JPH0777167B2 - Magnetic core parts - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION [Industrial field of application] The present invention relates to a magnetic core component having little durability and excellent durability, such as a saturable reactor, a semiconductor circuit reactor, a common mode choke, a transformer, and a magnetic core for an electric motor. It is about.

[Prior Art] Generally, the above-described magnetic core component is required to have a small magnetostriction, a high effective magnetic permeability, and a high saturation magnetic flux density, and further, these magnetic characteristics do not change with time, It is necessary to have excellent durability.

In addition to the above characteristics, especially for saturable reactors used in magnetic amplification circuits, etc., the core loss is small,
It is also required that the controlled magnetization characteristics be good (the uncontrollable magnetic flux density is small).

In addition, the semiconductor circuit reactor prevents current spikes and current linking that occur when the semiconductor circuit is turned on and off, causing a current exceeding the specified value to flow into the semiconductor and destroying the semiconductor circuit, or preventing the semiconductor circuit from malfunctioning due to noise. In particular, the effective magnetic permeability is high, and a high squareness ratio is required to control only the above-mentioned abnormal current.

Further, particularly in the common mode choke, in order to prevent unipolar noise, it is necessary to increase the effective operating magnetic flux density, and it is required that the squareness ratio in the DC BH curve is small.

Further, in a unipolar voltage excitation transformer, since it is necessary to have a large operating magnetic flux density, the squareness ratio in the DC BH curve is low, and with the recent shift to a high frequency drive type switching power supply, high frequency characteristics It is required to be excellent (for example, small iron loss when driven at high frequency).

In recent years, Fe-based and Co-based amorphous alloys have attracted attention as materials having a high saturation magnetic flux density. Co-based amorphous alloys have the advantages of low magnetostriction and high effective magnetic permeability, and recently, as a magnetic core material for saturable reactors, JP-A-57-21061
No. 2 or Japanese Patent Laid-Open No. 21521/1982 discloses that a Co-based amorphous alloy is used. On the other hand, the Fe-based amorphous alloy has a higher saturation magnetic flux density than the Co-based amorphous alloy,
It is known that heat treatment in a non-oxidizing atmosphere, as described in Japanese Patent Publication No. 58-1183, has the advantage that high squareness DC magnetic characteristics can be obtained.

[Problems to be Solved by the Present Invention] As described above, the Fe-based amorphous alloy has an advantage that the saturation magnetic flux density is higher than that of the Co-based amorphous alloy. When a saturable reactor using a base-based amorphous alloy is used, especially when it is driven at a high frequency of 20 kHz or more, the core loss and controlled magnetization characteristics are inferior to the Co-based amorphous alloy, and the total controlled magnetization Since the force is large, there is a problem that the control magnetizing current for controlling the output voltage becomes large and a problem that the temperature rise of the magnetic core becomes large, which increases the load on the control circuit and reduces the efficiency.
In some cases, the durability of surrounding parts was reduced.

Further, when the reactor for a semiconductor circuit is made of an Fe-based amorphous alloy, the magnetostriction is remarkably large and the effective magnetic permeability is low, so that the effect of preventing spike current and the like is not sufficient.

In addition, the transformer of the switching power supply is conventionally mainly Mn-Z.
Although n-ferrite is used, an attempt to use an Fe-based amorphous alloy for a transformer of a switching power supply driven at high frequency is described in SI Tech. However, in this report, when Fe-based amorphous alloy is used, the magnetostriction is large and the characteristics tend to deteriorate due to mechanical stress. When the impregnated core or cut core is used, the high frequency magnetic characteristics deteriorate. Has been pointed out.

Therefore, it has low magnetostriction and high effective magnetic permeability comparable to Co-based amorphous alloys, and has the same saturation magnetic flux density as Fe-based amorphous alloys. There has been a demand for a material having excellent properties.

Also, as a magnetic core component whose magnetic characteristics do not change over time, Japanese Patent Application Laid-Open No. 62-101008 discloses that fine crystals of about 0.1 μm or less are amorphous and are dispersed uniformly in the mother phase, and the volume of the mother phase is small. It is disclosed that the above-mentioned solid crystalline material is used for at least a part of a magnetic circuit. However, the above-mentioned coagulated crystalline material is merely proposed as a material for improving only heat resistance, and it is not disclosed at all to improve the magnetic characteristics of conventional Fe-based and Co-based amorphous alloys. .

An object of the present invention is to improve the magnetic properties and durability of the above-mentioned amorphous alloys and coagulated alloys, to provide a magnetic core component having high saturation magnetic flux density and effective magnetic permeability and low loss.

[Means for Solving the Problems] In the present invention, Fe, Cu and M (where M is Nb, W, Ta, Zr, Hf, T
At least one element selected from the group consisting of i and Mo) is contained as an essential element, at least 50% of the structure is composed of fine crystal grains, and the effective magnetic permeability change rate X is 0.
A magnetic core component characterized by using a magnetic core having a size of 3 or less.

Here, the alloy used in the present invention is disclosed in Japanese Patent Application No. 62-3
It is a Fe-based ultrafine crystal alloy filed previously as 67187. This alloy has a compositional formula: (Fel-aMa) 100-x-yz-αCuxSiyBzM'α (where M is Co and / or Ni and M'is Nb, W, Ta, Z).
It is at least one element selected from the group consisting of r, Hf, Ti and Mo, and a, x, y, z and α are each 0 ≦ a ≦ 0.5,
0.1 ≦ x ≦ 3.0, 0 ≦ y ≦ 30, 0 ≦ z ≦ 25, 5 ≦ y + z ≦ 30 and 0.1 ≦ α ≦ 30 are satisfied. ), A Fe-based ultrafine crystal alloy having a composition represented by at least 50% of fine crystal grains, or a composition formula: (Fel-aMa) 100-xyz-α-β −γCuxSiyBzM ′
αM ″ βX (where M is Co and / or Ni and M ′ is Nb, W, Ta, Z
r, Hf, at least one element selected from the group consisting of Ti and Mo, M ″ is V, Cr, Mn, Al, a platinum element, Sc, Y, a rare earth element,
At least one element selected from the group consisting of Au, Zn, Sn and Re, X is at least one element selected from the group consisting of C, Ge, P, Ga, Sb, In, Be and As A, x, y, z, α, β and γ are 0 ≦ a ≦ 0.5, 0.1 ≦ x ≦ 3.0, 0 ≦ y ≦ 30,0 ≦, respectively.
z ≦ 25, 5 ≦ y + z ≦ 30, 0.1 ≦ α ≦ 30, β ≦ 10, γ ≦ 10 are satisfied. ) Is a Fe-based ultra-fine crystal alloy having a composition represented by at least 50% of the microstructure.

Here, Fe, Cu and M (where M is Nb, W, Ta, Zr, Hf, T
At least one element selected from the group consisting of i and Mo) is an essential element, and Cu and an element that suppresses crystal growth are considered to be elements that promote the formation of crystal nuclei and promote crystal growth. This is because a possible Fe-based ultrafine crystal alloy is obtained by the possible interaction of M. This microcrystalline alloy is microcrystalline by being heat-treated after being amorphized, and it is preferable that it contains an element that promotes amorphization, such as Si or B, in addition to the above essential elements.

