JP2713373B2 - Magnetic core - Google Patents

Description

Description: BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to various transformers and choses.
For coil, saturable reactor, noise filter, etc.
The present invention relates to a magnetic core having excellent soft magnetic characteristics. [0002] Conventionally, various transformers, choke coils,
For magnetic cores such as saturable reactors and noise filters
Blower with advantages such as high electrical resistance and low eddy current loss
Unit core, silicon with high saturation magnetic flux density and relatively low iron loss
Steel core, medium saturation flux density and relatively high frequency characteristics
Permalloy core and the like were used. However, the ferrite core has a saturation magnetic flux density.
It is difficult to downsize the magnetic core because of its low temperature and poor temperature characteristics.
There are drawbacks that are difficult. Silicon core has high saturation magnetic flux density
However, soft magnetic properties, especially permeability and core loss at high frequencies
Is inferior. Permalloy core has high frequency magnetic characteristics.
Although it is superior to stainless steel, it has poor impact resistance.
And high frequency magnetic properties are easily degraded by impact
was there. In recent years, these disadvantages can be improved to some extent.
As the magnetic core formed of amorphous alloy attracts attention
Has been put to practical use. [0005] Amorphous alloys are roughly classified into Fe-based and Co-based
The Fe-based amorphous alloy has a high saturation magnetic flux density,
Has the advantage that it is cheaper than Co-based,
Core loss at higher frequencies than Co-based amorphous alloys
And the magnetic permeability is low. In addition, Fe-based amorphous alloy
Gold has a remarkably large magnetostriction, causing the core to beat or impregnate
Disadvantages are that the properties are significantly degraded when
is there. On the other hand, Co-based amorphous alloys
Although the loss is small and the permeability is high, the core loss and permeability
The disadvantage is that the change over time is large and the saturation magnetic flux density is not sufficient.
is there. In addition, expensive Co is used as the main raw material,
The profit is inevitable. Under these circumstances, the Fe-based amorphous alloy
Various proposals have been made. Japanese Patent Publication No. 60-17019, 74-
84 at% Fe, 8 to 24 at% B and up to 16 at% Si
And at least one of C of 3 atomic% or less
Having at least 85% of its structure an amorphous metal substrate
And discontinuous throughout the amorphous metal body
It has crystalline particles that are distributed successively.
The crystalline particle group has an average particle size of 0.05-1 μm and an average of 1-10 μm
It has a distance between particles, and the particle group has a total of 0.01 to 0.3
Iron-based boron-containing material occupying the average volume fraction
A magnetic amorphous alloy is disclosed. Crystalline grains of this alloy
Is a discontinuous distribution α acting on the domain wall pinning point.
-(Fe, Si) particles. Japanese Patent Application Laid-Open No. 60-52557 discloses Fe _a Cu _b B _c Si _d (T
75 ≦ a ≦ 85,0 <b ≦ 1.5,10 ≦ c ≦ 20, d ≦ 10 and c + d ≦ 3
No. 0) is disclosed. This
Amorphous alloy is below the crystallization temperature and above the Curie temperature
Heat treatment. [0009] The above-mentioned Japanese Patent Publication No. 60-17019
Core composed of Fe-based soft magnetic alloy is discontinuous crystalline particles
The core loss is reduced by the presence of
Is still large, especially because of its large magnetostriction
Core loss and magnetic permeability
There is a problem that causes a significant deterioration of the rate.
Characteristics are not available. On the other hand, the Fe-based amorphous material disclosed in the above-mentioned JP-A-60-52557
The core loss of the magnetic core of the alloy is reduced due to the effect of Cu content.
However, a magnetic core using the above-described Fe-based amorphous alloy containing crystal particles is
Not equally satisfied. Furthermore, core loss changes with time, transparency
There is a problem that the magnetic susceptibility is not sufficient. Therefore, an object of the present invention is to provide a low core loss and low permeability.
Providing a magnetic core with high magnetic susceptibility and small deterioration of characteristics due to magnetostriction
The porpose is to do. [0012] In view of the above-mentioned object, intensive studies have been made.
As a result, the inventors have found the following. [0013] Fe _73.4 Cu ₁ Nb _3.1 Si _13.4 B _9.1 Having the composition of
Amorphous ribbon made from molten metal using single roll method
However, under various heat treatment conditions, the ratio of fine crystal grains was different.
(Nos. 1 to 5) were prepared. The percentage of crystal grains in this sample
Effective permeability (μ _e1KHz ), Core loss (W _{2 / 100K} : 100KHz, Bm 2K
(In G). The results are shown in FIGS.
Show. In addition, transmission electron micrographs (magnification 300,000) of Samples 1 to 5
These are shown in FIGS. Note that the value is calculated by the line segment method described later.
Of the fine grains and the grain size measured at the largest dimension
The average (angstrom) is as follows. [0014] As is clear from FIGS. 13 and 14 described above, the fine crystal
When the percentage of grains exceeds 80%, the effective magnetic permeability is significantly improved.
And the core loss is reduced. X-ray diffraction and transmission
As a result of analysis using a scanning electron microscope, fine crystal grains
Was determined to be Fe having a body-centered cubic lattice structure with solid solution. The present invention
Is based on the above findings, and the body-centered cubic lattice
The average of the particle size measured at the largest dimension has 200 angst
Fe with less than loam grains accounting for at least 80% of the structure
Winding, laminating, or adhering to a substrate of base soft magnetic alloy
A magnetic core formed by being formed. As an alloy used for the magnetic core according to the present invention,
A preferred composition has the general formula: (Fe _1-a M _a ) _100-xyz- α _- β _- γCu _x Si _y B _z M'αM "βXγ (Hara
(Where 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
Element, M "is V, Cr, Mn, Al, white metal element, Sc, Y, rare earth element, Au, Z
n, Sn, at least one element selected from the group consisting of Re,
X is a small number selected from the group consisting of C, Ge, P, Ga, Sb, In, As, Be
A, x, y, z, α, β and γ are at least one element
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. )
It has a composition represented by Fe-based soft magnetism used in the magnetic core according to the present invention
For alloys, quench the amorphous alloy of the specified composition from the molten metal.
