JPH08153614A - Magnetic core - Google Patents

Abstract

PURPOSE: To provide a magnetic core having low loss, high permeability and low characteristic deterioration due to magnetostriction. CONSTITUTION: The title magnet core is formed by winding a thin band formed by an Fe-radical soft magnetic alloy, in which crystal grains, having a body- centered cubic structure and the average grain diameter of 200 Angstroms or smaller, as measured in maximum dimensions occupy at least 80% of the structure, laminating or bonding to a substrate.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a magnetic core having excellent soft magnetic characteristics used for various transformers, choke coils, saturable reactors, noise filters and the like.

[0002]

2. Description of the Related Art Conventionally, various transformers, choke coils,
Ferrite core, which has the advantages of high electrical resistance and low eddy current loss, as a magnetic core for saturable reactors, noise filters, etc., silicon steel core with high saturation magnetic flux density and relatively low iron loss, and medium saturation magnetic flux density Permalloy cores and the like, which have relatively high frequency characteristics, have been used.

However, since the ferrite magnetic core has a low saturation magnetic flux density and poor temperature characteristics, it has a drawback that it is difficult to miniaturize the magnetic core. The silicon steel core has a high saturation magnetic flux density, but is inferior in soft magnetic characteristics, particularly magnetic permeability and core loss at high frequencies. Permalloy cores can obtain high-frequency magnetic properties superior to silicon steel, but have poor impact resistance, and have the disadvantage that high-frequency magnetic properties are easily degraded by impact.

In recent years, magnetic cores made of amorphous alloys have attracted attention and have been partially put into practical use in order to improve these drawbacks to some extent.

Amorphous alloys are mainly classified into Fe-based alloys and Co-based alloys. Fe-based amorphous alloys have the advantages that the saturation magnetic flux density is high and the material cost is lower than that of Co-based alloys. There is a problem that the core loss is higher and the magnetic permeability is lower than that of the Co-based amorphous alloy at high frequencies. Further, the Fe-based amorphous alloy has a remarkably large magnetostriction, and there is a drawback that the characteristics are remarkably deteriorated when the magnetic core is beaten or impregnated or coated.

On the other hand, the Co-based amorphous alloy has a small high frequency core loss and a high magnetic permeability, but has the disadvantages that the core loss and the magnetic permeability change over time and the saturation magnetic flux density is insufficient. Furthermore, since expensive Co is used as a main raw material, disadvantages in price are inevitable.

Under such circumstances, various proposals have been made for Fe-based amorphous alloys. In Japanese Examined Patent Publication No. 60-17019, 74-
84 atomic% Fe, 8-24 atomic% B, and 16 atomic% or less Si
And at least one of 3 atomic% or less of C, at least 85% of its structure has the form of an amorphous metal matrix, and discontinuously throughout the amorphous metal matrix. It has a precipitate of distributed crystalline particle groups, the crystalline particle group has an average particle size of 0.05 to 1 μm and an average interparticle distance of 1 to 10 μm, the particle group is 0.01 to 0.3 of the whole. An iron-based boron-containing magnetic amorphous alloy is disclosed which is characterized by occupying an average volume fraction of. The crystalline particles of this alloy have a discontinuous distribution of α that interacts with the pinning point of the domain wall.
-It is said to be a group of (Fe, Si) particles.

Further, JP-A-60-52557 discloses that Fe _a Cu _b B _c Si _d (provided that 75 ≦ a ≦ 85, 0 <b ≦ 1.5, 10 ≦ c ≦ 20, d ≦ 10 and c + d ≦ 3.
A low-loss amorphous magnetic alloy consisting of 0) is disclosed. This amorphous alloy is heat treated below the crystallization temperature and above the Curie temperature.

[0009]

In the magnetic core made of the Fe-based soft magnetic alloy of Japanese Patent Publication No. 60-17019, the core loss is reduced due to the presence of discontinuous crystalline particles, but the core loss is still large. In particular, since the magnetostriction is large, there is a problem that a beat is generated and the impregnating coating causes a core loss and a remarkable deterioration of magnetic permeability, and a cut core or the like having high characteristics has not been obtained.

On the other hand, in the Fe-based amorphous alloy disclosed in JP-A-60-52557, the core loss of the magnetic core is reduced due to the effect of containing Cu. Not as satisfying as a magnetic core. Further, there is a problem that the core loss with time and the magnetic permeability are not sufficient.

Therefore, an object of the present invention is to provide a magnetic core having a low core loss, a high magnetic permeability and a small characteristic deterioration due to magnetostriction.

[0012]

As a result of earnest research in view of the above object, the present inventor has found the following.

Samples having different ratios of fine crystal grains under various heat treatment conditions were prepared from a molten metal having a composition of Fe _73.4 Cu ₁ Nb _3.1 Si _13.4 B _9.1 by using a single roll method to produce amorphized ribbons. No. 1 to 5) were produced. Percentage of crystal grains, effective permeability (μ _e1KHz ), core loss (W _{2 / 100K} : 100KHz, Bm 2K)
(In G). The results are shown in FIGS. 13 and 14. Further, transmission electron microscope photographs (300,000 times) of Samples 1 to 5 are shown in FIGS. The proportion of fine crystal grains obtained by the line segment method described later and the average (angstrom) of the grain size measured by the maximum dimension are as follows.

[0014] As is clear from FIGS. 13 and 14, when the ratio of fine crystal grains is 80% or more, the effective magnetic permeability is significantly improved and the core loss is reduced.

As a result of X-ray diffraction and transmission electron microscope analysis of the above samples, it was determined that the fine crystal grains were Fe having a body-centered cubic lattice structure in which Si or the like was dissolved. The present invention is based on the above findings, and the average grain size measured in the maximum dimension having a body-centered cubic lattice structure is 200 angstroms or less crystal grains occupy at least 80% of the structure Fe
A magnetic core is formed by winding a thin plate of a base soft magnetic alloy, laminating it, or adhering it to a substrate.

A preferred composition for the alloy used in the magnetic core according to the present invention is represented by the general formula: (Fe _1-a M _a ) _100-xyz- α _- β _- γCu _x Si _y B _z M'αM "βXγ (atomic% (However, M is Co and / or Ni, and M'is Nb, W, Ta, Zr,
At least one element selected from the group consisting of Hf, Ti and Mo, M "is V, Cr, Mn, Al, a white metal element, Sc, Y, a rare earth element, Au, Z
n, Sn, at least one element selected from the group consisting of Re,
X is at least one element selected from the group consisting of C, Ge, P, Ga, Sb, In, As, Be, and a, x, y, z, α, β and γ are each 0 ≦ a. <0.5, 0.1 ≤ x ≤ 3, 0 ≤ y ≤ 30, 0 ≤ z ≤ 25, 0 ≤ y + z ≤ 3
5, 0.1 ≦ α ≦ 30, 0 ≦ β ≦ 10 and 0 ≦ γ ≦ 10 are satisfied. ).