Further, at least 50% or more of the structure is made fine crystal grains because the change with time becomes large when there are many amorphous parts, and it is more preferable to make the alloy structure to be substantially fine crystal grains. preferable.

Further, in the present invention, it is preferable that the saturation magnetic flux density (Bs) is 10 kG or more and the effective magnetic permeability (μelkHz) is 5 × 10 ³ or more.

The amount of change in effective magnetic permeability X with time is measured by putting data in a thermostatic chamber at 100 ° C in the atmosphere and conducting a 1000-hour test, and the effective magnetic permeability at 1 kHz before the test is μa, and the effective magnetic permeability at 1 kHz after the test is μb. The change rate X of the effective magnetic permeability was defined as follows.

X = 1-μb / μa The rate of change with time is preferably 0.3 or less. Also,
M in the composition formula is preferably Nb in terms of magnetic properties.

Further, in order to reduce the deterioration of the magnetic properties due to the internal stress generated when impregnating or coating these alloys with a resin, the saturation magnetostriction λs is preferably + 5 × 10 ⁻⁶ to −5 × 0 ^−6. . Particularly preferably + 1.5 × 10 ⁻⁶ to −1.5 ×
It is in the range of 10 ^-6 .

Saturable reactors, semiconductor circuit reactors, common mode chokes, normal mode chokes, high frequency transformers, excellent magnetic core parts such as magnetic cores for electric motors can be realized by using an Fe-based ultrafine crystal alloy having the above composition. .

In the present invention, when the magnetic core component is a saturable reactor or a semiconductor circuit reactor, in order to increase the control range for the former, and for the latter to prevent the voltage applied to the original circuit, only to prevent spike current. The squareness ratio Br / B10 in the DC BH curve is preferably 70% or more, more preferably the squareness ratio Br / B10 is 80.
% Or more (Br: residual magnetic flux density, magnetic flux density when a magnetic field of B10: 10Oe is applied).

Such a high squareness ratio characteristic can be obtained by heat treatment while applying a magnetic field in the magnetic path direction of the magnetic core.

For the saturable reactor, the uncontrollable magnetic flux density ΔBb at 50 kHz is preferably 3 KG or less so that voltage fluctuation does not occur especially when the load current becomes large.

By using the alloy having the above-described structure for the magnetic core for a reactor for a semiconductor circuit, excellent performance is exhibited in preventing spike current in the semiconductor circuit.

When used as a magnetic core for a common mode choke coil and a high frequency transformer, it is possible to increase the effective operating magnetic flux density, especially when a unipolar pulse voltage is applied.
It is particularly preferable that the squareness ratio Br / B10 in the −H curve is 30% or less.

In the manufacturing method, after the amorphous alloy is formed, the microcrystallization heat treatment is performed after the cutting, winding, etc., to form the magnetic core, and the alloy is brittle due to crystallization after the heat treatment. This is because the workability is significantly reduced and the workability is significantly reduced. By using such a manufacturing method, it is possible to punch a magnetic core for an electric motor having a complicated shape, for example. However, it is not always necessary to use this manufacturing method by a technique such as etching.

The heat treatment can be performed by holding the amorphous ribbon processed into a specific shape in a vacuum, in an atmosphere of an inert gas such as hydrogen, nitrogen, or Ar, or in the air for a certain period of time.

When the heat treatment is performed in a magnetic field, it is not necessary to continuously apply the magnetic field during the heat treatment, and sufficient effect can be obtained only by applying the magnetic field at a temperature lower than the Curie temperature Tc of the alloy.

In the case of the alloy of the above composition used in the present invention, the Curie temperature of the bccFe solid solution, which is the main phase, is considerably higher than the Curie temperature of the amorphous phase (usually 500 ° C. or higher). Even at a high temperature, if it is lower than the Curie temperature of the solid solution of bccFe, there is an effect of heat treatment in a magnetic field.

The heat treatment is usually carried out at a constant temperature, which is usually 450 ° C. to 700 ° C. and is preferably higher than the crystal starting temperature, and the holding time is preferably 5 minutes to 24 hours in mass production.

The conditions of temperature rise and cooling during the heat treatment can be arbitrarily changed depending on the situation. Further, it is also possible to perform the heat treatment at the same temperature or different temperatures a plurality of times, or to use a multi-step heat treatment pattern. Furthermore, a heat treatment in which the temperature is raised and then cooled without holding for a certain period of time can be applied.

As a method of applying a magnetic field, there are a method of winding a heat-resistant conductor around a magnetic core and passing a current, and a method of passing a conductor rod or plate through the magnetic core and passing a current through it. There is also a method of applying a magnetic field from the outside with an electromagnet, a permanent magnet, a solenoid coil, or the like. If necessary, heat treatment in a rotating magnetic field can be applied.

In this case, the heat treatment can be performed at the same time by increasing the frequency of the alternating current and by the heat generation effect of the core loss of the magnetic core. An arbitrary waveform such as a half-wave sine wave or a triangular wave can be used as the waveform of the current flowing through the conductor.

Further, the heat treatment can be performed under stress as necessary to adjust the magnetic characteristics.

The magnetic cores of saturable reactors, transformers, etc. according to the present invention include wound magnetic cores and laminated magnetic cores.

Further, it is preferable to form an insulating layer on a part or the whole surface of the alloy in order to reduce core loss. It goes without saying that this insulating layer may be on one side or both sides of the alloy thin plate.

As a method of forming this insulating layer, for example, a powder of SiO ₂ , MgO, Al ₂ O ₃ or the like is dipped, and is attached by a spray method or an electrophoresis method, or a film of SiO ₂ or the like is attached by a sputtering method or a vapor deposition method.
Alternatively, there is a method in which an acid is added to an alcohol solution containing a modified alkyl silicate, the solution is applied and dried, or a forsterite (MgSiO ₄ ) layer is formed by heat treatment. In addition, SiO ₂ -TiO ₂ metal alkoxide partial hydrolysis sol mixed with various ceramic powder raw materials is applied, a solution mainly composed of tyranopolymer is applied or heated after immersion, or a phosphate solution is applied. There is also a method of forming an insulating layer by post-heating.

It is also possible to form an oxide layer such as Si or a nitride layer on the surface by heat treatment, or form an insulating layer on the alloy surface by using an oxidizing agent or the like.

When forming a saturable reactor or the like with a wound magnetic core, the alloy ribbon and the insulating tape may be overlapped and wound to perform interlayer insulation.

As the insulating tape, polyimide tape, ceramic fiber insulating tape, polyester tape, aramid tape, glass fiber tape or the like can be used.

When a tape having excellent heat resistance is used, it can be heat-treated after being wound around an amorphous alloy ribbon having the same composition as the alloy ribbon and wound.

In the case of a laminated magnetic core, it is also possible to perform interlayer insulation by inserting an insulating material on a thin plate for each one or a plurality of layers of the alloy ribbon. In the case of laminated magnetic core, non-plastic material such as
Ceramic plates, glass plates, mica plates, etc. can be used. Also in this case, when an insulator having excellent heat resistance is used, heat treatment can be performed after inserting the insulator.

When the wound magnetic core is produced, it is preferable that the winding start portion or the winding end portion is fixed. This is because the shape of the wound magnetic core is not easily deformed during the heat treatment, and the handling after the heat treatment is easy.

