein a specific magnetic permeability core member having a relative magnetic permeability μdc of 1 is embedded. The wire ring component according to any one of claims 1 to 8 , further comprising a holding case, wherein at least a part of the mixture is solidified or hardened in the case.

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