The Fe-based soft magnetic alloy used in the magnetic core according to the present invention includes a step of rapidly cooling an amorphous alloy having a predetermined composition from a molten metal, and a heat treatment step of heating the amorphous alloy to form fine crystal grains. Obtained by

In the alloy used in the present invention, Cu
Is contained in the range of 0.1 to 3 atomic%. If it is less than 0.1 atom%, there is almost no effect of lowering core loss and increase of magnetic permeability due to addition of Cu, while if it is more than 3 atom%, core loss may be larger than that without addition, and permeability is also deteriorated. To do. Particularly preferred Cu content in the present invention
x is 0.5 to 2 atomic%, and the core loss is particularly small in this range.

The cause of the decrease of the core loss and the increase of the magnetic permeability of Cu is not clear, but it is considered as follows.

The interaction parameter between Cu and Fe is positive,
Since the solid solubility is low and there is a tendency for separation, when an alloy in an amorphous state is heated, Fe atoms or Cu atoms gather to form clusters, resulting in composition fluctuations. For this reason, a large number of regions are likely to be partially crystallized, and fine crystal grains are generated with these regions as nuclei. Since this crystal has Fe as a main component and there is almost no solid solubility between Fe and Cu, Cu is extruded around fine crystal grains due to crystallization, and the Cu concentration around the crystal grains becomes high. Therefore, it is considered that crystal grains are hard to grow.

As described above, it is considered that the addition of Cu produces a large number of crystal nuclei and makes it difficult for the crystal grains to grow, so that the grain refinement occurs, but this action is caused by Nb, Ta, W, Mo, Zr, Hf, Ti.
It is believed that the presence of the above will make it particularly remarkable.

When Nb, Ta, W, Mo, Zr, Hf, Ti, etc. are not present, the crystal grains are not so finely divided. Nb, Ta, Zr, Hf, and Mo have a particularly large effect, but when Nb is added among these elements, the crystal grains tend to be particularly thin and excellent soft magnetic properties can be obtained.

Further, since a fine crystalline phase containing Fe as a main component is generated, the magnetostriction becomes smaller than that of the Fe-based amorphous alloy, and the magnetic anisotropy due to internal stress-strain becomes small, and the soft magnetic characteristics are improved. It is considered to be the reason.

Among the Fe-based soft magnetic alloys relating to the magnetic core of the present invention, for example, those having a negative magnetostriction, such as an alloy represented by the composition formula: Fe _bal Cu ₁ Nb ₃ B ₅ Si _17.5 , or Magnetostriction of 0 or almost 0 is also included.

When Cu is not added, the crystal grains are hard to be made fine and the compound phase is easily formed, so that the magnetic characteristics are easily deteriorated by the crystallization.

V, Cr, Mn, Al, white metal element, Sc, Y, rare earth element,
Elements such as Au, Zn, Sn, and Re have effects of improving corrosion resistance, improving magnetic properties, and adjusting magnetostriction. Its content is at most 10 atomic% or less. This is because if the content exceeds 10 atomic%, the saturation magnetic flux density will be significantly reduced, and the particularly preferable content is 8 atomic% or less.

Among these, Ru, Rh, Pd, Os, Ir, Pt, Au, Cr, V
When it is made of an alloy to which at least one element selected from the above is added, the magnetic core has excellent corrosion resistance and wear resistance.

In the present invention, C, Ge, P, Ga, Sb, In, Be, As
It is also possible to contain at least one element selected from the group consisting of 10 atomic% or less. These elements are effective for amorphization, and when added together with Si and B, they help amorphization of the alloy and are effective for adjusting magnetostriction and Curie temperature.

Si and B are elements particularly useful for refining the crystal grains of the alloy according to the present invention. The Fe-based soft magnetic alloy according to the present invention is preferably obtained by once forming an amorphous alloy by the effect of adding Si and B and then forming fine crystal grains by heat treatment. The reason for limiting the contents y and z of Si and B is that y is 30 atomic% or less, z is 25 atomic% or less, and y + z is 35 atomic% or less, the saturation magnetic flux density of the alloy is significantly reduced. Is.

When the amount of addition of the other amorphous forming element is small, if the y + z is in the range of 10 to 35 atomic%, the amorphization of the alloy at the intermediate stage is easy. However, since M ′ described later also acts as an amorphous forming element, the inclusion of B and Si is not essential.

In the present invention, M'has a function of refining the crystal grains precipitated by complex addition with Cu, and is selected from the group consisting of Nb, W, Ta, Zr, Hf, Ti and Mo. It is at least one element. Nb and the like have the effect of increasing the crystallization temperature of the alloy, but it is considered that the precipitated crystal grains become finer due to the interaction with Cu which has the function of forming clusters and lowering the crystallization temperature. The content α of M ′ is 0.1 to 30 atom%, and if it is less than 0.1 atom%, the effect of grain refinement is insufficient, while if it exceeds 30 atom%, the saturation magnetic flux density is significantly reduced. The preferable content α of M ′ is 2 to 8 atom%. Note that Nb is most preferable as M ′ in terms of magnetic characteristics. Further, by adding M ′, it has a high magnetic permeability equivalent to that of the Co-based high magnetic permeability material.

The balance consists essentially of Fe except for impurities, but part of Fe can be replaced by the component M (Co and / or Ni). The content a of M is 0 ≦ a <0.5,
Preferably, 0 ≦ a ≦ 0.3. This is because if a exceeds 0.3, the core loss may increase.

Addition of M "can improve the corrosion resistance, improve the magnetic properties, or adjust the magnetostriction. When M" exceeds 10 atomic%, the saturation magnetic flux density is significantly reduced.

Among the alloys according to the present invention, in particular 0 ≦ a ≦ 0.3,0.
When 5 ≦ x ≦ 2, 10 ≦ y ≦ 25, 3 ≦ z ≦ 12, 18 ≦ y + z ≦ 28, 2 ≦ α ≦ 8, particularly high magnetic permeability and low core loss are easily obtained.

In the Fe-based soft magnetic alloy according to the present invention, at least 80% or more of the structure is composed of fine crystal grains having a body-centered cubic lattice structure.

This crystal grain is mainly composed of α-Fe and is composed of Si.
It is considered that B, etc. are in solid solution. The crystal grains are characterized by having a remarkably small average grain size of 200 angstroms or less, and are uniformly distributed in the alloy structure. The part of the alloy structure other than the fine crystal grains is mainly amorphous.
Note that the magnetic core of the present invention exhibits sufficiently excellent magnetic characteristics even when the proportion of fine crystal grains is substantially 100%.