This fixing method includes a method of locally melting and joining by laser light irradiation or electric energy, and a method of fixing with a heat-resistant adhesive or tape.

The present invention, for example, when used as a saturable reactor,
It may be formed as a combined magnetic core, for example, by stacking a plurality of magnetic cores, or may be formed in combination with another magnetic core.

The magnetic core of the present invention is coated or coated on the surface of the thin ribbon to be used to improve the corrosion resistance, but in general, it is put in a bobbin or a case that rings from an insulator or coated around the magnetic core. To prevent deterioration of characteristics due to rust, damage, and insulation from windings, by filling the magnetic core with silicon oil, impregnating or coating with silicon resin, and filling the case with an alloy such as grease and a substance that blocks the outside air To do. Further, since the alloy used in the present invention is Fe-based, it is an effective means to improve durability, in particular to shut off the alloy and the outside air to prevent the generation of rust.

[Examples] Examples of the present invention will be described in detail below, but the present invention is not limited to these examples.

Example 1 From a molten alloy containing Cu1, Nb2.5, Si13.5, B7.2 and the balance substantially Fe in atomic%, a width of 4.5 mm and a thickness of 18 were obtained by a single roll method.
A μm ribbon was created. The result of the X-ray diffraction analysis of this ribbon is shown in FIG. This shows a halo pattern peculiar to an amorphous alloy, and it was confirmed that this ribbon was amorphous. This ribbon has an outer diameter of 13 mm and an inner diameter of 1
The wound magnetic core shown in FIG.

Then, a microcrystallization heat treatment was performed at 550 ° C. for 1 hour.

This magnetic core was put into a phenol resin core case, and 10 turns of winding were applied to both the primary side and the secondary side. This magnetic core part was placed in a constant temperature bath at 100 ° C. and the change with time of the effective magnetic permeability was measured. The results are shown in Fig. 1. As a comparative example, the same method was used to prepare an amorphous alloy consisting of Fe0.4, Mn5.9, Si15, B9 in atomic% and the balance consisting essentially of Co, and an amorphous alloy having the same composition as the present invention without heat treatment for microcrystallization. The changes over time of the formed magnetic core parts are also shown.

From FIG. 1, the effective magnetic permeability of the magnetic core component of the present invention was hardly deteriorated, and the above-mentioned change rate X with time was 0.02. on the other hand,
The Co-based alloy of Comparative Example had a severe change with time of 0.73. Further, in the case of an alloy having the same composition as the present invention, 0.
The effective permeability was only 7,000, which was much smaller than that of the magnetic core component of the present invention. Therefore, it was found that the magnetic core component of the present invention has little change over time and is excellent in durability.

This magnetic core was disassembled and the structure of the alloy was analyzed. As a result, the X-ray diffraction pattern shown in Fig. 3 (a) and the schematic diagram observed with a transmission electron microscope in Fig. 3 (b) showed that the superstructure consisting of bccFe solid solution of 50 to 200 Å It was found that it has a fine grain structure and that these grains are uniformly distributed.

It is considered that the periphery of this crystal grain is amorphous,
When the heat treatment temperature is high, it is presumed to be in the crystalline phase.

Example 2 FIG. 6 shows a controlled magnetization characteristic measuring circuit, which is a measuring circuit used for evaluating a saturable reactor. FIG. 7 is an operation schematic diagram of the saturable reactor when an arbitrary direct-current control current Ic is flowing in the control circuit.

In FIG. 6, the sample S is a saturable reactor composed of three types of windings N _L , Nc, and Nv and a magnetic core.

Nl corresponds to the output winding of the saturable reactor used as the magnetic amplifier, and is connected to the AC power source Eg having the frequency f (cycle Tp) via the resistor RL and the rectifier D. The value of Eg is set to a large value such that the magnetic core reaches saturation at a phase angle within 90 ° of the sine wave voltage of the applied voltage in the gate half cycle Tg.

Nc is a control winding, which is connected to a DC power source Ec through an inductance Lc having a sufficiently large value compared with the magnetic core inductance seen from the control circuit, and gives a DC magnetomotive force of a restricted magnetizing condition. Nv is a winding for measuring the reset magnetic flux amount Δφcm corresponding to the control input, and is connected to the average value rectification type AC voltmeter V.

FIG. 8 shows a schematic diagram of a control magnetization curve obtained by measuring with this measurement circuit.

If β ₀ is the reciprocal of the total control magnetizing force Hr, β ₀ = 1 / Hr As a saturable reactor, the larger β ₀ (smaller Hr), the smaller the control current and the better the characteristics.

On the other hand, if the parameter indicating the degree of squareness of the magnetization characteristics of the magnetic core is set to α ₀ , β ₀ = 1−ΔBb / ΔBm As a saturable reactor, the larger the α ₀ is, the smaller the uncontrollable magnetic flux density ΔBb is. It will be good.

The product of α ₀ and β ₀ is represented by G _0, which is called Specific Core Gain. It can be determined that the larger G ₀ = α ₀ · β ₀ , the better the magnetic core for a saturable reactor as a whole.

In addition, the maximum value of the gate magnetic field H _L m = {N _L · i _L (max)} / le (1) le: The maximum value B m of the magnetic flux density corresponding to the average magnetic path length in the data and the control magnetic field H = (Nc ・ Ic) / le (2) The magnetic flux density, which is the difference from the magnetic flux density Bc determined by (2), is ΔBcm.
And the frequency is f, the reading of the magnetic flux voltage type V of the Nv circuit is Ev = f · Nv · A · ΔBcm (3) A: Effective area of the magnetic core In the actual saturable reactor, the magnetic field H is Characteristic H _L m-ΔBb characteristic in the positive region and characteristic H lm-Δ in the region where the magnetic field H is negative
It is necessary to understand the Bb characteristics.

ΔBb = Bm−Br (4) and Evd = f · Nv · A · ΔBcm (5) On the other hand, ΔB = ΔBcm−ΔBb (6).

As the saturable reactor, the curve in the first quadrant shown in FIG. 8 is on the lower side, and the curve in the second quadrant is on the right side,
And the steeper the slope, the better.

Example 3 From a molten metal having a composition of Cu1%, Si13.5%, B9%, Nb3% and the balance Fe in atomic%, a width of 4.5 mm and a thickness of 18 μ were measured by a single roll method.
m ribbon was created. This ribbon was almost completely amorphous. Wrap this ribbon around the outer diameter of 13 mm and the inner diameter of 10 mm,
A wound core was created. The crystallization temperature of this alloy is 508 ℃ when measured at a heating rate of 10 ℃ / min, and the Curie temperature is about 310 ℃.
Met.

Next, heat treatment in a magnetic field was performed according to various heat treatment patterns shown in FIG. When applying a magnetic field, in the magnetic path direction of the magnetic core
Applied 10 Oe. It was confirmed that most of the structure of the alloy after heat treatment consisted of 100-200 Å crystal grains consisting of Fe solid solution of bcc structure.

This magnetic core was put in a phenolic core case, and winding was performed for 10 turns on both the primary side and the secondary side in the same manner as in Example 1, and the characteristics as a saturable reactor were tested. Table 1 shows the magnetic characteristics of the prepared magnetic core.