And heating to form fine crystal grains
Heat treatment step. In the alloy used in the present invention, Cu
Is contained in the range of 0.1 to 3 atomic%. Less than 0.1 atomic%
Otherwise, the effect of lowering core loss and increasing magnetic permeability due to the addition of Cu
There is almost no, whereas if it is more than 3 atomic%, core loss
They may be larger than those not added,
The rate also deteriorates. Particularly preferred Cu content in the present invention
x is 0.5 to 2 atomic%, and in this range, the core loss is particularly
small. Causes of Cu core loss reduction and permeability increase
Although it is not clear, it is considered as follows. The interaction parameter between Cu and Fe is positive,
Because of its low solid solubility and tendency to separate,
When gold is heated, Fe atoms or Cu atoms come together
In order to form clusters, composition fluctuations occur. this
As a result, there are many regions that are easy to partially crystallize,
Fine crystal grains are generated. This crystal is mainly composed of Fe
And there is almost no solid solubility of Fe and Cu.
During the crystallization, Cu is extruded around the fine crystal grains,
The Cu concentration around the crystal grains increases. This causes the grains to grow
It is considered difficult. As described above, a large number of crystal nuclei are obtained by adding Cu.
And the crystal grains are difficult to grow.
It is thought that this effect is due to Nb, Ta, W, Mo, Zr, Hf, Ti
It is thought that the presence of the above-mentioned method becomes particularly remarkable. When Nb, Ta, W, Mo, Zr, Hf, Ti, etc. do not exist
Is not very fine. Nb, Ta, Zr, Hf, Mo are special
Is effective, but when Nb is added among these elements,
In particular, the crystal grains tend to be thin, and the soft magnetic properties are also excellent.
Is obtained. Also, a fine crystalline phase mainly composed of Fe is generated.
Therefore, the magnetostriction is smaller than that of an Fe-based amorphous alloy,
-Soft magnetic properties are also reduced due to the reduced magnetic anisotropy due to strain.
It is considered the reason for improvement. In the Fe-based soft magnetic alloy according to the magnetic core of the present invention,
Is, for example, a composition formula: Fe _bal Cu ₁ Nb _Three B _Five Si _17.5 Represented by
Like alloys, those with negative magnetostriction or zero or almost no magnetostriction
Almost zero items are included. When Cu is not added, the crystal grains are refined.
Is difficult to form and the compound phase is easy to form.
Characteristics are easily degraded. V, Cr, Mn, Al, white metal element, Sc, Y, rare earth element,
Elements such as Au, Zn, Sn, and Re improve corrosion resistance, improve magnetic properties,
This has the effect of distortion adjustment. Its content is at most
Less than 10 atomic%. Significant when the content exceeds 10 atomic%
This is because it causes a decrease in the saturation magnetic flux density.
The content is less than 8 atomic%. Of these, Ru, Rh, Pd, Os, Ir, Pt, Au, Cr, V
From alloys added with at least one element selected from
In particular, a magnetic core having excellent corrosion resistance and wear resistance is obtained. In the present invention, C, Ge, P, Ga, Sb, In, Be, As
At least one element selected from the group consisting of 10 atoms
% Or less. These elements are effective for amorphization
It is an element that is not
Aids crystallinity and is effective for magnetostriction and Curie temperature adjustment
There is fruit. Si and B are fine grains of the alloy according to the present invention.
It is an element particularly useful for thinning. Fe-based soft magnetism according to the present invention
The alloy is preferably amorphous once due to the effect of the addition of Si and B.
After forming the alloy, it is possible to form fine crystal grains by heat treatment.
And is obtained by Reasons for limiting the y and z contents of Si and B
Means that y is 30 atom% or less, z is 25 atom% or less, and y + z is 35 atom
%, The saturation magnetic flux density of the alloy may be significantly reduced.
This is because that. When the amount of other amorphous forming elements is small
If y + z is in the range of 10 to 35 atomic%,
Amorphization at an intermediate stage is easy. However, below
M 'also acts as an amorphous forming element, and therefore contains B and Si.
Yes is not required. In the present invention, M ′ is obtained by adding complex with Cu.
Has the effect of refining crystal grains
Selected from the group consisting of Nb, W, Ta, Zr, Hf, Ti, and Mo.
It is at least one element. Nb etc. set the crystallization temperature of the alloy
Has the effect of raising, but forms clusters and crystallizes
Deposits due to interaction with Cu, which has a temperature lowering effect
It is considered that the crystal grains to be produced become fine. M 'content
The amount α is 0.1-30 atomic%, and if it is less than 0.1 atomic%, crystal grains
Insufficient effect of miniaturization, while exceeding 30 atomic%
This causes a significant decrease in the saturation magnetic flux density. Preferred M 'content
α is 2 to 8 atomic%. Note that Nb is the surface of the magnetic characteristics as M '
Is most preferred. In addition, Co-based high permeability material
It has a high magnetic permeability equivalent to that of. The balance is substantially Fe-excluding impurities.
But part of Fe is replaced by component M (Co and / or Ni)
You can also. The content a of M is 0 ≦ a <0.5,
Preferably, 0 ≦ a ≦ 0.3. If a exceeds 0.3,
This is because the loss may increase. Improvement of corrosion resistance and magnetic properties by adding M "
Or an effect of adjusting magnetostriction is obtained. M "is 10 atomic%
If it exceeds, the saturation magnetic flux density decreases significantly. Among the alloys according to the present invention, in particular, 0 ≦ a ≦ 0.3,0.
5 ≦ x ≦ 2,10 ≦ y ≦ 25,3 ≦ z ≦ 12,18 ≦ y + z ≦ 28,2 ≦ α ≦ 8
High permeability and low core loss
I'm sorry. The Fe-based soft magnetic alloy according to the present invention has a small structure.
At least 80% of the fine particles have a body-centered cubic lattice structure.
Consists of crystal grains. The crystal grains are mainly composed of α-Fe,
And B etc. are considered to be in solid solution. These grains are 200 o
Having a very small average particle size of less than
And are uniformly distributed in the alloy structure. alloy
The portion of the structure other than the fine crystal grains is mainly amorphous.
Even if the ratio of fine crystal grains is substantially 100%,
The bright magnetic core shows sufficiently excellent magnetic properties. In the present invention, the proportion of fine crystal grains is
This is a value obtained by the line segment method. This line segment method is common
Any line segment (length L) drawn in the tissue photograph
The sum of the lengths (L1, L2, L3, ... Ln) of each traversing crystal grain (L1 + L2 + L3
+… Ln), and dividing this by L,
It seeks a match. The ratio of crystal grains is about 80% or less.