The proportion of fine crystal grains in the present invention is a value obtained by the line segment method. This line segment method is a general method, and the total length (L1, L2, L3, ... Ln) of each crystal grain (L1) crossed by an arbitrary line segment (length L) drawn in the micrograph + L2 + L3
+ ... Ln) is obtained and divided by L to obtain the proportion of crystal grains. When the proportion of crystal grains increases to about 80% or more, the crystal grains appear to occupy almost the entire structure, but it is considered that some amorphous phase is present in this case as well. This is because the outer peripheral portion of the crystal grain looks blurred in the micrograph as shown in FIG. 19, which is considered to be due to the presence of the amorphous phase. Under this premise, the proportion of the amorphous phase can be known from the proportion of the peripheral portion that appears to be blurred. When the proportion of crystal grains is large as described above, it is extremely difficult to express the proportion by an accurate numerical value.

In the present invention, unavoidable impurities such as N, O and S can be regarded as the same as the alloy composition used in the magnetic core of the present invention even if they are contained to the extent that the desired characteristics are not deteriorated. Of course.

Next, a method of manufacturing the magnetic core of the present invention will be described. First, a ribbon-shaped amorphous alloy is formed from a molten metal having the above-mentioned predetermined composition by a known liquid quenching method such as a single roll method or a twin roll method. Usually, the sheet thickness of the amorphous alloy ribbon produced by the single roll method or the like is about 3 to 100 μm, but the sheet thickness of 25 μm or less is particularly suitable as a ribbon for magnetic cores used at high frequencies.

This amorphous alloy may contain a crystal phase, but it is desirable that it be amorphous in order to uniformly generate fine crystal grains by the subsequent heat treatment.

The amorphous ribbon is preferably wound, punched, etched or the like to be processed into a predetermined shape to form a magnetic core before heat treatment.

The reason for this is that the ribbon has good workability in the amorphous state, but in many cases, once crystallized, the workability deteriorates remarkably. However, it is also possible to manufacture the magnetic core by performing processing such as winding after the heat treatment or etching.

The heat treatment is carried out by holding the amorphous alloy ribbon processed into a predetermined shape in a vacuum, in an atmosphere of an inert gas such as hydrogen, nitrogen, Ar or the like, or in the air for a certain period of time. The heat treatment temperature and time vary depending on the shape, size, composition, etc. of the magnetic core made of the amorphous alloy ribbon, but generally 450 ° C to 7 ° C.
5 minutes to 24 hours at 00 ° C is desirable. Heat treatment temperature is 450 ℃
If it is less than crystallization, crystallization is less likely to occur and the heat treatment takes too long. On the other hand, if the temperature is higher than 700 ° C., coarse crystal grains may be generated or crystal grains having an inhomogeneous form may be generated, and it becomes impossible to obtain fine crystal grains uniformly. Regarding the heat treatment time, if it is less than 5 minutes, it is difficult to keep the temperature of the processed alloy uniform, and the magnetic properties are likely to vary.If it is longer than 24 hours, not only the productivity deteriorates, but also excessive growth of crystal grains occurs. Magnetic properties are likely to be deteriorated due to the generation of nonuniform crystal grains. A preferable heat treatment condition is 500 ° C. to 650 ° C. for 5 minutes to 6 hours in consideration of practicality and uniform temperature control.

The heat treatment atmosphere is preferably an inert gas atmosphere such as Ar, nitrogen, hydrogen or a reducing atmosphere, but may be an oxidizing atmosphere such as the air. Cooling can be appropriately performed by air cooling, furnace cooling, or the like. Further, in some cases, a multi-step heat treatment can be performed. In the heat treatment, the magnetic core can be heat-treated by causing a current to flow through the core material or applying a high-frequency magnetic field to generate heat.

The heat treatment can be performed in a magnetic field such as direct current or alternating current. Further, by heat treatment in a magnetic field, magnetic anisotropy is caused in the alloy used for the main magnetic core to improve the characteristics. The magnetic field may be applied during the heat treatment, but it is not necessary to apply it for the entire period, and a sufficient effect can be obtained at a temperature lower than the Curie temperature Tc of the alloy.

[0046]

EXAMPLES The present invention will be described in more detail with reference to the following examples, which should not be construed as limiting the invention thereto.

(Example 1) Cu1%, Si16.5%, B6 in atomic%
%, Nb3%, and the balance substantially consisting of Fe,
A ribbon with a width of 20 mm and a thickness of 18 μm was prepared by the single roll method. When X-ray diffraction of this ribbon was performed, a halo pattern typical of an amorphous alloy as shown in FIG. 1 was obtained.
A transmission electron micrograph (300,000 times) of this ribbon is shown in Fig. 2.
Shown in As is clear from FIGS. 1 and 2, the ribbon obtained was almost completely amorphous. Next, a ring having an outer diameter of 13 mm and an inner diameter of 10 mm was punched out from this amorphous ribbon and heat-treated at 530 ° C. for 1 hour in an argon gas atmosphere. The X-ray diffraction pattern of the ribbon after the heat treatment showed a crystal peak as shown in FIG. FIG. 4 is a transmission electron microscope (300,000 times) of the ribbon after this heat treatment, and it was found that most of the structure after heat treatment (almost 100%) consisted of fine crystal grains. The average grain size of the crystal grains was about 100 Å.

From the X-ray diffraction pattern and the analysis by the transmission electron microscope, it was presumed that the crystal grains were Fe having a body-centered cubic structure in which Si or the like was formed as a solid solution.

Observation of the concentration distribution of Cu in the structure confirmed that Cu was mainly present around the crystal grains.

Next, ten heat-treated ring-shaped thin strips were laminated and placed in a phenol resin core case, and the magnetic characteristics were measured.

As a result, Bs = 12 kG, Br / Bs = 62%, Hc = 0.012 Oe,
The characteristics of effective magnetic permeability μ _e1K = 76000,100kHz at 1kHz and core loss W _{2 / 100K} = 250mW / cc at Bm 2kG were obtained. Bs
_Are higher than Co-based amorphous magnetic cores, and effective permeability μ _e1K and core loss W _{2 / 100K} show excellent characteristics comparable to Co-based amorphous magnetic cores.

Next, the magnetic core was impregnated with an epoxy resin and the magnetic characteristics were measured. Bs = 12kG, Br / Bs = 50%, Hc = 0.014 Oe, μ
_e1K = 42000, W _{2 / 100K} = 380mW / cc
It was confirmed that the characteristic deterioration was significantly smaller than that of the base amorphous magnetic core.

In order to clarify the reason for this, the saturation magnetostriction constant λs of the ribbon in the amorphous state and the same heat treatment condition was measured. As a result, it was confirmed that λs = + 20.8 × 10 ^-6 in the amorphous state and λs = + 1.3 × 10 ^-6 after the heat treatment, and that the magnetostriction of the magnetic core of the present invention is extremely small.