As shown in Table 1, the heat treatment patterns shown in FIG. 4 provide high squareness characteristics, and the core loss W2 / 100k at 2kG and 100kHz is the core of Co-based amorphous alloy (W2 / 100k =
200-900). The magnetic flux density B10 (≈ Bs) at 10 Oe was 12.4 kG, which was considerably higher than that of a magnetic core made of Co-based amorphous alloy, 80% Ni permalloy, etc.

The Curie temperature Tc of the heat-treated alloy shown in FIG. 4B was 570 ° C., and the saturation magnetostriction λs was 3.8 × 10 ⁻⁶ .

Example 4 Cu1%, Si13.5%, B9%, N5% and the balance substantially Fe in atomic%
5 mm wide and thick by the single roll method from the molten metal composed of
An 18 μm ribbon was created. The crystallization temperature of this alloy is
It was 533 ° C when measured at 10 ° C / min. The Curie temperature was 260 ° C.

Next, MgO powder was applied to the surface of this ribbon by an electrophoresis method, and the ribbon was wound around an outer diameter of 19 mm and an inner diameter of 15 mm to form a wound magnetic core.

Next, the wound magnetic core was placed in an N ₂ gas atmosphere furnace kept at 610 ° C. and held for 1 hour, and then cooled to 250 ° C. at a cooling rate of 5 ° C./min while applying a magnetic field of 5 Oe in the magnetic path direction of the magnetic core. Then 4
After holding for a period of time, it was cooled to room temperature at a cooling rate of about 60 ° C./min.

After holding the same wound magnetic core at 610 ° C. for 1 hour, it was cooled to room temperature at a cooling rate of 100 ° C./min while applying a magnetic field of 5 Oe in the magnetic path direction of the magnetic core.

These magnetic cores were put in a phenol resin core case, and windings of 10 turns were made on both the primary side and the secondary side in the same manner as in Example 1 to test the characteristics as a saturable reactor. The obtained magnetic characteristics are shown in Table 2 (a) and (b), respectively.

As can be seen from Table 2, these have a high squareness ratio and are suitable as a saturable reactor. The Curie temperature of the main phase of the alloy heat-treated according to the pattern (b) in Table 2 was 550 ° C., and the saturation magnetostriction λs was 1 × 10 ₋₆ .

Further, the alloy structure was occupied by ultrafine crystals in the same manner as in Example 1.

Example 5 FIG. 9 shows a magnetic core used in the saturable reactor of the present invention, a magnetic core used in a saturable reactor of a conventional high squareness ratio Fe-based amorphous alloy, and a saturable reactor of a high squareness ratio Co-based amorphous alloy. An example of the frequency dependence of the core loss of the magnetic core was shown.

Among the alloys used in the saturable reactor of the present invention, Fe73.5Cu
The 1Nb3Si13.5B9 alloy (type 1) was heat-treated by holding it at 550 ° C for 1 hour and then holding it at 280 ° C for 1 hour while applying a 2Oe magnetic field in the magnetic path direction. Fe71.5Cu1Nb5Si13.5B9
The alloy (type 2) was heat-treated by holding it at 610 ° C for 1 hour while applying a magnetic field of 15 Oe in the magnetic path direction, further holding it at 250 ° C for 2 hours, and then cooling it. Fe71.5Cu1Nb5Si13.5B9 alloy (type 3) Is heat-treated by holding at 610 ° C. for 1 hour and then air-cooling while applying a magnetic field of 2 Oe in the magnetic path direction.

The magnetic core used for the saturable reactor of the present invention has a core loss equal to or less than that of the conventional high-square-ratio Co-based amorphous alloy, and is suitable as the saturable reactor. In addition, the core loss was less than half that of the conventional high-square-ratio Fe-based amorphous alloy.

Example 6 The evaluation circuit of FIG. 6 showing the saturable reactor of the present invention using the alloy shown in FIG. 9 of Example 5 and the saturable reactor of the conventional high squareness ratio Co-based amorphous alloy shown in FIG. The controlled magnetization characteristics were evaluated by. The winding at this time is the primary side (N
v) and the secondary winding (Nl) have 17 turns each and the control winding (Nc) has 5 turns. The results are shown in Fig. 10.

The control magnetizing force of the saturable reactor of the present invention for the same ΔB is almost the same as that of the high-square-ratio Co-based amorphous alloy, but the total controlled magnetic flux density ΔBm of the saturable reactor of the Co-based amorphous alloy is the same. It can be seen that the saturable reactor can be miniaturized under the condition that the temperature rise of the magnetic core is not so problematic because it is 1.5 to 2 times larger and can be made large.

Example 7 Fig. 11 shows Cu1%, Si13.5%, B9%, Nb3% and balance F in atomic%.
The temperature characteristics of the saturable reactor according to the present invention using the microcrystalline alloy of e are shown.

Squareness ratio Br / B10, core loss, coercive force Hc from room temperature to 150
Almost no change in the range of ° C. It was also found that B10 is a saturable reactor with excellent durability and practically no problem as it only drops about 1 kG from room temperature at 150 ° C.

Example 8 A width of 5 m was obtained from a molten alloy having the composition shown in Table 3 by the single roll method.
An amorphous ribbon having a thickness of m and a thickness of 18 μm was prepared. Next, this ribbon was wound around an outer diameter of 19 mm and an inner diameter of 15 mm to form a wound magnetic core.
The wound magnetic core was heat-treated to have a structure composed of ultrafine crystal grains.

The magnetic core was put in a phenol resin case, and windings of 10 turns were made on both the primary side and the secondary side in the same manner as in Example 1 to test the characteristics as a saturable reactor. DC B- at this time
H curve, AC B-H curve, core loss W2 / 100k at 100 kHz, 2 kG, and 50 KH when a saturable reactor similar to that in Example 6 was prepared by the method shown in Example 2.
The controlled magnetization curve at z was measured.

Magnetic flux density B10, DC when a magnetic field of 10 Oe is applied Squareness ratio of B-H curve Br / B10, Hc (DC), AC squareness ratio of AC BH curve at 20kHz Br / B1 (AC), Hc (AC), W2 / 10
Table 3 shows 0k, total control magnetizing force Hr, and uncontrollable magnetic flux density ΔBb.

In the saturable reactor of the present invention, when B10 is a Co-based amorphous alloy, it is higher than in the case of 80 wt% Ni permalloy and has a high squareness ratio, Hc, core loss, Hr, ΔBb is a Co-based amorphous alloy. It has been found that it exhibits excellent characteristics comparable to

Moreover, compared with the case of 50 wt% Ni permalloy or Fe-based amorphous alloy, the loss is low, the Hr is small, and the controlled magnetization characteristics are excellent.

From this, it was found that the control current can be reduced and the efficiency of the circuit can be increased. It was also found that the control range is sufficiently wide because ΔBb is small.

Example 9 A wound magnetic core having an ultrafine grain structure was prepared in the same manner as in Example 8 from the molten alloy having the composition shown in Table 4, and the characteristics as a saturable reactor were tested. this Magnetic flux density at 10 Oe of saturable reactor B10,100kHz, 2
The core loss W2 / 100k in kG, the uncontrollable magnetic flux density ΔBb, and the saturation magnetostriction λs were measured. The results obtained are shown in Table 4.