As the number increases, the crystal grains occupy almost the entire structure.
You can see, but even in this case, there is some amorphous phase
Conceivable. This is because, as shown in FIG.
The outer periphery is blurred in the micrograph, but this is amorphous
Because it is thought to be due to the presence of
is there. Based on this assumption, the percentage of the outer periphery that appears blurry
From this, it can be seen that the proportion of the amorphous phase is approximately. Like this crystal
If the ratio of grains is large, it is not possible to express the ratio as an exact number.
It is difficult. In the present invention, inevitable impurities such as N, O, S, etc.
Substances are contained to such an extent that the desired properties do not deteriorate.
It is considered the same as the alloy composition used for the magnetic core of the present invention.
Of course you can. Next, a method of manufacturing a magnetic core according to the present invention will be described.
I do. First, a single roll method, a twin
A ribbon-shaped amorphous material by a known liquid quenching method such as a roll method
Form an alloy. Usually manufactured by single roll method
The thickness of the amorphous alloy ribbon is about 3 to 100 μm.
Magnetic core whose thickness is 25μm or less is used at high frequencies
It is particularly suitable for use as a thin ribbon. This amorphous alloy may contain a crystalline phase.
However, fine grains are uniformly generated by subsequent heat treatment
For this purpose, it is desirable to be amorphous. The amorphous ribbon is wound and punched before heat treatment.
And processed into a predetermined shape by etching etc. to form a magnetic core
Is more desirable. The reason is that the ribbon is processed at the amorphous stage.
Good workability, but once crystallized, workability is significantly reduced
This is because there are many cases. However, winding after heat treatment
Manufacturing a magnetic core by performing processing such as
Is also possible. The heat treatment is performed on an amorphous alloy processed into a predetermined shape.
Place the ribbon in a vacuum or in an inert gas atmosphere of hydrogen, nitrogen, Ar, etc.
Hold for a certain period of time in the atmosphere or the atmosphere. Heat treatment
The temperature and time are determined by the shape of the core made of amorphous alloy ribbon.
Depends on shape, size, composition, etc.
Desirably, the temperature is about 5 minutes to 24 hours at 00 ° C. Heat treatment temperature is 450 ℃
If the amount is less than the above, crystallization hardly occurs, and the heat treatment takes a long time.
Too light. If the temperature is higher than 700 ° C, coarse crystal grains are formed
Or the formation of non-uniform morphological grains.
As a result, fine crystal grains cannot be obtained uniformly. Ma
Heat treatment time is less than 5 minutes
It is difficult to keep the body at a uniform temperature, and the magnetic properties vary.
Easy to stick, longer than 24 hours only lowers productivity
Excessive grain growth and formation of grains with non-uniform morphology
As a result, the magnetic properties tend to deteriorate. Preferred heat treatment
The conditions are set considering practicality and uniform temperature control.
5 minutes to 6 hours at 500 ° C to 650 ° C. The heat treatment atmosphere is inert gas such as Ar, nitrogen, hydrogen, etc.
Although a gas atmosphere or a reducing atmosphere is desirable, acid
A oxidizing atmosphere may be used. Cooling is performed by air cooling, furnace cooling, etc.
It can be carried out. In some cases, multi-step heat treatment
You can do it too. During heat treatment, current is applied to the core material.
Or applying a high-frequency magnetic field to generate heat in the magnetic core
The heart can also be heat treated. Heat treatment is performed in a magnetic field such as direct current or alternating current.
You can also. Furthermore, it is used for this core by heat treatment in a magnetic field.
To improve the properties by causing magnetic anisotropy in the alloy
I can do it. Magnetic field may be applied throughout the heat treatment
Does not need to be applied for the entire period.
Sufficient effects can be obtained at lower temperatures. The present invention will be described in more detail with reference to the following examples.
However, the present invention is not limited to these. Example 1 1% Cu, 16.5% Si, B6
%, Nb3% and the balance substantially consisting of Fe,
A ribbon with a width of 20 mm and a thickness of 18 μm was manufactured by the single roll method.
Was. Figure 1 shows the result of X-ray diffraction of this ribbon.
A halo pattern typical of such an amorphous alloy was obtained.
Fig. 2 shows a transmission electron micrograph (300,000 times) of this ribbon.
Shown in The ribbon obtained as is clear from FIGS. 1 and 2
It was almost completely amorphous. Next, from this amorphous ribbon
Punch a ring with an outer diameter of 13 mm and an inner diameter of 10 mm, and use argon gas
Heat treatment was performed at 530 ° C. for 1 hour in an atmosphere. After heat treatment
The X-ray diffraction pattern of Bonn is a crystal peak as shown in FIG.
Was observed. Figure 4 shows the transmitted electrons of the ribbon after this heat treatment.
It is a microscope (300,000 ×), and most of the structure after heat treatment (approximately
It was found that about 100%) consisted of fine crystal grains. Conclusion
The average grain size of the crystal grains was about 100 angstroms. X-ray diffraction pattern and transmission electron microscope
Analysis shows that these grains have a body-centered cubic structure
Was estimated to be Fe. Further, when the concentration distribution of Cu in the structure was observed,
At this time, it was confirmed that Cu was mainly present around the crystal grains.
Was. Next, ten heat-treated ring-shaped thin ribbons were prepared.
Laminated and placed in a phenolic resin core case, magnetic properties
Was measured. As a result, Bs = 12 kG, Br / Bs = 62%, Hc = 0.012 Oe,
Effective permeability μ at 1kHz _e1K = 76000,100kHz, Bm 2kG
Core loss W _{2 / 100K} = 250mW / cc. Bs
Is higher than the Co-based amorphous core, and the effective permeability μ _e1K ,
A loss W _{2 / 100K} Is superior to Co-based amorphous magnetic cores
Characteristics. Next, this core is impregnated with an epoxy resin,
The properties were measured. Bs = 12kG, Br / Bs = 50%, Hc = 0.014 Oe, μ
_e1K = 42000, W _{2 / 100K} = 380 mW / cc, and
Remarkably less deterioration of characteristics compared to base amorphous core
Was confirmed. To clarify the reason, the amorphous state and the
And the saturation magnetostriction constant λs of the ribbon under the same heat treatment conditions.