(Example 2) Width 5 m having the composition shown in Table 1
An amorphous alloy ribbon having a thickness of m and a thickness of 18 μm was produced by a single roll method and wound in a toroidal shape with an outer diameter of 19 mm and an inner diameter of 15 mm to form a wound magnetic core. The winding method was such that the surface that was in contact with the roll and solidified was the inside. An adhesive was used at the beginning of winding and a polyimide tape was used at the end of winding. MgO powder was attached to the surface of the ribbon by electrophoresis to perform interlayer insulation. Next, the winding core is heated in the N ₂ gas atmosphere to a temperature about 50 ° C higher than the crystallization temperature at a heating rate of about 10 ° C / min, and after holding for 1 hour at room temperature at a cooling rate of about 5 ° C / min. Then, a heat treatment for cooling down was performed to obtain a magnetic core of the present invention made of an alloy having an ultrafine grain structure.

When the structure was observed in the same manner as in Example 1, most of the alloys shown in Table 1 had fine crystal grains having a body-centered cubic structure with an average grain size of 100 to 150 angstroms (almost 100%). It was confirmed that Cu occupied mainly in the crystal grains and that Cu was mainly present around the crystal grains.

After the magnetic core was immersed in silicone oil, it was placed in a phenol resin case filled with silicone grease, and the lid was fixed with an adhesive. Next, the DC BH curve of this winding core, the effective magnetic permeability μ _{e1K at} 1 kHz, the core loss W _{2 / 100K} at a frequency of 100 kHz and Bm 2 kG were measured. The saturation magnetostriction λs was also measured. Table 1 shows the obtained results.
Shown in Some of the alloys of the present invention have a saturation magnetic flux density Bs of more than 10 kG, which is higher than that of a Co-based amorphous alloy and has a soft magnetic property.
It can be seen that characteristics equal to or higher than those of Co-based amorphous can be obtained. Also, a magnetostriction of small magnetostriction can be obtained.

[0057]

[Table 1] Bs Hc W _{2 / 100K} λs Composition (at%) μ _e1K (kG) (Oe) (mW / cc) (× 10 ^-6 ) Fe ₇₄ Cu _0.5 Si _13.5 B ₉ Nb ₃ 12.4 0.013 68000 300 +1.8 Fe ₇₄ Cu _1.5 Si _13.5 B ₉ Nb ₂ 12.6 0.015 76000 230 +2.0 Fe ₇₉ Cu _1.0 Si ₈ B ₉ Nb ₃ 14.6 0.056 21000 470 +1.8 Fe _74.5 Cu _1.0 Si _13.5 B ₆ Nb ₅ 11.6 0.020 42000 350 + 1.5 Fe ₇₇ Cu _1.0 Si ₁₀ B ₉ Nb ₃ 14.3 0.025 48000 430 +1.6 Fe _73.5 Cu _1.0 Si _17.5 B ₅ Ta ₃ 10.5 0.015 42000 380 -0.3 Fe ₇₁ Cu _1.5 Si _13.5 B ₉ Mo ₅ 11.2 0.012 68000 280 +1.9 Bright Fe ₇₄ Cu _1.0 Si ₁₄ B ₈ W ₃ 12.1 0.022 74000 250 +1.7 Fe ₇₃ Cu _2.0 Si _13.5 B _8.5 Hf ₃ 11.6 0.028 29000 350 +2.0 Fe _74.5 Cu _1.0 Si _13.5 B ₉ Ta ₂ 12.8 0.018 33000 480 +1.8 Example Fe ₇₂ Cu _1.0 Si ₁₄ B ₈ Zr ₅ 11.7 0.030 28000 380 +2.0 Fe _71.5 Cu _1.0 Si _13.5 B ₉ Ti ₅ 11.3 0.038 28000 480 +1.8 Fe ₇₃ Cu _1.5 Si _13.5 B ₉ Mo ₃ 12.1 0.014 69000 250 +2.8 Fe _73.5 Cu _1.0 Si _13.5 B ₉ Ta ₃ 11.4 0.017 43000 330 +1.9 Fe ₇₁ Cu _1.0 Si ₁₃ B ₁₀ W ₅ 10.0 0.023 68000 320 +2.5 Secondary Fe ₇₈ Si ₉ B ₁₃ Amorphous 15.6 0.03 5000 3300 +27 _Conventional Co _70.3 Fe _4.7 Si ₁₅ B ₁₀ Amorphous 8.0 0.006 8500 350 〜 0 Example Fe _84.2 Si _9.6 Al _6.2 (wt%) 11.0 0.02 10000 − 〜 0

(Example 3) Composition 2 shown in Table 2 width 5 mm, thickness
An amorphous alloy ribbon of 18 μm was produced by the single roll method, and the surface solidified by contact with the roll was placed outside, and was wound around a ceramic bobbin in a toroidal shape with an outer diameter of 19 mm and an inner diameter of 15 mm to produce a wound magnetic core. . At the beginning of the winding, laser light was irradiated to partly melt and fix, and at the end of winding, it was fixed with a metal tape. Next, this winding core is placed in an Ar gas atmosphere for about 20
An alloy having an ultrafine grain structure that is heated to a temperature about 50 ° C higher than the crystallization temperature at a heating rate of ℃ / min, held for 1 hour, and then cooled to room temperature at a cooling rate of about 10 ° C / min. The magnetic core of the present invention consisting of When the structure was observed in the same manner as in Example 1, all the alloys in Table 2 had an average grain size of 100 to 150.
Fine crystal grains with an angstrom body-centered cubic structure occupy most of the structure (almost 100%) and Cu
It was confirmed that was mainly present around the crystal grains.

Next, the DC BH curve of this winding core, 1 kHz
The effective permeability μ _e1K , the frequency 100kHz, the core loss W _{2 / 100K at} Bm _2kG , and the saturation magnetostriction λs of the alloy were measured. The obtained results are shown in Table 2. The saturation magnetic flux density Bs of the magnetic core of the present invention is higher than that of a normal Co-based amorphous alloy or 80 wt% Ni permalloy, and μ _e1K , Hc, W _{2 / 100K and the} like show characteristics equal to or higher than those of the Co-based amorphous and have a small magnetostriction. It can be seen that the magnetic core of the present invention has excellent characteristics as a soft magnetic material and has excellent characteristics.