The saturable reactor of the present invention has a higher squareness ratio, lower Hc, lower core loss, and uncontrollable magnetic flux density Δ than those of Fe-based amorphous alloys.
Bb is small. It was also found that the deterioration of characteristics due to coating or the like can be prevented because λs is small.

Example 10 Amorphous alloy ribbon composed of Cu1%, Si13.5%, B9%, Nb3% and balance Fe in atomic% and Si13.5%, B in atomic% as a comparative example
An amorphous alloy ribbon consisting of 9%, Nb3% and balance Fe was prepared.

The crystallization temperature of the former amorphous alloy containing Cu-Nb is 508 ° C. when measured at a temperature rising rate of 10 ° C./min,
The amorphous alloy of the comparative example had a temperature of 583 ° C.

These amorphous alloys were wound to form a wound magnetic core having an outer diameter of 19 mm and an inner diameter of 15 mm.

The magnetic core containing Cu-Nb used in the present invention was held at 550 ° C. for 1 hour while applying a magnetic field of 10 Oe in the magnetic path direction, and then kept at 20 ° C.
After cooling to room temperature at a cooling rate of / min, a magnetic core was obtained in which the ultrafine crystal grains occupied most of the structure.

On the other hand, the magnetic core of the comparative example was held at 500 ° C for 1 hour,
While applying a magnetic field of 0 Oe, it was cooled to 280 ° C at a cooling rate of 5 ° C / min, kept at 280 ° C for 4 hours, and then cooled to room temperature at a cooling rate of 20 ° C / min. The structure of the magnetic core of the comparative example was in an amorphous state. These magnetic cores were put in a core case made of phenol resin, and a saturable reactor having 20 windings on both the primary side and the secondary side and 5 turns of the control winding was prepared.

These saturable reactors drive frequency 100kHz, output 12V
The output charge characteristics were measured by mounting it on a magnetically controlled switching power supply of 4A (mag amp control) and 5V12A (PWM control). Input voltage was AC100V, 5V output was 12A constant, 12V load current was changed, and 12V output terminal voltage, power supply efficiency η, and core case surface temperature rise ΔT were compared.

The obtained results are shown in FIG.

In the case of the saturable reactor of the present invention, it was possible to obtain the one in which the temperature rise was smaller than that of the comparative example, the power supply efficiency η was high, and the output voltage hardly changed.

Example 11 A molten metal having a composition of Cu 0.8%, Si 13.6%, B 9%, Nb 3%, and balance Fe at atomic% and Cu 1%, Si 13.5%, B 9 at atomic%.
%, Nb5%, and the balance consisting essentially of Fe, an amorphous alloy was prepared by the single roll method. These were annealed in a magnetic field while applying a magnetic field of 10 Oe in the magnetic path direction in an N ₂ gas atmosphere.

The former was for holding at 550 ° C for 1 hour and then at 280 ° C for 1 hour, and the latter was for holding at 610 ° C for 1 hour and then at 250 ° C for 4 hours. The magnetic field was continuously applied during the heat treatment.

This heat treatment made it possible to obtain a structure having ultrafine crystal grains.

Next, put them in a bake core case, and
The secondary side was wound with 10 turns and tested for its characteristics as a saturable reactor.

The results of measuring these DC BH curves are shown in FIG. As a comparative example, there is shown a DC BH curve of a saturable reactor constituted in the same manner as the present invention by using an amorphous alloy composed of atomic%, Si15%, B9%, Mn5.9% and the balance substantially Co. In the case of the present invention, compared to the case of the Co-based amorphous alloy of the comparative example
B10 was high, coercive force Hc, and squareness ratio Br / B10 were almost the same. The maximum permeability μm was 1.45 × 10 ^{6 in} the case of Fe73.6Cu0.8Si13.6B9Nb3 alloy and 1.00 × 10 ⁶ in the case of Fe71.5Cu1Si13.5B9Nb5 alloy.

Example 12 Fe72.5-XCuXSi13.5B9Nb3 alloy molten metal and Fe7 as a comparative example
Amorphous alloy ribbons were prepared from the 7.5-XCuXSi13.5B9 alloy melt by the single roll method.

Next, these ribbons were wound around an outer diameter of 19 mm and an inner diameter of 15 mm to produce a magnetic core. This magnetic core is oriented in the magnetic path in an N ₂ gas atmosphere.
While applying a magnetic field of 20 Oe, other conditions were the same as the heat treatment pattern (b) of FIG. This magnetic core was placed in a phenol resin core case, and windings of 10 turns were made on both the primary side and the secondary side to make a saturable reactor, and the control magnetization characteristics were measured by the circuit shown in Example 2.

Figure 14 shows the results of measuring the Specific Core Gain G ₀ at 50kHz.

It was found that when X exceeds 0.1, G ₀ remarkably increases, but when X exceeds 3, ₀ decreases, which is not preferable.

Further, when Nb is not added, G ₀ is not so much improved by the addition of Cu. From this, it was found that the combined addition of Cu and Nb is very effective in improving the controlled magnetization characteristics of the saturable reactor.

Example 13 Fe76.5-αCu1Si15.5B7Nbα molten alloy and F as a comparative example
Amorphous alloy ribbons were prepared from the melted e77.5-αSi15.5B7Nbα alloy by the single roll method.

Next, these ribbons were wound around an outer diameter of 19 mm and an inner diameter of 15 mm to produce a magnetic core. This magnetic core is oriented in the magnetic path in an N ₂ gas atmosphere.
While applying a magnetic field of 20 Oe, heat treatment was performed under the other conditions in the same manner as the heat treatment pattern (b) of FIG. 4, and a saturable reactor was created in the same manner as in Example 12, and then at 50 kHz.
Core Gain G ₀ was measured. The obtained results are shown in FIG.

It was confirmed that the saturable reactor of the present invention has a remarkably larger G ₀ than the comparative example, and that the combined addition of Cu and Nb is very effective in improving the controlled magnetization characteristics.

Example 14 Cu1%, Si13.5%, B9%, Nb3% and the balance substantially F at atomic%
A ribbon having a width of 3 mm and a thickness of 18 μm was prepared from a molten metal having a composition of e by a single roll method. This ribbon was heat-treated in Example 3 as shown in FIG.

Next, put this magnetic core in a case made of phenol resin and 0.4 mm
The φ winding was wound about 20 turns to produce the semiconductor circuit reactor shown in FIG. The 1kHz inductance of this reactor was measured. The ratio of the maximum inductance to the initial inductance was 3.03, and the ratio of the maximum inductance to the residual inductance (the residual inductance is the inductance when DC is superimposed) was 300.

Since the ratio between the maximum inductance and the residual inductance is large, excellent characteristics were obtained for improving the recovery characteristics of the diode.

FIG. 17 shows a basic circuit example of a switching power supply using the semiconductor circuit reactor. Fig. 18 shows pulse width
FIG. 7 shows load current waveforms with and without the above reactor inserted in a half-wave rectifier circuit at 10 μs, input voltage 100 V, DC, and by using the semiconductor circuit reactor of the present invention, current spikes are significantly reduced. I knew I could do it.