Was. As a result, λs = + 20.8 × 10 ^-6 ,Heat treatment
Later λs = + 1.3 × 10 ^-6 And the magnetostriction of the magnetic core of the present invention is
It was confirmed that it was extremely small. (Example 2) 5 m in width having the composition shown in Table 1
m, 18μm thick amorphous alloy ribbon produced by single roll method
And wound in a toroidal shape with an outer diameter of 19 mm and an inner diameter of 15 mm.
And The winding method is such that the surface that has contacted the roll and solidified
Was. Use an adhesive at the beginning and a polyimide tape at the end.
Specified. MgO powder is applied to the surface of the ribbon by electrophoresis.
Then, interlayer insulation was performed. Next, this wound core is _Two gas
In the atmosphere, increase the crystallization temperature at a heating rate of about 10 ° C / min.
Rise to a temperature about 50 ° C higher, hold for 1 hour, and
Heat treatment to cool to room temperature at cooling rate
The magnetic core of the present invention made of an alloy having a structure was obtained. The structure was observed in the same manner as in Example 1.
All alloys in Table 1 have an average particle size of 100 to 150 Å
Fine grains composed of ROHM's body-centered cubic structure
Share (almost 100%), and Cu
It was confirmed that it was present around the crystal grains. Next, this magnetic core was attached to silicone oil.
After that, a case made of phenol resin filled with silicon grease
And the lid was fixed with an adhesive. Next, the winding core
Flow BH curve, effective permeability μ at 1 kHz _e1K ,frequency
Core loss W at several 100kHz, Bm 2kG _{2 / 100K} Measure
Was. The saturation magnetostriction λs was also measured. Table 1 shows the obtained results.
Shown in The saturation magnetic flux density Bs of the alloy of the present invention exceeds 10 kG.
And higher soft magnetic properties than Co-based amorphous alloys
It can be seen that properties equal to or better than Co-based amorphous
Call In addition, a product with small magnetostriction and almost zero magnetostriction can be obtained.
You. [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 _Three 12.4 0.013 68000 300 +1.8 Fe ₇₄ Cu _1.5 Si _13.5 B ₉ Nb _Two 12.6 0.015 76000 230 +2.0 Fe ₇₉ Cu _1.0 Si ₈ B ₉ Nb _Three 14.6 0.056 21000 470 +1.8 Fe _74.5 Cu _1.0 Si _13.5 B ₆ Nb _Five 11.6 0.020 42000 350 +1.5 Fe ₇₇ Cu _1.0 Si _Ten B ₉ Nb _Three 14.3 0.025 48000 430 +1.6 Fe _73.5 Cu _1.0 Si _17.5 B _Five Ta _Three 10.5 0.015 42000 380 -0.3 Fe ₇₁ Cu _1.5 Si _13.5 B ₉ Mo _Five 11.2 0.012 68000 280 +1.9 Light Fe ₇₄ Cu _1.0 Si ₁₄ B ₈ W _Three 12.1 0.022 74000 250 +1.7 Fe ₇₃ Cu _2.0 Si _13.5 B _8.5 Hf _Three 11.6 0.028 29000 350 +2.0 Fe _74.5 Cu _1.0 Si _13.5 B ₉ Ta _Two 12.8 0.018 33000 480 +1.8 Example Fe ₇₂ Cu _1.0 Si ₁₄ B ₈ Zr _Five 11.7 0.030 28000 380 +2.0 Fe _71.5 Cu _1.0 Si _13.5 B ₉ Ti _Five 11.3 0.038 28000 480 +1.8 Fe ₇₃ Cu _1.5 Si _13.5 B ₉ Mo _Three 12.1 0.014 69000 250 +2.8 Fe _73.5 Cu _1.0 Si _13.5 B ₉ Ta _Three 11.4 0.017 43000 330 +1.9 Fe ₇₁ Cu _1.0 Si ₁₃ B _Ten W _Five 10.0 0.023 68000 320 +2.5 Secondary Fe ₇₈ Si ₉ B ₁₃ Amorphous 15.6 0.03 5000 3300 +27 _70.3 Fe _4.7 Si _Fifteen B _Ten Amorphous 8.0 0.006 8500 350 〜0 Example Fe _84.2 Si _9.6 Al _6.2 (wt%) 11.0 0.02 10000 − 00 (Example 3) Width 5 mm, thickness of composition shown in Table 2
An 18μm amorphous alloy ribbon was prepared by the single roll method.
The surface solidified by contact with
Wound in a toroidal shape with an outer diameter of 19 mm and an inner diameter of 15 mm
Then, a wound magnetic core was produced. At the beginning of the volume, irradiate laser light
Part of the winding is fixed and the end of the winding is fixed with metal tape.
Specified. Next, the wound core is placed in an Ar gas atmosphere for about 20 minutes.
Up to about 50 ℃ higher than the crystallization temperature at a heating rate of ℃ / min
Raise the temperature, hold for 1 hour, and cool to room temperature at a cooling rate of about 10 ° C / min.
Alloy with ultra-fine grain structure after cooling heat treatment
Thus, a magnetic core of the present invention was obtained. The tissue observation was performed in the same manner as in Example 1.
As a result, all of the alloys in Table 2 had an average particle size of 100 to 150.
Angstrom body-centered cubic fine grains
Most of the organization (almost 100%) and Cu
Was mainly present around the crystal grains. Next, the DC BH curve of the wound core, 1 kHz
Effective permeability μ at _e1K , Frequency 100kHz, Bm 2kG
Core loss W _{2 / 100K} And the alloy's saturation magnetostriction λs
Was. Table 2 shows the obtained results. Saturated magnetism of the core of the present invention
The bundle density Bs is the same as that of a normal Co-based amorphous alloy or 80 wt% Ni
Higher than Maloy, μ _e1K , Hc, W _{2 / 100K} Etc. are Co-based amorphous
Soft magnetic material with low magnetostriction and characteristics equivalent to or better than
The characteristics of the magnetic core of the present invention are excellent.