[0060]

[Table 2] Bs Hc W _{2 / 100K} λs Composition (at%) μ _e1K (kG) (Oe) (mW / cc) (x10 ^-6 ) (Fe _0.959 Ni _0.041 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb ₃ 12.3 0.018 32000 280 +4.6 (Fe _0.93 Ni _0.07 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb ₃ 12.1 0.023 18000 480 +4.8 (Fe _0.905 Ni _0.095 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb ₃ 11.8 0.020 16000 540 +5.0 (Fe _0.986 Co _0.014 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb ₃ 12.6 0.011 82000 280 +4.0 (Fe _0.959 Co _0.041 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb ₃ 13.0 0.015 54000 400 +4.2 (Fe _0.93 Co _0.07 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb ₃ 13.2 0.020 27000 500 +4.8 Fe _71.5 Cu ₁ Si _15.5 B ₇ Nb ₅ 10.7 0.012 85000 230 +2.8 Fe _71.5 Cu ₁ Si _17.5 B ₅ Nb ₅ 10.2 0.010 80000 280 +2.0 Fe _71.5 Cu ₁ Si _19.5 B ₃ Nb ₅ 9.2 0.065 8000 820 +1.6 Fe _70.5 Cu ₁ Si _20.5 B ₅ Nb ₃ 10.8 0.027 23000 530 ~ 0 Fe _75.5 Cu ₁ Si _13.5 B ₇ Nb ₃ 13.3 0.011 84000 250 +1.5 Fe ₈₇ Cu ₁ B ₅ Zr ₇ 15.5 0.044 20000 570 +0.9 Fe ₉₀ Cu ₁ B ₂ Hf ₇ 16.0 0.037 18000 540 〜 0 Fe ₈₈ Cu ₁ Si ₂ B ₃ Zr ₇ 15.0 0.025 28000 540 〜 0 Fe ₉₀ Cu ₁ B ₂ Zr ₇ 16.5 0.03 17000 580 〜 0 Fe ₈₆ Cu ₁ B ₆ Zr ₇ 15.2 0.04 48000 520 ~ 0

Example 4 An amorphous alloy ribbon having a composition of Fe ₇₉ Cu ₁ Nb ₃ Si ₈ B ₉ (atomic%) and a width of 50 mm and a thickness of 18 μm was prepared, and E having the shape shown in FIG. Photo-etching was performed on the shape of the mold. Next, after forming a SiO ₂ film on the surface of this ribbon, heat treatment was carried out at 550 ° C. higher than the crystallization temperature for 1 hour and air cooling to room temperature.

Next, this was laminated between layers with an epoxy resin interposed therebetween to obtain a laminated magnetic core having the shape shown in FIG. Next, this magnetic core is 2
The loss was measured at 100 kHz and Bm 2 kG with one combined EE core. The core loss was 400 mW / cc, which was comparable to that of a Co-based amorphous magnetic core.

Example 5 An amorphous alloy ribbon having a composition shown in Table 3 and having a width of 5 mm and a thickness of 18 μm was prepared by a single roll method to prepare a wound magnetic core having an inner diameter of 12 mm and an outer diameter of 18 mm. Next, this wound core was heat-treated in the atmosphere at a temperature 50 ° C. higher than the crystallization temperature to obtain a core of the present invention made of an alloy having a fine grain structure. Analysis of the thin ribbon surface of the magnetic core confirmed that a silicon oxide layer had been formed.

Next, this magnetic core was put in a case made of phenol resin, and the effective magnetic permeability μ _{e1K at} 1 kHz, 100 kHz, and core loss W _{2 / 100K} at ₂ kG were measured.

After the measurement, an epoxy resin was placed in the case, vacuum impregnated and cured at 120 ° C., and then μe1K and W2 / 100K were measured in the same manner. Table 3 shows the obtained results. For comparison, the results of a study on a conventional amorphous wound core are also shown.

The Co-based amorphous magnetic core has a high μe1K and a low core loss W2 / 100K, and its characteristics do not deteriorate much after impregnation, but the saturation magnetic flux density Bs is lower than that of the magnetic core of the present invention. The Fe-based amorphous magnetic core is significantly impaired in both μe1K and core loss due to impregnation.

On the other hand, it can be seen that some of the magnetic cores of the present invention have Bs of 10 kG or more, and the magnetic properties after impregnation are not significantly deteriorated and exhibit excellent properties.

[0068]

[Table 3] Composition before and after immersion (at%) Bs W _{2 / 100K} W _{2 / 100K} (kG) μ _e1K (mW / cc) μ _e1K (mW / cc) Fe _70.5 Cu ₁ Nb ₃ Si _20.5 B ₅ 10.8 23000 530 20000 550 Fe _73.5 Cu ₁ Nb ₃ Si _17.5 B ₅ 11.8 50000 350 45000 370 Fe _71.5 Cu ₁ Nb ₅ Si _17.5 B ₅ 10.2 80000 280 56000 340 Fe ₇₃ Cu _1.5 Mo ₃ Si _13.5 B ₉ 12.1 69000 250 48000 320 Fe _73.5 Cu ₁ Ta ₃ Si _17.5 B ₅ 10.5 42000 380 38000 410 Bright Fe ₇₃ Cu ₂ Hf ₃ Si _13.5 B _8.5 11.6 29000 350 20000 390 Fe ₇₂ Cu ₁ Zr ₅ Si ₁₄ B ₈ 11.7 28000 480 19000 550 Example Fe ₇₄ Cu ₁ W ₃ Si ₁₄ B ₈ 12.1 74000 250 59000 330 Fe ₇₇ Cu ₁ Nb ₃ Si ₁₀ B ₉ 14.3 48000 430 32000 550 Fe _74.5 Cu ₁ Nb ₃ Si _13.5 B ₈ 11.6 42000 350 38000 380 Slave Fe _74.5 Nb ₃ Si _13.5 B ₉ Amorphous 12.7 14400 1470 2000 3300 Fe _77.5 Si _13.5 B ₉ Amorphous 15.0 3800 2800 1500 3800 Example Co ₆₇ Fe ₄ Mo _1.5 Si _16.5 B ₁₁ 5.5 88000 350 65000 380 Amorphous

Example 6 Fe _73.5 C having a width of 25 mm and a thickness of 20 μm
u ₁ Nb ₃ Si _13.5 B ₉ amorphous alloy ribbon was prepared by the single roll method.

Next, the thin ribbon and the glass tape were overlapped and wound to form a wound magnetic core having an outer diameter of 150 mm and an inner diameter of 100 mm, which has a shape shown in FIG.

Next, a glass-coated copper wire is wound around this wound magnetic core, and a current is applied to the copper wire to apply a magnetic field of about 10 Oe in the magnetic path direction, and heat treatment is performed at 550 ° C. for 1 hour in an N ₂ gas atmosphere. It was

The heating rate is 10 ° C./min, the cooling rate is 2.5 ° C./mi
n. The DC BH curve, core loss, and maximum magnetic permeability of this magnetic core were measured.

As a result, the saturation magnetic flux density Bs was 12.4 kG, the squareness ratio Br / Bs was 90%, the coercive force Hc was 0.005 Oe, and the maximum magnetic permeability μm was 1.
800000,100kHz, core loss W _{2 / 100K at} 2kG is 800mW / c
The characteristic of c was obtained.

Example 7 An amorphous alloy ribbon having a composition of Fe _71.5 Cu ₁ Nb ₅ Si _13.5 B ₉ and a width of 3 mm and a thickness of 15 μm was prepared,
A wound magnetic core having an outer diameter of 8 mm and an inner diameter of 4 mm was produced. Next, this magnetic core was placed in a furnace whose temperature was raised to 610 ° C. while flowing nitrogen gas, held for 1 hour, taken out of the furnace, and air-cooled.