Example 15 Cu1% at atomic%, Si13.5%, B7%, Nb2.5% and the balance substantially 3% by a single roll method from a molten metal having a composition consisting of Fe,
An amorphous alloy ribbon having a thickness of 18 μm was prepared.

Next, on the contact surface side of this alloy ribbon with the single roll described above,
After applying MgO powder to form an insulating layer, outer diameter 4 mm, inner diameter 2 m
It was wound around m and used as a toroidal magnetic core. This magnetic core is 1 at 550 ℃
After heat treatment for a time, the outer surface of the magnetic core was coated with epoxy resin, and the magnetic core prepared at the terminals of the diode was inserted as shown in FIG. 19 to prepare a semiconductor circuit reactor combined with the diode.

Next, this reactor was used for the smoothing circuit on the output side of the switching power supply, and the diode voltage and the output noise were measured.

Without using the reactor of the present invention, the diode voltage is
61.0V, the output noise was 123mVp-p, but by using the reactor of the present invention, the diode voltage is
It was confirmed that the reduction effect was remarkably excellent at 33.5 V and the output noise was 47.3 mVp-p.

Example 16 A reactor of the present invention using a magnetic core made of an alloy ribbon having the composition shown in Table 5 was prepared in the same manner as in Example 14, and the initial inductance L0 and the maximum inductance Lm were measured.
Initial inductance L0 ¹⁰⁰⁰ after holding at 120 ℃ for 1000 hours,
The maximum inductance Lm ¹⁰⁰⁰ was measured and the ratio L0 ¹⁰⁰⁰ / L0 and Lm ¹⁰⁰⁰ / Lm of the value at 0 hour and the value at 1000 hours were obtained. The results obtained It is shown in Table 5.

As can be seen from Table 5, the time-dependent change in inductance of the semiconductor circuit reactor of the present invention was significantly smaller than that of the conventional reactor using a Co-based amorphous alloy.

Example 17 Cu1%, Si14%, B8%, Nb5% and the balance substantially Fe in atomic%
An amorphous alloy ribbon with a width of 5 mm, a maximum plate thickness of 20 μm, and an average plate thickness of 17 μm was made from a molten metal having a composition of, and wound in a toroidal shape with an inner diameter of 6 mm 20 times and then in an Ar gas atmosphere. A magnetic core having a structure similar to that of Example 1 was prepared by performing a heat treatment of holding at 600 ° C. for 1 hour and air cooling.

A winding for 20 turns was applied to this magnetic core to create a semiconductor circuit reactor.

The power supply efficiency was obtained by inserting this semiconductor circuit reactor in series with the diode of the switching power supply. The power efficiency at this time was 80%. The temperature rise of this reactor was 15 ° C. On the other hand, the power supply efficiency when using a similar reactor made of Fe-Si-B type Fe-based amorphous alloy is
77%, and the reactor of the present invention had higher efficiency.

Example 18 A molten alloy having the composition shown in Table 6 was rapidly cooled by a single roll method to obtain an amorphous alloy. This amorphous alloy is wound to an outer diameter of 35
A wound magnetic core having an inner diameter of 25 mm and an inner diameter of 25 mm was prepared. This wound magnetic core was heat-treated at a temperature above the crystallization temperature while applying a magnetic field of 5000 Oe in the direction perpendicular to the magnetic path to prepare a magnetic core having a structure having ultrafine crystal grains.

As shown in Fig. 20, two 10-turn windings were formed on this magnetic core to form a common mode choke. DC magnetic characteristics of this common mode choke, core loss at 2kG, 100kHz W2 / 100k, absolute value of complex permeability at 100kHz ||
The effective pulse permeability μp and the saturation magnetostriction λs were measured when ΔB was 4 kG with a pulse width of 100 k and 10 μs. The results obtained are shown in Table 6.

DC magnetic characteristics are comparable to Fe-based amorphous alloys, and || 100k is C
It was found that a large common mode noise attenuation effect can be expected in the frequency band around 100 kHz, which is comparable to the o-based amorphous alloy and requires the most noise suppression.

It was also found that the core loss at 2kG100kHz was smaller than that of the Fe-based amorphous alloy. The saturation magnetostriction could be made as small as that of Co-based amorphous alloy.

Example 19 Cu1%, Si16.5%, B6%, Nb3% and the balance substantially F in atomic%
Width 7.5 mm from the molten metal composed of e by the single roll method,
An 18 mm thick amorphous alloy was prepared.

This amorphous alloy was wound to form a wound magnetic core having an outer diameter of 19.5 mm and an inner diameter of 9.6 mm. This magnetic core was heat-treated in a N ₂ atmosphere while applying a magnetic field of 3000 Oe in the direction perpendicular to the magnetic path. In this heat treatment, the temperature was raised at a temperature rising rate of 10 ° C./min, held at 510 ° C. for 1 hour, and then cooled to room temperature at a cooling rate of 2.5 ° C./min.

Put this magnetic core in a phenol resin core case and
We made a common mode choke with two 10-turn windings as shown in the figure.

As a result of measuring the magnetic characteristics at this time, B10 = 12 kG, Br / B10 =
14%, Hc = 0.018 Oe, μe1k = 28000, || 100K = 22000, B1 =
It was 11.5KG.

Next, this common mode choke was used for the line filter of the AC100V input line of the switching power supply driven at 50kHz. Fig. 21 shows the measurement result of the common mode noise leaking from the power input terminal at this time.

From this figure, it is understood that the line filter using the common mode choke of the present invention has a lower noise level especially on the low frequency side and has a greater effect of reducing noise than the case of using the ferrite magnetic core.

Example 20 Cu1%, Si13.5%, B9%, Nb3% and the balance substantially F at atomic%
An amorphous alloy was prepared by a single roll method from a melt having a composition of e.

This amorphous alloy was wound to form a wound magnetic core having an outer diameter of 31 mm and an inner diameter of 18 mm. This magnetic core was heat-treated in an N ₂ atmosphere while applying a magnetic field of 5000 Oe in the direction perpendicular to the magnetic path, and a structure having ultrafine crystal grains was obtained.

The magnetic core was put in a bake core case, and windings of 10 turns were made on both the primary side and the secondary side, and the magnetic characteristics were measured.

At this time, the DC BH curve and the pulse permeability μp were measured. The results are shown in FIGS. 23 (a) and (b), respectively. As a comparative example, the case of Mn-Zn ferrite and a Co-based amorphous alloy is additionally shown. In the case of the present invention, the saturation magnetic flux density is high, the magnetic permeability is high at a low squareness ratio, and the constant magnetic permeability is excellent,
Since the core loss is low, it was found that the dependency of the effective pulse permeability on the operating magnetic flux density variation ΔB was superior to that of the alloy of the comparative example. As a result, when used as a common mode choke, the magnetic core is less likely to be saturated by high-voltage pulse noise and high inductance can be maintained, so that a line filter excellent in high-voltage pulse attenuation characteristics can be created.

FIG. 24 shows the result of measuring the frequency characteristic of the absolute value || of the complex permeability of this magnetic core. A large || means that the ordinary noise has a large attenuation efficiency.

It has been found that in the case of the magnetic core of the present invention, || exhibits excellent characteristics equal to or higher than those in the case of using the Co-based amorphous alloy.