You can see that it is. [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 _Three 12.3 0.018 32000 280 +4.6 (Fe _0.93 Ni _0.07 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb _Three 12.1 0.023 18000 480 +4.8 (Fe _0.905 Ni _0.095 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb _Three 11.8 0.020 16000 540 +5.0 (Fe _0.986 Co _0.014 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb _Three 12.6 0.011 82000 280 +4.0 (Fe _0.959 Co _0.041 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb _Three 13.0 0.015 54000 400 +4.2 (Fe _0.93 Co _0.07 ) _73.5 Cu ₁ Si _13.5 B ₉ Nb _Three 13.2 0.020 27000 500 +4.8 Fe _71.5 Cu ₁ Si _15.5 B ₇ Nb _Five 10.7 0.012 85000 230 +2.8 Fe _71.5 Cu ₁ Si _17.5 B _Five Nb _Five 10.2 0.010 80000 280 +2.0 Fe _71.5 Cu ₁ Si _19.5 B _Three Nb _Five 9.2 0.065 8000 820 +1.6 Fe _70.5 Cu ₁ Si _20.5 B _Five Nb _Three 10.8 0.027 23000 530 〜0 Fe _75.5 Cu ₁ Si _13.5 B ₇ Nb _Three 13.3 0.011 84000 250 +1.5 Fe ₈₇ Cu ₁ B _Five Zr ₇ 15.5 0.044 20000 570 +0.9 Fe ₉₀ Cu ₁ B _Two Hf ₇ 16.0 0.037 18000 540 〜0 Fe ₈₈ Cu ₁ Si _Two B _Three Zr ₇ 15.0 0.025 28000 540 〜0 Fe ₉₀ Cu ₁ B _Two Zr ₇ 16.5 0.03 17000 580 〜0 Fe ₈₆ Cu ₁ B ₆ Zr ₇ 15.2 0.04 48000 520 to 0 (Example 4) Fe ₇₉ Cu ₁ Nb _Three Si ₈ B ₉ (Atomic%)
Creates an amorphous alloy ribbon with a composition of 50 mm width and 18 μm thickness
And photo-etched to the E-shaped shape shown in FIG.
went. Next, SiO _Two Crystal after forming the film
Heat for 1 hour at 550 ° C, which is higher than the
Processing was performed. Next, this is laminated between the layers via an epoxy resin.
Then, a laminated magnetic core having the shape shown in FIG. 6 was obtained. Next, this core is
Combined EE core and 100kHz, Bm 2kG loss
It was measured. The core loss is 400mW / cc and the Co-based amorphous
It showed a value comparable to the magnetic core. (Example 5) The composition shown in Table 3 had a width of 5 mm and a thickness of 5 mm.
An 18μm-thick amorphous alloy ribbon was produced by the single roll method.
A wound core having a diameter of 12 mm and an outer diameter of 18 mm was produced. Next, this wound core
Heat treated at 50 ° C higher than crystallization temperature in air
The magnetic core of the present invention made of an alloy having a crystal grain structure was obtained. This
Analysis of the thin ribbon surface of the magnetic core formed a silicon oxide layer
It was confirmed that it was. Next, this magnetic core is attached to a case made of phenol resin.
And the effective permeability μ at 1 kHz _e1K , 100kHz, 2kG
Core loss W _{2 / 100K} Was measured. After the measurement, put the epoxy resin into the case and vacuum
After impregnation and curing at 120 ° C, μe1K, W2 / 100K
It was measured. Table 3 shows the obtained results. Also for comparison
The results of a study on a conventional amorphous wound core
Also shown. The Co-based amorphous core has a high μe1K and
The loss W2 / 100K is also low, and its characteristics deteriorate much after impregnation.
However, the saturation magnetic flux density Bs is lower than that of the magnetic core of the present invention. Fe group
The morphus core has both μe1K and core loss due to impregnation.
Deteriorates. On the other hand, the magnetic core of the present invention has a Bs of 10 kG or more.
Excellent characteristics with little deterioration of magnetic properties after impregnation
It can be seen that [Table 3] Composition before impregnation and after impregnation (at%) Bs W _{2 / 100K} W _{2 / 100K} (kG) μ _e1K (mW / cc) μ _e1K (mW / cc) Fe _70.5 Cu ₁ Nb _Three Si _20.5 B _Five 10.8 23000 530 20000 550 pcs Fe _73.5 Cu ₁ Nb _Three Si _17.5 B _Five 11.8 50000 350 45000 370 Fe _71.5 Cu ₁ Nb _Five Si _17.5 B _Five 10.2 80000 280 56000 340 Fe ₇₃ Cu _1.5 Mo _Three Si _13.5 B ₉ 12.1 69000 250 48000 320 Fe _73.5 Cu ₁ Ta _Three Si _17.5 B _Five 10.5 42000 380 38000 410 Akira Fe ₇₃ Cu _Two Hf _Three Si _13.5 B _8.5 11.6 29000 350 20000 390 Fe ₇₂ Cu ₁ Zr _Five Si ₁₄ B ₈ 11.7 28000 480 19000 550 Example Fe ₇₄ Cu ₁ W _Three Si ₁₄ B ₈ 12.1 74000 250 59000 330 Fe ₇₇ Cu ₁ Nb _Three Si _Ten B ₉ 14.3 48000 430 32000 550 Fe _74.5 Cu ₁ Nb _Three Si _13.5 B ₈ 11.6 42000 350 38000 380 Secondary Fe _74.5 Nb _Three 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 _Four Mo _1.5 Si _16.5 B ₁₁ 5.5 88000 350 65000 380 Amorphous (Example 6) Fe having a width of 25 mm and a thickness of 20 μm _73.5 C
u ₁ Nb _Three Si _13.5 B ₉ Fabrication of amorphous alloy ribbon by single roll method
did. Next, the ribbon and the glass tape are stacked and wound.
Then, create a wound core with an outer diameter of 150 mm and an inner diameter of 100 mm as shown in Fig. 7.
Made. Next, a glass-coated copper wire is wound around the core.
Current through the copper wire and apply a magnetic field of about 10 Oe in the direction of the magnetic path.
While N _Two Heat treatment at 550 ° C for 1 hour in a gas atmosphere
Was. The heating rate is 10 ° C./min, and the cooling rate is 2.5 ° C./mi.
n. The DC BH curve, core loss,
The large magnetic permeability was measured. As a result, the saturation magnetic flux density Bs was 12.4 kG,
The ratio Br / Bs is 90%, the coercive force Hc is 0.005 Oe, and the maximum magnetic permeability μm is 1
Core loss W at 800000,100kHz, 2kG _{2 / 100K} Is 800mW / c
The characteristic of c was obtained. Example 7 Fe _71.5 Cu ₁ Nb _Five Si _13.5 B ₉ Composition of
To produce an amorphous alloy ribbon having a width of 3 mm and a thickness of 15 μm,
A wound core having an outer diameter of 8 mm and an inner diameter of 4 mm was produced. Next, this core
Place the furnace in a furnace heated to 610 ° C while flowing nitrogen gas and keep it for 1 hour.
After the heat treatment, it was taken out of the furnace and air-cooled. From the obtained alloy having a fine grain structure,
Powder core with epoxy resin to a thickness of about 0.5 mm
BH curve and effective permeability μ at 1 kHz
_e1K , 100kHz, core loss W at 2kG _{2 / 100K} Was measured.
Table 4 shows the obtained results. For comparison, Fe _76.5 Cr ₁ Si _13.5 B ₉ Amorpha
This shows the characteristics when a steel alloy core is coated. The core of the present invention is a conventional Fe-based amorphous core.
Less magnetostriction makes it less susceptible to distortion.
It can be seen that excellent characteristics are exhibited even after the coating. More
The core of the present invention coated with 90% humidity and 30 ° C
Magnetic properties were measured again after one month in a thermostat, but changed
Was not found. Also on concrete from a height of 1m
No change in magnetic properties after 10 drops
Was done. [Table 4] Composition Bs Hc μ _e1K W _{2 / 100K} (at%) (kG) (Oe) (mW / cc) Fe of the present invention _71.5 Cu ₁ Nb _Five Si _13.5 B ₉ 11.3 0.012 72000 320 Conventional Fe _76.5 Cr ₁ Si _13.5 B ₉ Amorphous 14.3 0.11 1400 2400 (Example 8) Fe _73.5 Cu ₁ Ta _Three Si _13.5 B ₉ Composition of
Amorphous alloy ribbon 20 mm wide and 20 μm thick with a single row
It was prepared by a metal method. Next, apply the Tyrannopolymer to this ribbon.
After applying the main solution and drying at 200 ° C,
Prepare a wound core of the shape shown _Two Heat treatment in atmosphere
did. Heat treatment is performed at a rate of 10 ° C / min to 570 ° C for 1 hour
After the holding, it was cooled to room temperature at a cooling rate of 5 ° C./min. Next
Wrap Kapton tape around the magnetic core as shown in Fig. 9.
The core loss at 100kHz, 2kG was measured. 430mW / cc
A value comparable to that of a Co-based amorphous magnetic core was obtained. Measurement
After observing the ribbon with a transmission electron microscope,
Part (almost 100%) average of about 100 angstroms
It was confirmed that the particles consisted of crystal grains having a particle size. Example 9 Fe _74.5 Cu ₁ Nb _Two Si _13.5 B ₉ Composition of
Amorphous alloy ribbon with width of 20mm and thickness of 20μm
And punched out with a press to an outside diameter of 13 mm and an inside diameter of 10 mm and kept at 530 ° C
N _Two Empty for 1 hour in a furnace with gas atmosphere
A heat treatment for cooling was performed. Next, this ring-shaped ribbon is
Interchange with ceramic ring of 13mm, inner diameter 10mm, thickness 40μm
Twenty layers were laminated on each other to produce the magnetic core of the present invention. Effective magnetic permeability μ at 1 kHz _e1K Is 76000,100
A core loss of 250 mW / cc at 2 kHz and 2 kHz was obtained. After measurement
When the structure was observed with a transmission electron microscope,
Most (almost 100%) are about 100 Angstrom flat
It was confirmed that the particles consisted of crystal grains having a uniform particle size. Example 10 Fe _71.5 Cu ₁ Nb _Five Si _15.5 B ₇ Pair of
Amorphous alloy ribbon with width of 25mm and thickness of 25μm
And SiO _Two -TiO _Two -Based metal alkoxide partially hydrolyzed sol
Apply a solution mixed with ceramic powder on one side and dry
And wrap it around a stainless steel ring with an outer diameter of 80 mm and an inner diameter of 78 mm.
A wound core having an inner diameter of 80 mm and an outer diameter of 120 mm was manufactured. Then this
A glass-coated copper wire is wound around the magnetic core, and an alternating current is
And a maximum of 10 Oe in the direction of the magnetic path.
After heating at 590 ° C for 1 hour,
At a cooling rate of 5 ° C./min. Next, a 1 mm thick stainless steel
A band made of Les was fixed. Measure the magnetic properties of this core
As a result, the saturation magnetic flux density Bs was 10.6 kG, and the squareness ratio Br / Bs was 8
Core loss at 0%, coercive force Hc is 0.015Oe, 100kHz, 2kG
However, a characteristic of 500 mW / cc was obtained. High saturation magnetic flux density, corner
Magnetic form for pulse compression due to high form ratio and low core loss
Ideal for switches and the like. After the measurement,
From the observation of the structure, most of the tissue (almost 10
0%) from grains with an average grain size of about 120 angstroms
It was confirmed that it became. (Example 11) Fe _73.5 Cu ₁ Nb _Three Si _13.5 B ₉ Pair of
Production of amorphous alloy ribbon with width of 15 mm and thickness of 15 μm
After applying alumina powder to the surface, the outer diameter is 30 mm, the inner diameter is 18
5,000 mm in a direction perpendicular to the magnetic path
Heating up to 550 ° C at a heating rate of 20 ° C / min while applying a field
After holding for 1 hour, cool to 250 ° C at a cooling rate of 2 ° C / min
Stop applying the magnetic field afterwards and take it out of the furnace and wipe it with nitrogen gas.
Cooled to room temperature. After heat treatment, bake the core
BH curve and pulse transmittance μp
Was measured for the operating magnetic flux density ΔB. The results obtained
These are shown in FIGS. In addition, transmission electron microscope and X-ray
As a result of diffraction, 80% or more of the magnetic core after heat treatment is fine crystal grains.
It was confirmed that the The magnetic core of the present invention has a high saturation magnetic flux density and a low squareness ratio.
Operating flux with effective pulse permeability μp with high magnetic permeability
Mn-Zn ferrite or Co-based amorph
Much better than ass core. Therefore, the inverter
For transformers and cores for common mode chokes.
You. (Example 12) 5 mm wide by the single roll method
18μm thick Fe _73.5 Cu ₁ Nb _Three Si _13.5 B ₉ Create amorphous alloy ribbon
The core was wound around an outer diameter of 19 mm and an inner diameter of 15 mm. One of the manufactured cores was heated to 550 ° C.
Into the furnace, hold it for 1 hour, remove it from the furnace
The other is to wind a glass-coated copper wire around this copper wire
Apply a current and apply a magnetic field of 10 Oe in the
After holding for 1 hour in a furnace heated to ℃, cool down to 280 ℃ at 5 ℃ / min
It was cooled at a speed and taken out of the furnace and air-cooled to room temperature. FIG. 12 shows the temperature characteristics of the magnetic core after the heat treatment.
You. The results of transmission electron microscope observation of the alloy ribbon after heat treatment
Most of the fruits (nearly 100%) can be composed of fine grains
confirmed. As can be seen from the figure, the magnetic characteristics of the magnetic core of the present invention
Temperature change is as small as 150 ° C, which is sufficient for practical use.
It can be seen that it has the property. (Example 13) Table 5
An amorphous alloy ribbon having a composition shown in Table 8 and a width of 5 mm and a thickness of 18 μm was prepared.
Manufacturing, winding core with outer diameter 19 mm, inner diameter 15 mm
Heat treatment under the same conditions as in 1 and core at 100kHz, 2kG
Loss, effective permeability μ at 1 kHz _e1K Was measured. Get
The results obtained are shown in Tables 5 to 8. Table 5 Heat treatment alloy composition of the present invention Core loss Effective magnetic permeability (atomic%) W _{2 / 100K} (mW / cc) μ _e1K Fe ₇₁ Cu ₁ Si _Fifteen B ₉ Nb _Three Ti ₁ 230 98000 Fe ₆₉ Cu ₁ Si _Fifteen B ₉ W _Five V ₁ 280 62000 Fe ₆₉ Cu ₁ Si ₁₆ B ₈ Mo _Five Mn ₁ 280 58000 Fe ₆₉ Cu ₁ Si ₁₇ B ₇ Nb _Five Ru ₁ 250 102000 Fe ₇₁ Cu ₁ Si ₁₄ B _Ten Ta _Three Rh ₁ 290 78000 Fe ₇₂ Cu ₁ Si ₁₄ B ₉ Zr _Three Pd ₁ 300 52000 Fe _72.5 Cu _0.5 Si ₁₄ B ₉ Hf _Three Ir ₁ 310 53000 Fe ₇₀ Cu _Two Si ₁₆ B ₈ Nb _Three Pt ₁ 270 95000 Fe _70.5 Cu _1.5 Si _Fifteen B ₉ Nb _Five Au ₁ 250 111000 Fe _71.5 Cu _0.5 Si _Fifteen B ₉ Nb _Three Zn ₁ 300 88000 Fe _69.5 Cu _1.5 Si _Fifteen B ₉ Nb _Three Mo ₁ Sn ₁ 270 97000 Fe _68.5 Cu _2.5 Si _Fifteen B ₉ Nb _Three Ta ₁ Re ₁ 330 99000 Fe ₇₀ Cu ₁ Si _Fifteen B ₉ Nb _Three Zr ₁ Al ₁ 300 88000 Fe ₇₀ Cu ₁ Si _Fifteen B ₉ Nb _Three Hf ₁ Sc ₁ 280 86000 Fe ₇₀ Cu ₁ Si _Fifteen B ₉ Hf _Three Zr ₁ Y ₁ 340 48000 Fe ₇₁ Cu ₁ Si _Fifteen B ₉ Nb _Three La ₁ 380 29000 Fe ₆₇ Cu ₁ Si ₁₇ B ₉ Mo _Five Ce ₁ 370 27000 [Table 6] Heat treatment alloy composition of the present invention Core loss Effective magnetic permeability (atomic%) W _{2 / 100K} (mW / cc) μ _e1K Fe ₆₇ Cu ₁ Si ₁₇ B ₉ W _Five Pr ₁ 390 23000 Fe ₆₇ Cu ₁ Si ₁₇ B ₉ Ta _Five Nb ₁ 400 21000 Fe ₆₇ Cu ₁ Si ₁₇ B ₉ Zr _Five Sm ₁ 360 23000 Fe ₆₇ Cu ₁ Si ₁₆ B _Ten Hf _Five EU ₁ 370 20000 Fe ₆₈ Cu ₁ Si ₁₈ B ₉ Nb _Three Gd ₁ 380 21000 Fe ₆₈ Cu ₁ Si ₁₉ B ₈ Nb _Three Tb ₁ 350 20000 Fe ₇₂ Cu ₁ Si ₁₄ B ₉ Nb _Three Dy ₁ 370 21000 Fe ₇₂ Cu ₁ Si ₁₄ B ₉ Nb _Three Ho ₁ 360 20000 Fe ₇₁ Cu ₁ Si ₁₄ B ₉ Nb _Three Cr ₁ Ti ₁ 250 88000 (Fe _0.95 Co _0.01 ) ₇₂ Cu ₁ Si ₁₄ B ₉ Nb _Three Cr ₁ 240 85000 (Fe _0.95 Co _0.05 ) ₇₂ Cu ₁ Si ₁₄ B ₉ Ta _Three Ru ₁ 260 80000 (Fe _0.9 Co _0.1 ) ₇₂ Cu ₁ Si ₁₄ B ₉ Ta _Three Mn ₁ 270 75000 (Fe _0.99 Ni _0.01 ) ₇₂ Cu ₁ Si ₁₄ B ₉ Ta _Three Ru ₁ 260 89000 (Fe _0.95 Ni _0.05 ) ₇₁ Cu ₁ Si ₁₄ B ₉ Ta _Three Cr ₁ Ru ₁ 270 85000 (Fe _0.90 Ni _0.1 ) ₆₈ Cu ₁ Si _Fifteen B ₉ W _Five 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 _Five Cr ₁ Rh ₁ 270 75000 (Fe _0.98 Co _0.01 Ni _0.01 ) ₆₇ Cu ₁ Si _Fifteen B ₉ W _Five Ru _Three Table 7 Heat treatment alloy composition of the present invention Core loss Effective magnetic permeability (atomic%) W _{2 / 100K} (mW / cc) μ _e1K Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Ni _Three C ₁ 240 70000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb _Three Ge ₁ 230 68000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb _Three P ₁ 250 65000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb _Three Ga ₁ 250 66000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb _Three Sb ₁ 300 59000 Fe ₇₃ Cu ₁ Si ₁₃ B ₉ Nb _Three As1 310 63000 Fe ₇₁ Cu ₁ Si ₁₃ B ₈ Mo _Five C _Two 320 52000 Fe ₇₀ Cu ₁ Si ₁₄ B ₆ Mo _Three Cr ₁ C _Five 330 48000 (Fe _0.95 Co _0.05 ) ₇₀ Cu ₁ Si ₁₃ B ₉ Nb _Five Al ₁ C ₁ 350 38000 (Fe _0.98 Ni _0.02 ) ₇₀ Cu ₁ Si ₁₃ B ₉ W _Five V ₁ Ge ₁ 340 39000 Fe _68.5 Cu _1.5 Si ₁₃ B ₉ Nb _Five Ru ₁ C _Two 250 88000 Fe ₇₀ Cu ₁ Si ₁₄ B ₈ Ta _Three Cr ₁ Ru _Two C ₁ 290 66000 Fe ₇₀ Cu ₁ Si ₁₄ B ₉ Nb _Five Be ₁ 250 66000 Fe ₆₈ Cu ₁ Si _Fifteen B ₉ Nb _Five Mn ₁ Be ₁ 250 91000 Fe ₆₉ Cu _Two Si ₁₄ B ₈ Zr _Five Rh ₁ In ₁ 280 68000 Fe ₇₁ Cu _Two Si ₁₃ B ₇ Hf _Five Au ₁ C ₁ 290 59000 Fe ₆₆ Cu ₁ Si ₁₆ B _Ten Mo _Five Sc ₁ Ge ₁ 280 65000 Fe _67.5 Cu _0.5 Si ₁₄ B ₁₁ Nb _Five Y ₁ P ₁ 250 77000 Fe ₆₇ Cu ₁ Si ₁₃ B ₁₂ Nb _Five La ₁ Ga ₁ [Table 8] Heat treatment alloy composition of the present invention Core loss 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 _Five Sm ₁ Sb ₁ 410 58000 (Fe _0.92 Co _0.08 ) ₇₀ Cu ₁ Si ₁₃ B ₉ Nb _Five Zn ₁ As ₁ 380 57000 (Fe _0.96 Ni _0.02 Co _0.02 ) ₇₀ Cu ₁ Si ₁₃ B ₉ Nb _Five Sn ₁ In ₁ 390 58000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ Mo _Five Re ₁ C _Two 330 55000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ Mo _Five Ce ₁ C _Two 400 56000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ W _Five Pr ₁ C _Two 410 52000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ W _Five Nd ₁ C _Two 390 50000 Fe ₆₈ Cu ₁ Si ₁₄ B ₉ Ta _Five Gd ₁ C _Two 410 48000 Fe ₆₉ Cu ₁ Si ₁₃ B ₉ Nb _Five Tb ₁ C _Two 420 50000 Fe ₇₀ Cu ₁ Si ₁₄ B ₈ Nb _Five Dy ₁ Ge ₁ 410 47000 Fe ₇₂ Cu ₁ Si ₁₃ B ₇ Nb _Five Pd ₁ Ge ₁ 400 46000 Fe ₇₀ Cu ₁ Si ₁₃ B ₉ Nb _Five Ir ₁ P ₁ 410 57000 Fe ₇₀ Cu ₁ Si ₁₃ B ₉ Nb _Five Os ₁ Ga ₁ 250 71000 Fe ₇₁ Cu ₁ Si ₁₄ B ₉ Ta _Three Cr ₁ C ₁ 280 61000 Fe ₆₇ Cu ₁ Si _Fifteen B ₆ Zr _Five V ₁ C _Five 290 58000 Fe ₆₃ Cu ₁ Si ₁₆ B _Five Hf _Five Cr _Two C ₈ 280 57000 Fe ₆₈ Cu ₁ Si ₁₄ B ₉ Mo _Four Ru _Three C ₁ 260 51000 Fe ₇₀ Cu ₁ Si ₁₄ B ₉ Mo _Three Ti ₁ Ru ₁ C ₁ 270 48000 Fe ₆₇ Cu ₁ Si ₁₄ B ₉ Nb ₆ Rh _Two C ₁ According to the present invention, various transformers and chokes are provided.
Suitable for coils, saturable reactors, noise filters, etc.
Magnet with low core loss, high magnetic permeability, and small characteristic deterioration
Providing cores, magnetic cores with a high squareness ratio, magnetic cores with a low squareness ratio, etc.
The effect is remarkable.

BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is an X-ray diffraction pattern of an alloy produced in an intermediate stage of manufacturing the magnetic core of the present invention. FIG. 2 is a transmission electron microscope microstructure photograph of an alloy produced in an intermediate stage of manufacturing the magnetic core of the present invention. FIG. 3 is an X-ray diffraction pattern of an alloy used for the magnetic core of the present invention. FIG. 4 is a transmission electron microscope microstructure photograph of an alloy used for the magnetic core of the present invention. FIG. 5 is a diagram showing an example of a 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 a 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 diagram showing the ΔB dependency of the effective pulse permeability μp of the magnetic core of the present invention. FIG. 12 is a diagram showing an example of the temperature dependence of the 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 microstructure photograph of an alloy having a crystal grain ratio of 0%. FIG. 16 is a transmission electron microscope microstructure photograph of an alloy having a crystal grain ratio of 12%. FIG. 17 is a transmission electron microscope microstructure photograph of an alloy having a crystal grain ratio of 47%. FIG. 18 is a transmission electron microscope microstructure photograph of an alloy having a crystal grain ratio of about 80%. FIG. 19 is a transmission electron microscope microstructure photograph of an alloy having a crystal grain ratio of about 100%.

Claims (1)

(57) [Claims] Winding a ribbon of an Fe-based soft magnetic alloy in which at least 80% of the structure has an average grain size of 200 Å or less in the average grain size measured at the largest dimension having a body-centered cubic lattice structure,
A magnetic core formed by laminating or attaching to a substrate. 2. The magnetic core according to claim 1, wherein the Fe-based soft magnetic alloy contains Cu, and the Cu is mainly present around the crystal grains.