A magnetic core made of the obtained alloy having a fine crystal grain structure was powder-coated with epoxy resin to a thickness of about 0.5 mm, and the effective magnetic permeability μ at the BH curve and 1 kHz was obtained.
The core loss W _{2 / 100K} at _e1K , 100kHz and _2kG was measured.
The results obtained are shown in Table 4.

For comparison, the characteristics of a Fe _76.5 Cr ₁ Si _13.5 B ₉ amorphous alloy magnetic core coated are shown.

It can be seen that the magnetic core of the present invention has a smaller magnetostriction than the conventional Fe-based amorphous magnetic core, is less susceptible to the influence of strain, and exhibits excellent characteristics even when coated. Further, the coated core of the present invention was placed in a constant temperature bath having a humidity of 90% and a temperature of 30 ° C. for one month, and the magnetic characteristics were measured again, but no change was observed. In addition, it was confirmed that there was no change in the magnetic properties even after falling 10 times from concrete at a height of 1 m onto concrete.

[0078]

[Table 4] Composition Bs Hc μ _e1K W _{2 / 100K} (at%) (kG) (Oe) (mW / cc) Inventive Fe _71.5 Cu ₁ Nb ₅ Si _13.5 B ₉ 11.3 0.012 72000 320 Conventional example Fe _76.5 Cr ₁ Si _13.5 B ₉ amorphous 14.3 0.11 1400 2400

Example 8 An amorphous alloy ribbon having a composition of Fe _73.5 Cu ₁ Ta ₃ Si _13.5 B ₉ and a width of 20 mm and a thickness of 20 μm was produced by a single roll method. Next, a solution containing a tyranopolymer as a main component was applied to this ribbon and dried at 200 ° C., and then a wound magnetic core having a shape shown in FIG. 8 was produced and heat-treated in an N ₂ atmosphere. In the heat treatment, the temperature was raised at a rate of 10 ° C / min, the temperature was kept at 570 ° C for 1 hour, and then the temperature was cooled to room temperature at a cooling rate of 5 ° C / min. Next, wrap Kapton tape around this magnetic core as shown in Fig. 9.
The core loss at 100kHz, 2kG was measured. A value of 430 mW / cc, which is comparable to that of a Co-based amorphous magnetic core, was obtained. After the measurement, the ribbon was observed by a transmission electron microscope, and it was confirmed that the majority of the texture (almost 100%) consisted of crystal grains with an average grain size of about 100 Å.

(Example 9) An amorphous alloy ribbon having a composition of Fe _74.5 Cu ₁ Nb ₂ Si _13.5 B ₉ and a width of 20 mm and a thickness of 20 μm was prepared and punched with a press to have an outer diameter of 13 mm and an inner diameter of 10 mm. A heat treatment was carried out in which the furnace was placed in a N ₂ gas atmosphere maintained at ℃ for 1 hour, taken out of the furnace and air-cooled. Next, use this ring-shaped ribbon
20 layers were alternately laminated with a ceramic ring having a diameter of 13 mm, an inner diameter of 10 mm and a thickness of 40 μm to fabricate a magnetic core of the present invention.

Effective permeability μ _{e1K at} 1 kHz is 76000,100
A core loss of 250 mW / cc at 2 kHz was obtained. When the structure was observed with a transmission electron microscope after the measurement, it was confirmed that most of the structure (almost 100%) was composed of crystal grains having an average particle size of about 100 angstroms.

Example 10 An amorphous alloy ribbon having a width of 25 mm and a thickness of 25 μm and having a composition of Fe _71.5 Cu ₁ Nb ₅ Si _15.5 B ₇ was prepared, and SiO ₂ —TiO ₂ -based metal alkoxide was partially hydrolyzed. A solution prepared by mixing ceramic powder with sol was applied on one surface, dried, and then wound around a stainless steel ring having an outer diameter of 80 mm and an inner diameter of 78 mm to produce a wound magnetic core having an inner diameter of 80 mm and an outer diameter of 120 mm. Next, wind a glass-coated copper wire around this magnetic core, apply an alternating current to it, and apply a maximum magnetic field of 10 Oe in the magnetic path direction at 10 ° C /
The temperature was raised at a heating rate of min and kept at 590 ° C for 1 hour, and then the temperature was lowered to room temperature at a cooling rate of 5 ° C / min.

Next, a 1 mm-thick stainless steel band was fixed to the outer periphery of the magnetic core. When the magnetic characteristics of this magnetic core were measured, the saturation magnetic flux density Bs was 10.6 kG and the squareness ratio Br / Bs was 8
The characteristics were 0%, coercive force Hc was 0.015 Oe, 100kHz, and core loss was 500mW / cc at 2kG. Since the saturation magnetic flux density is high, the squareness ratio is high, and the core loss is low, it is optimal for a magnetic switch for pulse compression and the like. When the structure was observed with a transmission electron microscope after measurement, most of the structure (approximately 10
It was confirmed that 0%) consisted of crystal grains with an average grain size of about 120 angstroms.

Example 11 An amorphous alloy ribbon having a composition of Fe _73.5 Cu ₁ Nb ₃ Si _13.5 B ₉ and a width of 15 mm and a thickness of 15 μm was prepared, and alumina powder was applied on the surface thereof, and then the outer diameter was 30 mm. , Inner diameter 18
With a magnetic core of 5,000 mm in the direction perpendicular to the magnetic path, the temperature was raised to 550 ° C at a heating rate of 20 ° C / min and held for 1 hour, then at a cooling rate of 2 ° C / min to 250 mm. After cooling to ℃, the magnetic field application was stopped and the product was taken out of the furnace and sprinkled with nitrogen gas to cool it to room temperature. Put the heat-treated core in a bake-made core case and set the DC BH curve and pulse transmittance in μp.
The operating magnetic flux density ΔB dependence of was measured. The obtained results are shown in FIGS. As a result of transmission electron microscopy and X-ray diffraction, it was confirmed that 80% or more of the magnetic core after heat treatment was composed of fine crystal grains.

The magnetic core of the present invention has a high saturation magnetic flux density, a low squareness ratio and a high magnetic permeability, and the effective magnetic flux permeability μp dependency of the operating magnetic flux density variation ΔB is far superior to that of the Mn-Zn ferrite or Co-based amorphous magnetic core. ing. Therefore, it is most suitable for transformers for inverters and magnetic cores for common mode chokes.

(Example 12) A width of 5 mm was obtained by the single roll method.
A Fe _73.5 Cu ₁ Nb ₃ Si _13.5 B ₉ amorphous alloy ribbon having a plate thickness of 18 μm was produced and wound around an outer diameter of 19 mm and an inner diameter of 15 mm to produce a wound magnetic core.