Further, from this fact, when used as a transformer magnetic core, the exciting current of the transformer can be reduced, and the magnetic core is less likely to be saturated even when operated at a high ΔB, and when the temperature rise does not cause a problem, the magnetic core can be downsized, It turned out that a highly efficient transformer can be obtained.

Example 21 From the melt having a composition of Cu1%, Si13.5%, B7.2%, Nb2.5%, and the balance substantially Fe in atomic%, a width of 6.
A 5 mm amorphous alloy was prepared.

This amorphous alloy was wound to form a wound magnetic core having an outer diameter of 20 mm and an inner diameter of 10 mm. This magnetic core was heat-treated in an Ar atmosphere at 550 ° C. for 1 hour in the absence of a magnetic field in the same atmosphere as in the present invention example (A).
An example (B) of the present invention was prepared by performing heat treatment while applying a magnetic field of 3000 Oe at a temperature of 1 ° C for 1 hour in a direction perpendicular to the magnetic path. Two windings of 12 turns each were applied to this magnetic core to make a common mode choke. The circuit used for the pulse attenuation characteristic evaluation is shown in FIG. 26 (a), and the measured pulse attenuation characteristic is shown in FIG. 26 (b). FIG. 26 (b) shows an Mn-Zn ferrite and an F having the same shape as the common mode choke of the present invention.
The pulse attenuation characteristics for a common mode choke made of an e-based amorphous alloy are also shown.

As shown here, even in the present invention example (A) which was not subjected to the heat treatment in the magnetic field, the pulse attenuation characteristics were superior to those in the case of the Mn-Zn ferrite, and in the present invention example (B) which was subjected to the heat treatment in the magnetic field. Was found to be superior to the Fe-based amorphous alloy.

Example 22 With respect to the common mode choke created in Example 21, the frequency dependence of attenuation was measured. The measurement circuit at this time
The results are shown in Fig. 27 (a), and the results are shown in Fig. 27 (b) including the case of Mn-Zn. Thus, it was found that Mn-Zn ferrite was superior to Mn-Zn ferrite in the amount of attenuation at any frequency.

Example 23 Table 8 shows the magnetic characteristics and high-voltage pulse characteristics of the common mode choke using the ultrafine crystal alloy according to the present invention and the common mode choke of the conventional alloy. This Here, these common mode chokes have a width of 12.5 mm and an outer diameter.
A coil having a diameter of 25 mm and an inner diameter of 15 mm was wound with two turns of 22 turns. In this table, when a magnetic field was applied, a magnetic field of 3000 Oe was applied in the direction perpendicular to the magnetic path during the heat treatment.

In the case of the common mode choke of the present invention, the absolute value of complex magnetic susceptibility || at 100 kHz is higher than that prepared by crystallizing a conventional amorphous alloy, the noise damping property is excellent, and a line filter is formed. In case of 1000V, 1μsec
It can be seen that an excellent line filter was obtained because the output voltage V ₀ for the pulse voltage of was small.

It was also confirmed that || was improved by heat treatment in a magnetic field.

Example 24 Table 9 shows the magnetic characteristics and high-voltage pulse characteristics of a common mode choke according to the present invention having the same shape as that of Example 23. In this table, during the heat treatment period,
A magnetic field of 3000 Oe was applied.

As in Example 23, the complex magnetic susceptibility at 100 kHz Absolute value || and when a line filter is formed
The output voltage V was measured for a pulse voltage of 1000 V and 1 μsec. The results are shown in Table 9.

Example 25 A wound magnetic core shown in FIG. 22 (a) was made from an amorphous alloy having the composition of Example 19 and having a width of 7.5 mm and a thickness of 20 mm, and a magnetic field of 5000 Oe was formed at right angles to the magnetic path of the magnetic core during the entire heat treatment period. Ultra-fine crystallization heat treatment was applied in the direction. The heat treatment rate is 20 ℃ / m
Heated up to 500 ℃ in 1 hour, kept at 500 ℃ for 1 hour, then 5 ℃ / min
Was cooled to 280 ° C. at 280 ° C., kept at 280 ° C. for 2 hours, and then cooled to room temperature at 2 ° C./min. This magnetic core was wrapped with Kapton tape as shown in FIG. 22 (b) to prepare a magnetic core for a transformer. This magnetic core was applied to a winding and magnetic characteristics were measured.

As a result, B10 = 12kG, Br / B10 = 12%, Hc = 0.012Oe, W2 / 10
It was 0k = 240mw / cc.

Also, when a Kapton tape is wound after forming a mold core by vacuum impregnation with epoxy resin to make a transformer core, B10 = 12kG, Br / B10 = 18%, Hc = 0.018Oe, W
It was 2 / 100k = 370mw / cc.

For comparison, an amorphous alloy consisting of Si13.5%, B9%, Nb3% balance Fe in atomic% was prepared, and a Kapton tape was wound in the same manner as in the example of the present invention. A magnetic core for a transformer, which was impregnated and then wrapped with Kapton tape, was prepared. W2 / 100k = 1 for those not impregnated with epoxy resin
It was 500 mw / cc, but the one impregnated with epoxy resin is W2
/ 100k = 3300mw / cc, which markedly increased core loss. From this, it was found that the present invention had lower loss and less deterioration due to impregnation.

Example 26 An E core shown in FIG. 25 (a) was prepared from an amorphous alloy having the composition of Example 20, and heat treated at 550 ° C. for 1 hour in an Ar atmosphere to obtain a structure having ultrafine crystal grains. An E-type magnetic core for transformer shown in Fig. 25 (b) was prepared.

When the magnetic characteristics of this magnetic core were measured, the saturation magnetic flux density was
It was 12.6 kG, which was more than twice that of Mn-Zn ferrite.
The core loss was W2 / 100k = 280mw / cc.

As a transformer for a switching power supply that drives this magnetic core at 200 kHz, a winding with 13 turns on the primary side and a winding with 6 turns on the secondary side were mounted, and the temperature rise of the core was measured. The results obtained are shown in Table 7. It has been found that the magnetic core of the present invention is preferable to the Mn-Zn ferrite magnetic core because the temperature rise is small and the temperature does not affect other electric elements.

Example 27 After forming an amorphous alloy with a width of 8 mm from a molten alloy having a composition of Fe73.5Cu1Si16.5B6Nb3 at atomic% and forming a MgO layer on the surface by electrophoresis, as shown in 28 (a). It was wound around a large mold and held at 530 ° C. for 1 hour and then heat-treated for cooling. After the heat treatment, this magnetic core was impregnated with varnish, and the central portion was cut with an outer peripheral slicer. After that, the cut surface was flattened and further lapped to prepare a cut core shown in FIG. 28 (b).

The core loss at 100kHz2kG was 500mW / cc, which was a sufficiently low core loss.

Such a cut core has an advantage that the winding can be easily formed because the transformer can be formed by automatically winding the bobbin and inserting the bobbin. Further, the effective permeability can be adjusted by forming the gap.

Example 28 FIG. 29 shows the frequency dependence of the core loss of the magnetic core component of the present invention having the composition of Fe73.5Cu1Nb3Si13.5B9 shown in Example 14 in comparison with that of the conventional material.