One of the prepared wound magnetic cores was placed in a furnace heated to 550 ° C. as it was, held for 1 hour and then heat-treated to be taken out of the furnace. The other was wound with a glass-coated copper wire and an electric current was applied to the copper wire. And apply a magnetic field of 10 Oe in the direction of the magnetic path of the magnetic core.
The furnace was heated to ℃ for 1 hour, then cooled to 280 ℃ at a cooling rate of 5 ℃ / min, taken out of the furnace and air-cooled to room temperature.

FIG. 12 shows the temperature characteristic of the magnetic core after the heat treatment. As a result of transmission electron microscope observation of the alloy ribbon after the heat treatment, it was confirmed that most (almost 100%) consisted of fine crystal grains.

As can be seen from the figure, the temperature change of the magnetic characteristics of the magnetic core of the present invention is small up to 150 ° C., and it can be seen that it has sufficient characteristics as a practical material.

Example 13 Tables 5 to 5 were obtained by the single roll method.
Amorphous alloy ribbons having a width of 5 mm and a thickness of 18 μm having the composition shown in Table 8 were produced, a wound magnetic core having an outer diameter of 19 mm and an inner diameter of 15 mm was produced, and heat treated under the same conditions as in Example 1 at 100 kHz, 2 kG. The core loss and the effective permeability μ _e1K at 1 kHz were measured. The obtained results are shown in Tables 5 to 8.

[0091]

[Table 5] Heat treatment alloy composition core loss of the present invention Effective magnetic permeability (atomic%) W _{2 / 100K} (mW / cc) μ _e1K Fe ₇₁ Cu ₁ Si ₁₅ B ₉ Nb ₃ Ti ₁ 230 98000 Fe ₆₉ Cu ₁ Si ₁₅ B ₉ W ₅ V ₁ 280 62000 Fe ₆₉ Cu ₁ Si ₁₆ B ₈ Mo ₅ Mn ₁ 280 58000 Fe ₆₉ Cu ₁ Si ₁₇ B ₇ Nb ₅ Ru ₁ 250 102000 Fe ₇₁ Cu ₁ Si ₁₄ B ₁₀ Ta ₃ Rh ₁ 290 78000 Fe ₇₂ Cu ₁ Si ₁₄ B ₉ Zr ₃ Pd ₁ 300 52000 Fe _72.5 Cu _0.5 Si ₁₄ B ₉ Hf ₃ Ir ₁ 310 53000 Fe ₇₀ Cu ₂ Si ₁₆ B ₈ Nb ₃ Pt ₁ 270 95000 Fe _70.5 Cu _1.5 Si ₁₅ B ₉ Nb ₅ Au ₁ 250 111000 Fe _71.5 Cu _0.5 Si ₁₅ B ₉ Nb ₃ Zn ₁ 300 88000 Fe _69.5 Cu _1.5 Si ₁₅ B ₉ Nb ₃ Mo ₁ Sn ₁ 270 97000 Fe _68.5 Cu _2.5 Si ₁₅ B ₉ Nb ₃ Ta ₁ Re ₁ 330 99000 Fe ₇₀ Cu ₁ Si ₁₅ B ₉ Nb ₃ Zr ₁ Al ₁ 300 88000 Fe ₇₀ Cu ₁ Si ₁₅ B ₉ Nb ₃ Hf ₁ Sc ₁ 280 86000 Fe ₇₀ Cu ₁ Si ₁₅ B ₉ Hf ₃ Zr ₁ Y ₁ 340 48000 Fe ₇₁ Cu ₁ Si ₁₅ B ₉ Nb ₃ La ₁ 380 29000 Fe ₆₇ Cu ₁ Si ₁₇ B ₉ Mo ₅ Ce ₁ 370 27000

[0092]

[Table 6] Heat treatment alloy composition core loss of the present invention Effective magnetic permeability (atomic%) W _{2 / 100K} (mW / cc) μ _e1K Fe ₆₇ Cu ₁ Si ₁₇ B ₉ W ₅ Pr ₁ 390 23000 Fe ₆₇ Cu ₁ Si ₁₇ B ₉ Ta ₅ Nb ₁ 400 21000 Fe ₆₇ Cu ₁ Si ₁₇ B ₉ Zr ₅ Sm ₁ 360 23000 Fe ₆₇ Cu ₁ Si ₁₆ B ₁₀ Hf ₅ Eu ₁ 370 20000 Fe ₆₈ Cu ₁ Si ₁₈ B ₉ Nb ₃ Gd ₁ 380 21000 Fe ₆₈ Cu ₁ Si ₁₉ B ₈ Nb ₃ Tb ₁ 350 20000 Fe ₇₂ Cu ₁ Si ₁₄ B ₉ Nb ₃ Dy ₁ 370 21000 Fe ₇₂ Cu ₁ Si ₁₄ B ₉ Nb ₃ Ho ₁ 360 20000 Fe ₇₁ Cu ₁ Si ₁₄ B ₉ Nb ₃ Cr ₁ Ti ₁ 250 88000 (Fe _0.95 Co _0.01 ) ₇₂ Cu ₁ Si ₁₄ B ₉ Nb ₃ Cr ₁ 240 85000 (Fe _0.95 Co _0.05 ) ₇₂ Cu ₁ Si ₁₄ B ₉ Ta ₃ Ru ₁ 260 80000 (Fe _0.9 Co _0.1 ) ₇₂ Cu ₁ Si ₁₄ B ₉ Ta ₃ Mn ₁ 270 75000 (Fe _0.99 Ni _0.01 ) ₇₂ Cu ₁ Si ₁₄ B ₉ Ta ₃ Ru ₁ 260 89000 (Fe _0.95 Ni _0.05 ) ₇₁ Cu ₁ Si ₁₄ B ₉ Ta ₃ Cr ₁ Ru ₁ 270 85000 (Fe _0.90 Ni _0.1 ) ₆₈ Cu ₁ Si ₁₅ B ₉ W ₅ Ti ₁ Ru ₁ 290 78000 (Fe _0.95 Co _0.03 Ni _0.02 ) _69.5 Cu ₁ Si _13.5 B ₉ W ₅ Cr ₁ Rh ₁ 270 75000 (Fe _0.98 Co _0.01 Ni _0.01 ) ₆₇ Cu ₁ Si ₁₅ B ₉ W ₅ Ru ₃ 250 72000

[0093]

[Table 7] Heat treatment alloy composition core loss of the present invention Effective permeability (atomic%) W _{2 / 100K} (mW / cc) μ _e1K Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Ni ₃ C ₁ 240 70000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb ₃ Ge ₁ 230 68000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb ₃ P ₁ 250 65000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb ₃ Ga ₁ 250 66000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb ₃ Sb ₁ 300 59000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb ₃ As1 310 63000 Fe ₇₁ Cu ₁ Si ₁₃ B ₈ Mo ₅ C ₂ 320 52000 Fe ₇₀ Cu ₁ Si ₁₄ B ₆ Mo ₃ Cr ₁ C ₅ 330 48000 (Fe _0.95 Co _0.05 ) ₇₀ Cu ₁ Si ₁₃ B ₉ Nb ₅ Al ₁ C ₁ 350 38000 (Fe _0.98 Ni _0.02 ) ₇₀ Cu ₁ Si ₁₃ B ₉ W ₅ V ₁ Ge ₁ 340 39000 Fe _68.5 Cu _1.5 Si ₁₃ B ₉ Nb ₅ Ru ₁ C ₂ 250 88000 Fe ₇₀ Cu ₁ Si ₁₄ B ₈ Ta ₃ Cr ₁ Ru ₂ C ₁ 290 66000 Fe ₇₀ Cu ₁ Si ₁₄ B ₉ Nb ₅ Be ₁ 250 66000 Fe ₆₈ Cu ₁ Si ₁₅ B ₉ Nb ₅ Mn ₁ Be ₁ 250 91000 Fe ₆₉ Cu ₂ Si ₁₄ B ₈ Zr ₅ Rh ₁ In ₁ 280 68000 Fe ₇₁ Cu ₂ Si ₁₃ B ₇ Hf ₅ Au ₁ C ₁ 290 59000 Fe ₆₆ Cu ₁ Si ₁₆ B ₁₀ Mo ₅ Sc ₁ Ge ₁ 280 65000 Fe _67.5 Cu _0.5 Si ₁₄ B ₁₁ Nb ₅ Y ₁ P ₁ 250 77000 Fe ₆₇ Cu ₁ Si ₁₃ B ₁₂ Nb ₅ La ₁ Ga ₁ 400 61000

[0094]

[Table 8] Heat treatment alloy composition core loss of the present invention Effective magnetic permeability (atomic%) W _{2 / 100K} (mW / cc) μ _e1K (Fe _0.95 Ni _0.05 ) ₆₇ Cu ₁ Si ₁₃ B ₉ Nb ₅ Sm ₁ Sb ₁ 410 58000 (Fe _0.92 Co _0.08 ) ₇₀ Cu ₁ Si ₁₃ B ₉ Nb ₅ Zn ₁ As ₁ 380 57000 (Fe _0.96 Ni _0.02 Co _0.02 ) ₇₀ Cu ₁ Si ₁₃ B ₉ Nb ₅ Sn ₁ In ₁ 390 58000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ Mo ₅ Re ₁ C ₂ 330 55000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ Mo ₅ Ce ₁ C ₂ 400 56000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ W ₅ Pr ₁ C ₂ 410 52000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ W ₅ Nd ₁ C ₂ 390 50000 Fe ₆₈ Cu ₁ Si ₁₄ B ₉ Ta ₅ Gd ₁ C ₂ 410 48000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ Nb ₅ Tb ₁ C ₂ 420 50000 Fe ₇₀ Cu ₁ Si ₁₄ B ₈ Nb ₅ Dy ₁ Ge ₁ 410 47000 Fe ₇₂ Cu ₁ Si ₁₃ B ₇ Nb ₅ Pd ₁ Ge ₁ 400 46000 Fe ₇₀ Cu ₁ Si ₁₃ B ₉ Nb ₅ Ir ₁ P ₁ 410 57000 Fe ₇₀ Cu ₁ Si ₁₃ B ₉ Nb ₅ Os ₁ Ga ₁ 250 71000 Fe ₇₁ Cu ₁ Si ₁₄ B ₉ Ta ₃ Cr ₁ C ₁ 280 61000 Fe ₆₇ Cu ₁ Si ₁₅ B ₆ Zr ₅ V ₁ C ₅ 290 58000 Fe ₆₃ Cu ₁ Si ₁₆ B ₅ Hf ₅ Cr ₂ C ₈ 280 57000 Fe ₆₈ Cu ₁ Si ₁₄ B ₉ Mo ₄ Ru ₃ C ₁ 260 51000 Fe ₇₀ Cu ₁ Si ₁₄ B ₉ Mo ₃ Ti ₁ Ru ₁ C ₁ 270 48000 Fe ₆₇ Cu ₁ Si ₁₄ B ₉ Nb ₆ Rh ₂ C ₁ 240 72000

[0095]

According to the present invention, a magnetic core suitable for various transformers, choke coils, saturable reactors, noise filters, etc., having a low core loss, a high magnetic permeability and a small characteristic deterioration, a magnetic core having a high squareness ratio, and a low squareness ratio. Since the magnetic core and the like can be provided, the effect is remarkable.

[Brief description of drawings]

FIG. 1 is an X-ray diffraction pattern of an alloy produced in an intermediate step of producing the magnetic core of the present invention.

FIG. 2 is a transmission electron microscope metallographic photograph of an alloy produced in an intermediate step of producing the magnetic core of the present invention.

FIG. 3 is an X-ray diffraction pattern of an alloy used in the magnetic core of the present invention.

FIG. 4 is a transmission electron microscope metallographic photograph of an alloy used in the magnetic core of the present invention.

FIG. 5 is a diagram showing an example of the shape of a magnetic core according to the present invention.

FIG. 6 is a diagram showing an example of the shape of a magnetic core according to the present invention.

FIG. 7 is a diagram showing an example of the shape of a magnetic core according to the present invention.

FIG. 8 is a diagram showing an example of the shape of a magnetic core according to the present invention.

FIG. 9 is a diagram showing an example of the shape of a magnetic core according to the present invention.

FIG. 10 is a diagram showing an example of a DC BH curve of the magnetic core of the present invention.

FIG. 11 is a graph showing the ΔB dependence of the effective pulse permeability μp of the magnetic core of the present invention.

FIG. 12 is a diagram showing an example of temperature dependence of magnetic characteristics of the magnetic core of the present invention.

FIG. 13 is a diagram showing a relationship between a crystal grain ratio and a core loss.

FIG. 14 is a diagram showing a relationship between a crystal grain ratio and an effective magnetic permeability.

FIG. 15 is a transmission electron microscope metallographic photograph of an alloy having a crystal grain ratio of 0%.

FIG. 16 is a transmission electron microscope metallographic photograph of an alloy having a crystal grain ratio of 12%.

FIG. 17 is a transmission electron microscope metallographic photograph of an alloy having a crystal grain ratio of 47%.

FIG. 18 is a transmission electron microscope metallographic photograph of an alloy having a crystal grain ratio of about 80%.

FIG. 19 is a transmission electron microscope metallographic photograph of an alloy having a crystal grain ratio of about 100%.

Claims (2)

[Claims] 1. A ribbon of a Fe-based soft magnetic alloy, in which crystal grains having a body-centered cubic lattice structure and having an average grain size of 200 angstroms or less measured at least 80% of the structure are wound and laminated. Or a magnetic core formed by adhering to a substrate. 2. The Fe-based soft magnetic alloy contains Cu.
The magnetic core according to claim 1, wherein is mainly present in the peripheral portion of the crystal grains.