The core loss of the magnetic core component of the present invention is as low as or lower than that of a Co-based amorphous alloy up to a high frequency region, and much lower than that of a Fe-based amorphous alloy or Mn-Zn ferrite. It shows the value and is excellent as a transformer driven at high frequency. It was found that the saturation magnetic flux density is much higher than that of Mn-Zn ferrite and Co-based amorphous alloys, and the transformer can be miniaturized.

[Effects of the Present Invention] According to the present invention, a magnetic core component that has little change over time and is excellent in durability is provided. Further, since the saturation magnetic flux density and the effective magnetic permeability are large and the core loss is small, the magnetic core component can be downsized. Furthermore, since it is Fe-based, an inexpensive magnetic core component can be provided.

[Brief description of drawings]

FIG. 1 is a diagram showing an embodiment of changes over time in effective magnetic permeability of a magnetic core used in a magnetic core component of the present invention and a comparative example, and FIG. 2 is an amorphous material formed in the middle of the manufacturing process of the present invention. FIG. 3 (a) is a diagram showing an example of an X-ray diffraction pattern of an alloy, FIG. 3 (a) is a diagram showing an example of an X-ray diffraction pattern of a magnetic core used in a magnetic core component of the present invention, and FIG. 3 (b). ) Is a diagram showing a result of microscopic observation of the magnetic core of FIG. 3 (a), FIG. 4 is a diagram showing an example of a heat treatment pattern used for manufacturing the magnetic core component of the present invention, and FIG. Is a diagram showing an embodiment of the structure of the magnetic core used in the magnetic core component of the present invention, FIG. 6 is a diagram showing a control magnetization characteristic measuring circuit used for evaluation of the saturable reactor of the present invention, FIG. Is a schematic diagram of the operation of the saturable reactor, FIG. 8 is a schematic diagram of the control magnetization curve obtained by the circuit of FIG. 6,
FIG. 9 is a diagram showing an example of the frequency dependence of the core loss of the saturable reactor of the present invention and a comparative example, and FIG. 10 is the saturable reactor of the present invention and a comparative example measured by the circuit of FIG. FIG. 11 is a diagram showing the obtained control magnetization curve, FIG. 11 is a diagram showing an example of temperature characteristics of the saturable reactor of the present invention,
FIG. 12 is a diagram showing an example of output charge characteristics when an example of the saturable reactor of the present invention is attached to a switching power supply together with a comparative example, and FIG. 13 is a magnetic core used for the saturable reactor of the present invention. FIG. 14 is a diagram showing an example of a DC BH curve of the present invention together with a comparative example, and FIG. 14 is a specific core gain when the Cu content of the alloy component of the magnetic core part used in the saturable reactor of the present invention is changed. Fig. 15 is a diagram showing one example together with a comparative example in the case of measuring, and Fig. 15 shows the specific core gain when the Nb content of the alloy component of the magnetic core used in the saturable reactor of the present invention is changed. FIG. 16 is a diagram showing an example of the case with a comparative example, FIG. 16 is a diagram showing an example of the configuration of the semiconductor reactor of the present invention, and FIG. 17 is a switching power supply using the semiconductor circuit reactor of the present invention. FIG. 18 showing an embodiment, FIG. Diagram showing an example of the effect of reducing current spikes conductor circuit reactor, Fig. 19 is showing an example of a semiconductor circuit reactor is constructed in combination with the diode of the present invention FIG, 20th
FIG. 21 is a diagram showing an embodiment of the configuration of the common mode choke of the present invention, and FIG. 21 is a diagram showing an embodiment of the noise reduction effect when the common mode choke of the present invention is used in a line filter. 22 (a) and (b) are diagrams showing an embodiment of a magnetic core used in the transformer of the present invention, and FIGS. 23 (a) and (b) are direct currents of the magnetic core used in the common mode choke and the transformer of the present invention. FIG. 24 is a diagram showing an example of a BH curve and a pulse permeability together with a comparative example, and FIG. 24 is an example of the frequency dependence of the absolute value of the complex permeability of the magnetic core used in the common mode choke and transformer of the present invention. Fig. 25 shows a comparative example, Fig. 25 (a) shows an example of an E core for a transformer, and Fig. 25 (b) shows a transformer using the E core of Fig. 25 (a). FIG. 26 (a) shows a magnetic core according to an embodiment of the present invention. FIG. 26 (b) is a diagram showing a circuit used for evaluating the pulse attenuation characteristic of the hard choke.
Is a diagram showing an example of the pulse attenuation characteristics of the common mode choke of the present invention measured by the circuit of FIG. 26 (a) together with a comparative example, and FIG. 27 (a) is the pulse attenuation of the common mode choke of the present invention. FIG. 27 is a diagram showing a circuit used to evaluate the frequency dependence of the amount, and FIG. 27 (b) is a frequency dependence of the pulse attenuation amount of the common mode choke of the present invention measured by the circuit of FIG. 27 (a). FIG. 28 is a diagram showing an example together with a comparative example, FIGS. 28 (a) and 28 (b) are explanatory views of a cut core used in the transformer of the present invention, and FIG. 29 is a core of a magnetic core used in the transformer of the present invention. It is the figure which showed one Example of the frequency dependence of loss with the comparative example.

 ─────────────────────────────────────────────────── ─── Continuation of the front page (56) Reference JP 61-295602 (JP, A) JP 61-288048 (JP, A) JP 59-63704 (JP, A) JP 1- 294847 (JP, A) JP 2-19442 (JP, A) JP 63-302504 (JP, A)

Claims (11)

[Claims] 1. Fe, Cu, and M (where M is Nb, W, Ta, Z)
At least 50% of the structure contains at least one element selected from the group consisting of r, Hf, Ti and Mo) as an essential element.
Is composed of fine crystal grains, and the rate of change in effective permeability with time X is
Magnetic core parts characterized by being 0.3 or less. 2. The magnetic core component according to claim 1, wherein the saturation magnetic flux density (Bs) is 10 kG or more and the effective magnetic permeability (μelkHz) is 5 × 10 ³ or more. 3. A core component as claimed in claim 1 or 2, characterized in that the saturation magnetostriction λs is ^{5 × 10 -6 ~-5 ×} 10 -6. 4. The magnetic core component according to claim 1, wherein the magnetic core component is a supersaturated reactor. 5. The uncontrollable magnetic flux density ΔBb at 50 kHz is 3 kG.
The magnetic core component according to claim 4, wherein: 6. The magnetic core component according to claim 1, wherein the magnetic core component is a semiconductor circuit reactor. 7. The magnetic core component according to claim 4, wherein the squareness ratio Br / B10 of the DC BH curve is 70% or more. 8. The magnetic core part according to claim 1, wherein the magnetic core part is a common mode choke. 9. A DC BH curve having a squareness ratio Br / B10 of 30% or less and an absolute value of the complex permeability at 100 kHz ||
Magnetic flux density B1 is 5 kG when a magnetic field of 1000 or more and 1 Oe is applied
Above, and when the magnetic field of 10 Oe is applied, the magnetic flux density B10 is 1
9. The magnetic core component according to claim 8, wherein the magnetic core component is 0 kG or more. 10. The magnetic core component according to claim 1, wherein the magnetic core component is a magnetic core for a high frequency transformer. 11. A DC BH curve having a squareness ratio Br / B10 of 30%.
11. The magnetic core component according to claim 10, wherein: