JPH1174110A - Laminated magnetic core - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a laminated magnetic core whose iron loss is small at high frequencies and which can be downsized. SOLUTION: A laminated magnetic core 1, 11 having a magnetic core body 4 formed by winding a thin band 3 into a toroidal form or a magnetic core body 13 formed by laminating the thin bands 3 are adopted. The thin band 3 is made of a soft magnetic metal glass alloy in which the temperature difference ΔTx of a superrcooled liquid expressed by ΔTx =Tx -Tg (where Tx is the crystallization start temperature and Tg is the glass transition temperature) is 20 K or more, and in which at least one element selected from Fe, Co and Ni is contained as the main ingredient(s), and in which B and at least one or two or more elements selected from among Zr, Nb, Ta, Hf, Mo, Ti and V are contained.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a laminated magnetic core provided with a soft magnetic metallic glass alloy used for a transformer, a choke coil, a magnetic sensor and the like.

[0002]

2. Description of the Related Art Conventionally, 50% Ni-Fe permalloy core, 80% Ni-Fe permalloy core, and silicon steel have been used as magnetic core materials for transformers, choke coils, magnetic sensors, and the like. However, the magnetic core made of these magnetic materials has a problem that the core loss is relatively large, and the temperature of the magnetic core is drastically increased in a frequency band of several tens of kHz or more, so that it is difficult to use.

Therefore, recently, a magnetic core body formed by winding a ribbon of a Co-based amorphous alloy having a small core loss and a high squareness ratio, or a ribbon of an Fe-based amorphous alloy having a high saturation magnetic flux density and a high maximum magnetic permeability in a toroidal shape. Also, a laminated magnetic core having a magnetic core body formed by laminating punched pieces into a predetermined shape is used for a transformer, a choke coil, a magnetic sensor, and the like.

[0004]

By the way, for example, when the above-mentioned ribbon having a thickness of 20 μm is wound or laminated, three-dimensional space between adjacent ribbons occurs due to unevenness of the surface of the ribbon.
A gap of about μm occurs. The volume occupied by the ribbon relative to the volume of the magnetic core body is referred to as the space factor, and the space factor at this time is calculated as follows: 20 (μm) / (20 + 3 (μm)) × 100 = 87%. There is a problem that the volume of the magnetic core is large and the magnetic core cannot be miniaturized.

[0005] The present invention has been made to solve the above-mentioned problems, and has as its object to provide a laminated magnetic core having a small core loss and capable of being miniaturized.

[0006]

In order to achieve the above object, the present invention employs the following constitution. The laminated magnetic core of the present invention contains one or more elements of Fe, Co, and Ni as main components, and includes Zr, Nb, Ta, Hf, Mo,
One or two or more elements of Ti and V and B, and an excess amount represented by a formula of ΔTx = Tx−Tg (where Tx indicates a crystallization start temperature and Tg indicates a glass transition temperature). A soft magnetic metallic glass alloy ribbon having a temperature interval ΔTx of the cooling liquid of 20K or more is provided with a magnetic core body wound in a toroidal shape. Further, in the present invention, the composition always contains Zr, and ΔTx is 25K.
The features described above may be used. The laminated magnetic core of the present invention is characterized in that it comprises a magnetic core body formed by laminating the above-described soft magnetic metallic glass alloy ribbons.

[0007] The laminated magnetic core of the present invention is the laminated magnetic core described above, wherein the soft magnetic metallic glass alloy has a ΔTx of 60.
K or more, and is represented by the following composition. _{(Fe 1-ab Co a Ni} b) 100-xy M x B y where, 0 ≦ a ≦ 0.29,0 ≦ b ≦ 0.43,5 atomic%
≦ x ≦ 20 atomic%, 10 atomic% ≦ y ≦ 22 atomic%, and M is an element composed of one or more of Zr, Nb, Ta, Hf, Mo, Ti, and V. Further, the present invention is, 0.042 ≦ a ≦ in the _{(Fe 1-ab Co a Ni} b) 100-xy M x B y a composition formula 0.29,0.042
≦ b ≦ 0.43.

Further, the laminated magnetic core of the present invention is the laminated magnetic core described above, wherein the soft magnetic metallic glass alloy is ΔTx
Is not less than 60K and represented by the following composition. _{(Fe 1-ab Co a Ni} b) 100-xyz M x B y T z where, 0 ≦ a ≦ 0.29,0 ≦ b ≦ 0.43,5 atomic%
≦ x ≦ 20 at%, 10 at% ≦ y ≦ 22 at%, 0 at% ≦ z ≦ 5 at%, and M is Zr, Nb, Ta, H
f, Mo, Ti, an element composed of one or more of V, T is Cr, W, Ru, Rh, Pd, Os, I
It is an element composed of one or more of r, Pt, Al, Si, Ge, C, and P. Further, the present invention is, 0.042 ≦ a ≦ 0.29,0.042 ≦ b ≦ in the _{(Fe 1-ab Co a Ni} b) 100-xyz M x B y T z a composition formula
A relationship of 0.43 may be used.

Next, in the laminated magnetic core of the present invention, the element M is represented by (M ' _{1 -c} M " _c ), and M' is one of Zr and Hf.
M "is Nb, Ta, Mo, Ti,
V is an element composed of one or more of V
≤ c ≤ 0.6. Further, in the composition of the soft magnetic metallic glass alloy, c.
May be in the range of 0.2 ≦ c ≦ 0.4, and c may be in the range of 0 ≦ c ≦ 0.2. Further, in the laminated magnetic core of the present invention, in the composition of the soft magnetic metallic glass alloy, a is 0.04.
It may be characterized in that 2 ≦ a ≦ 0.25 and b is 0.042 ≦ b ≦ 0.1. The laminated magnetic core of the present invention may be characterized in that the soft magnetic metallic glass alloy is subjected to a heat treatment at 427 to 627 ° C. Further, 50% or less of the element B may be replaced with C in the composition of the soft magnetic metallic glass alloy.

[0010]

Embodiments of the present invention will be described below with reference to the drawings. The laminated magnetic core according to the present invention is realized in, for example, an annular shape. Such an annular laminated core is formed by manufacturing a soft magnetic metal glass alloy ribbon described later by a liquid quenching method, and then winding the soft magnetic alloy ribbon in a toroidal shape to form a core body, or Press-punching a soft magnetic alloy ribbon to obtain a ring, laminating the required number of rings to form a magnetic core body, and covering these magnetic core bodies with resin, for example, epoxy resin, or enclosing them in a resin case for insulation protection By doing so, a laminated magnetic core is obtained.

Further, in order to realize an EI core type laminated magnetic core, the above-mentioned soft magnetic metallic glass alloy ribbon is stamped into an E type or an I type so as to form an E type flake and an I type flake. After making a plurality of sheets, E-shaped flakes or I
The E-shaped core and the I-shaped core are formed by laminating the mold flakes, and the core is formed by joining them. The EI core type laminated magnetic core can be obtained by covering such a magnetic core body with a required portion by, for example, epoxy resin or enclosing the required portion with a resin case to insulate and protect the required portion.

FIG. 1 shows an example of an annular laminated magnetic core. This laminated magnetic core 1 is made of a resin-made hollow magnetic core main body storage case 2 made of a soft magnetic metallic glass alloy to be described later. A magnetic core body 4 formed by winding a thin ribbon 3 in a toroidal shape is housed. The magnetic core main body storage case 2 is formed preferably using a resin such as a polyacetal resin or a polyethylene terephthalate resin. Further, an adhesive member 5 for stably fixing the magnetic core main body 4 and the magnetic core main body storage case 2 is applied to two places on the bottom surface 2a of the magnetic core main body storage case 2. The number of positions where the adhesive member is applied is preferably in the range of 2 to 4 places. Epoxy resin, silicon rubber, or the like is used as the bonding member 5.

FIG. 2 shows another example of an annular laminated magnetic core. The laminated magnetic core 11 has a hollow annular core core lower case 12 made of a resin and a soft magnetic metallic glass (described later). It is obtained by housing a magnetic core body 13 formed by stacking rings obtained by punching from a thin ribbon 3 made of an alloy, and fitting a magnetic core main body upper cover 14 to a magnetic core main body lower case 12.
The magnetic core main body lower case 12 and the magnetic core main body upper lid 14 are preferably formed using a resin such as a polyacetal resin or a polyethylene terephthalate resin.

Conventionally, Fe-P-
C-based, Fe-P-B-based, Fe-Ni-Si-based compositions are known to cause glass transition,
The temperature width ΔTx of the supercooled liquid region of these alloys is extremely small, so that they cannot be practically formed as metallic glass alloys. On the other hand, the soft magnetic metallic glass alloy according to the present invention has one or more elements of Fe, Co, and Ni as main components, and ΔTx = Tx−Tg (where Tx is a crystallization start temperature. , Tg indicates a glass transition temperature) Since the temperature width ΔTx of the supercooled liquid region represented by the following expression is 20 K or more, and depending on the composition, it shows a remarkable temperature interval of 25 to 60 K or more, molding by slow cooling becomes possible. This makes it possible to produce a relatively thick ribbon or linear shaped body.

In order to increase the space factor, the laminated magnetic cores 1, 11
What is necessary is just to increase the thickness of the ribbon of the amorphous alloy used for the above. As described above, the conventional amorphous alloy has a very small temperature width ΔTx in the supercooled liquid region. Therefore, when a thin ribbon is manufactured by rapidly cooling a molten alloy having a predetermined composition by a liquid quenching method, the soft magnetic property is reduced. In order not to reduce the thickness, the thickness of the ribbon must be 50 μm or less, and there is a limit in improving the space factor. The soft magnetic metallic glass alloy according to the present invention can obtain a ribbon having a thickness of about 100 to 200 μm, and the magnetic core bodies 4 and 13 obtained by winding or laminating such a ribbon are: The space factor is increased, and the size of parts can be reduced. Further, since the specific resistance is high, when a ribbon having the same thickness is used, it is possible to reduce the core loss as compared with a conventional amorphous alloy.

One of the soft magnetic metallic glass alloys according to the present invention contains one or more of Fe, Co, and Ni as main components, and contains Zr, Nb, Ta, Hf, Mo, Ti,
This is realized by a component system in which one or more of V and a predetermined amount of B are added. One of the soft magnetic metallic glass alloy of the present invention, in the general formula can be expressed by _{(Fe 1-ab Co a Ni} b) 100-xy M x B y, in this formula, 0 ≦ a ≦
0.29, 0 ≦ b ≦ 0.43, 5 at% ≦ x ≦ 20 at%, 10 at% ≦ y ≦ 22 at% is preferable,
M is an element composed of one or more of Zr, Nb, Ta, Hf, Mo, Ti, and V. Further, in the above-mentioned component system, the temperature interval ΔTx of the supercooled liquid region represented by the formula of ΔTx = Tx−Tg (where Tx indicates a crystallization start temperature and Tg indicates a glass transition temperature) is 20K or more. Need that. In the above composition system, it is preferable that Zr or Hf is always contained and ΔTx is 25K or more. Further, in the above composition system, it is more preferable that ΔTx is 60K or more. Further, the (Fe
_1-ab Co _a Ni _b ) In the composition formula of _100-xy M _x B _y, it is preferable that 0.042 ≦ a ≦ 0.29 and 0.042 ≦ b ≦ 0.43.

Next, another soft magnetic metallic glass alloy according to the present invention has a general formula of (Fe _{1 -ab} Co _a Ni _b )
Is expressed in _{100-xyz M x B y T} z, in this formula,
0 ≦ a ≦ 0.29, 0 ≦ b ≦ 0.43, 5 atomic% ≦ x ≦ 2
0 atomic%, 10 atomic% ≦ y ≦ 22 atomic%, 0 atomic% ≦ z ≦
M is Zr, Nb, Ta, Hf, Mo,
An element composed of one or more of Ti and V, and T is Cr, W, Ru, Rh, Pd, Os, Ir, Pt, A
It is one or more of l, Si, Ge, C, and P. Further, the present invention relates to the above (Fe _{1 -ab} Co _a N).
i _b) 0.04 in _{100 -xyz} M _x B _y T _z a composition formula
The relationship may be such that 2 ≦ a ≦ 0.29 and 0.042 ≦ b ≦ 0.43.

Next, the element M is represented by (M ' _{1 -c} M " _c ), wherein M' is one or two of Zr and Hf;
M "is an element composed of one or more of Nb, Ta, Mo, Ti, and V, and may be characterized by satisfying 0 ≦ c ≦ 0.6. The characteristic c may be in the range of 0.2 ≦ c ≦ 0.4, and the characteristic c may be in the range of 0 ≦ c ≦ 0.2. 0.042
≦ a ≦ 0.25 and 0.042 ≦ b ≦ 0.1. In the present invention, the soft magnetic metallic glass alloy may be heat-treated at 427 ° C. (700 K) to 627 ° C. (900 K). Those heat-treated at temperatures in this range exhibit high magnetic permeability.

"Composition limitation reason" In the composition system of the present invention,
Fe, Co and Ni, which are main components, are elements responsible for magnetism, and are important for obtaining high saturation magnetic flux density and excellent soft magnetic characteristics. Further, in a component system containing a large amount of Fe, ΔT
x tends to be large, and in a component system containing a large amount of Fe, C
By setting the o content and the Ni content to appropriate values, ΔTx
Can be set to 60K or more. Specifically, 5
In order to reliably obtain ΔTx of 0K to 60K, the value of a indicating the composition ratio of Co is set in the range of 0 ≦ a ≦ 0.29, and the value of b indicating the composition ratio of Ni is set in the range of 0 ≦ b ≦ 0.43. , Δ over 60K
In order to reliably obtain Tx, the value of a indicating the composition ratio of Co is set to the range of 0.042 ≦ a ≦ 0.29, and the value of b indicating the composition ratio of Ni is set to the range of 0.042 ≦ b ≦ 0.43. It is preferable that In order to obtain good soft magnetic properties within the above range, the value of a indicating the composition ratio of Co is set to 0.042.
≦ a ≦ 0.25 is preferable, and in order to obtain a high saturation magnetic flux density, the value of b indicating the composition ratio of Ni is more preferably in the range of 0.042 ≦ b ≦ 0.1. preferable.

M is Zr, Nb, Ta, Hf, Mo, T
It is an element composed of one or more of i and V.
These are effective elements for forming an amorphous phase, and are preferably in the range of 5 atomic% to 20 atomic%. Further, in order to obtain high magnetic properties, the content is more preferably 5 at% or more and 15 at% or less. Among these elements M, Zr and Hf are particularly effective. A part of Zr or Hf can be replaced with an element such as Nb. When the composition ratio c in the case of replacement is in the range of 0 ≦ c ≦ 0.6, a high ΔTx can be obtained. However, in order to make ΔTx 80 or more, the range of 0.2 ≦ c ≦ 0.4 is preferable.

B has a high amorphous forming ability, and is added in the range of 10 to 22 atomic% in the present invention. Outside this range, if B is less than 10 atomic%, ΔTx disappears, which is not preferable.
If it is larger than this, it is not preferable because it becomes brittle. In order to obtain higher amorphous forming ability and better magnetic properties, it is more preferable that the content be 16 atomic% or more and 20 atomic% or less.

In the above composition system, C represented by T
r, W, Ru, Rh, Pd, Os, Ir, Pt, Al,
One or more elements of Si, Ge, C, and P can be added. In the present invention, these elements can be added in a range of 0 atomic% to 5 atomic%. These elements are added mainly for the purpose of improving the corrosion resistance. If the content is out of this range, the soft magnetic properties deteriorate. If the ratio is out of this range, the amorphous forming ability is deteriorated, which is not preferable.

In the method for producing a ribbon 3 of a soft magnetic metallic glass alloy according to the present invention, for example, elemental elemental powders of each component are prepared, and these elemental elementary powders are mixed so as to be within the above-mentioned composition range. This mixed powder is melted in a melting device such as a crucible in an atmosphere of an inert gas such as Ar gas to obtain a molten alloy having a predetermined composition, and the molten alloy is quenched by a single roll method to obtain a soft magnetic metal. A glass alloy ribbon can be obtained. The single-roll method is a method in which a molten metal is sprayed onto a rotating metal roll to quench the molten metal, thereby obtaining a ribbon-shaped metal glass in which the molten metal is cooled.

The above-mentioned laminated magnetic cores 1 and 11 have ΔT _x = T _x −
The temperature interval ΔT of the supercooled liquid represented by the formula of T _g (where T _x indicates the crystallization start temperature and T _g indicates the glass transition temperature)
_x is 20K or more soft magnetic metallic glass alloy ribbon,
Since the core body 4 wound in a toroidal shape or the core body 13 laminated is provided, it is possible to form a laminated core from a thin ribbon having a large thickness, and to occupy the laminated cores 1 and 11. Since the rate can be increased, the core loss can be reduced and the size can be reduced.

The above-mentioned soft magnetic metallic glass alloy has an F
e, one or more of Co, Ni as a main component, and one or more of Zr, Nb, Ta, Hf, Mo, Ti, V, and B, and supercooling Since the temperature interval ΔTx of the liquid can be increased, the laminated cores 1 and 11 can be formed from a thin ribbon having a large thickness, the space factor of the laminated cores 1 and 11 can be improved, and the core loss can be reduced. .

The laminated magnetic cores 1 and 11 of the present invention have a supercooled liquid having a temperature interval ΔTx of 60 K or more and a composition represented by the following formula, have a high magnetic permeability, a small coercive force, Since the magnetic core bodies 4 and 13 made of a soft magnetic metallic glass alloy having a high saturation magnetic flux density and excellent soft magnetic properties are provided, core loss can be reduced. _{(Fe 1-ab Co a Ni} b) 100-xy M x B y where, 0 ≦ a ≦ 0.29,0 ≦ b ≦ 0.43,5 atomic%
≦ x ≦ 20 atomic%, 10 atomic% ≦ y ≦ 22 atomic%, and M is an element composed of one or more of Zr, Nb, Ta, Hf, Mo, Ti, and V. _{Or, (Fe 1-ab Co a} Ni b) 100-xyz M x B y T z where, 0 ≦ a ≦ 0.29,0 ≦ b ≦ 0.43,5 atomic%
≦ x ≦ 20 at%, 10 at% ≦ y ≦ 22 at%, 0 at% ≦ z ≦ 5 at%, and M is Zr, Nb, Ta, H
f, Mo, Ti, an element composed of one or more of V, T is Cr, W, Ru, Rh, Pd, Os, I
It is an element composed of one or more of r, Pt, Al, Si, Ge, C, and P.

[0027]

【Example】

(Example 1) A pure metal of Fe, Co, Ni and Zr and a pure boron crystal were mixed in an Ar gas atmosphere and arc-melted to produce a mother alloy. Next, this mother alloy was melted in a crucible and blown out from a 0.4 mm diameter nozzle at the lower end of the crucible into a copper roll rotating at 40 m / S in an argon gas atmosphere at an injection pressure of 0.39 × 10 ⁵ Pa. By performing the single roll method of quenching, the width is 0.4 to 1 m.
m, a sample of a metallic glass alloy ribbon having a thickness of 13 to 22 μm was produced. The obtained sample was subjected to differential scanning calorimetry (DS
C).

FIG. 3 shows Fe ₆₀ Co ₃ Ni ₇ Zr ₁₀ B, respectively.
_{20, Fe 56 Co 7 Ni 7} Zr 10 B 20, Fe 49 Co 14 Ni 7
3 shows a DSC curve of a metallic glass alloy ribbon sample having a composition of Zr ₁₀ B ₂₀ and Fe ₄₆ Co ₁₇ Ni ₇ Zr ₁₀ B ₂₀ . In each of these samples, it was confirmed that a wide supercooled liquid region was present by increasing the temperature, and it was clarified that crystallization was caused by heating beyond the supercooled liquid region. . The temperature interval ΔTx in the supercooled liquid region is
ΔTx = Tx−Tg, where Tx−T shown in FIG.
The value of g exceeds 60K for any of the samples, and is 64 to 68K.
Is in the range. Substantial equilibrium, indicating a supercooled liquid region, was obtained over a wide range from 596 ° C (869K) to 632 ° C (905K), slightly below the temperature at which crystallization due to the exothermic peak occurred.

FIG. 4 shows (Fe _{1 -ab} Co _a Ni _b ) ₇₀ Zr ₁₀
B is a triangular composition diagram showing the respective content dependence of Fe, Co and Ni to the value of ΔTx (= Tx-Tg) at ₂₀ having a composition system. As is clear from the results shown in FIG. 4, the value of ΔTx exceeds 25K in the entire range of the composition system of (Fe ₁ -ab Co _a Ni _b ) ₇₀ Zr ₁₀ B ₂₀ . Further, regarding the value of Tg, Co is changed from about 7 atomic% to 5%.
It was also clarified that increasing Tg in the range of about 0 atomic% monotonously increases Tg. On the other hand, as shown in FIG. 5, it was found that ΔTx had a large value in a composition system containing a large amount of Fe, and in order to increase ΔTx to 60 K or more, the Co content was 3 atomic% or more and 20 atomic% or less. , N
It is understood that the i content is preferably set to 3 atomic% or more and 30 atomic% or less. Note that (Fe _1-ab Co _a N
_ib ) In the composition formula of ₇₀ Zr ₁₀ B ₂₀ , the Co content is 3
(Fe _1-ab Co _a Ni _b ) is set to 7
Since it is set to 0 atomic%, in order to set the Co composition ratio a to 0.042 or more and the Co content to 20 atomic% or less, the Co composition ratio a becomes 0.29 or less. Similarly, in order to increase the Ni content to 3 atomic% or more, the Ni composition ratio b is set to 0.042.
As described above, the composition ratio b of Ni is 0.43 or less in order to reduce the content to 30 at% or less.

(Example 2) A single pure metal of Fe, Co, Ni and Zr and a pure boron crystal were mixed in an Ar gas atmosphere and arc-melted to form a composition of Fe ₅₆ Co ₇ Ni ₇ Zr ₄ Nb ₆ B ₂₀ . A mother alloy was produced. Next, a sample of a metallic glass alloy ribbon was manufactured by melting this mother alloy in a crucible and performing a single roll method in which an alloy melt was blown out and rapidly cooled by rotating a copper roll in an argon gas atmosphere. . At this time, by appropriately adjusting the nozzle diameter of the crucible, the distance (gap) between the nozzle tip and the roll surface, the number of rotations of the roll, the injection pressure, the atmospheric pressure, and the like, the alloy ribbon having a plate thickness of 20 to 195 μm can be formed. Obtained. Each sample was analyzed by X-ray diffraction. FIG. 5 shows the results. From FIG. 5, 2θ = 38 to
It has a halo pattern at 52 °, indicating that it has an amorphous single phase structure.

Example 3 The atomic composition ratio was Fe ₅₆ Co ₇
A sample of a metallic glass alloy ribbon was produced in the same manner as in Example 1 except that Ni ₇ Zr _10-x Nb _x B ₂₀ (x = 0, 2, 4, 6, 8, _{10 at} %). . Next, the obtained sample is
The heat treatment was performed at a temperature of 527 ° C. (800 K) for 5 minutes. FIG. 6 shows the saturation magnetic flux density (Bs) of the manufactured sample,
The Nb content dependence of coercive force (Hc), permeability (μe) at 1 kHz, and magnetostriction (λs) is shown. Saturation magnetic flux density (B
s) decreases with the addition of Nb in both the quenched state and the sample after the heat treatment, and the sample without Nb is 0.9.
(T) As described above, about 0.75 for a sample containing 2 atomic% of Nb.
(T). The values of the magnetic permeability (μe) of the sample in the quenched state are 5031 for the sample not containing Nb, 2228 for the sample containing 2 atomic% of Nb, and 10 atomic% for Nb.
In the sample containing, it decreased to 906. However, by performing the heat treatment, the magnetic permeability (μe) is remarkably improved. In particular, in a sample containing 2 atomic% of Nb, a magnetic permeability (μe) of about 25000 can be obtained. Regarding the coercive force (Hc), in the sample in the quenched state, the sample containing no Nb and the sample containing 2 atomic% of Nb were both 50 A / m (=
0.625 Oe). In particular, the sample having Nb of 2 atomic% or less shows a very good value of 5 A / m (= 0.0625 Oe). When heat treatment is applied, Nb becomes 4
An excellent coercive force (Hc) can be obtained even in a sample containing at least atomic%. As described above, in this alloy sample, in order to obtain good soft magnetic characteristics, Nb
It is understood that the range of 0 to 2 atomic% is more preferable. Therefore, it is possible to obtain a laminated magnetic core having a soft magnetic metallic glass alloy having a high saturation magnetic flux density, a low coercive force, and a high magnetic permeability. And a transformer excellent in power transmission efficiency can be obtained.

Example 4 In the same manner as in Example 1, Fe
Thin strips of metallic glass alloy having various compositions were obtained with a composition of ₅₆ Co ₇ Ni ₇ Zr ₄ Nb ₆ B ₂₀ . Next, each of the above-mentioned ribbons is punched out in a ring shape, the required number of layers are laminated, and epoxy or polyimide resin is impregnated between the layers to insulate and fix each layer. 12m
An annular laminated magnetic core having a diameter of 4 m, an inner diameter of 4 mm, and a thickness of 5 mm was prepared.

FIG. 7 shows the relationship between the thickness of the ribbon of the laminated magnetic core obtained as described above and the space factor. The measurement of the space factor was obtained by observing the cross section of the laminated magnetic core with a microscope. As shown in FIG. 7, the space factor increases with an increase in the plate thickness. When the space factor exceeds 100 μm, the space factor becomes substantially constant at 97% or more. The laminated magnetic core made of the soft magnetic metallic glass alloy according to the present invention has a small core loss because the soft magnetic characteristics are not deteriorated as described above even if the thickness of the ribbon exceeds 100 μm. A magnetic core is obtained. On the other hand, a conventionally known amorphous alloy of Fe ₇₈ Si ₉ B ₁₃ has a plate thickness of only about 20 μm.
The space factor in this case is as low as 87%. Conventional amorphous alloys have a small temperature width ΔTx in the supercooled liquid region. Therefore, when manufacturing a thin ribbon by rapidly cooling a molten alloy having a predetermined composition by a liquid quenching method, in order to prevent soft magnetic characteristics from deteriorating. The thickness of the ribbon must be 50 μm or less. If the thickness exceeds this thickness, the soft magnetic properties deteriorate.
An increase in space factor and an improvement in soft magnetic characteristics cannot be realized at the same time, and a laminated core with small core loss cannot be obtained.

(Example 5) In the same manner as in Example 1, a Fe ₅₆ Co ₇ Ni ₇ Zr ₈ Nb ₂ B ₂₀ layer having a thickness of 20 μm and a thickness of 20
After obtaining thin ribbons of a metallic glass alloy having a composition of Fe ₆₂ Co ₇ Ni ₇ Zr ₈ Nb ₂ B ₁₄ μm, they were punched and laminated in a ring shape as in Example 4, and these thin ribbons were 527 ° C. 80
(K) for 5 minutes. Next, a polyimide core was impregnated from these ribbons in the same manner as in Example 4 to obtain a laminated magnetic core. 8 and 9 show the relationship between the operating magnetic flux density (Bm) of these laminated magnetic cores and the core loss. Further, the results of the core loss of the laminated core manufactured using silicon steel (6.5% of silicon) are shown in FIGS. 8 and 9 simultaneously as comparative examples. 8 and 9 show the results of three samples subjected to the same treatment. 8 and 9 that the laminated core according to the present invention has a smaller core loss than the laminated core of the comparative example.

It should be noted that the present invention is not limited by the above-described examples, and it is needless to say that the composition, the manufacturing method, the heat treatment conditions, the shape, and the like can be variously modified.

[0036]

As described in detail above, the laminated magnetic core of the present invention has the following relationship _: ΔT _x = T _x −T _g (where T _x indicates the crystallization start temperature and T _g indicates the glass transition temperature). Since the soft magnetic metallic glass alloy ribbon whose temperature interval ΔT _x of the supercooled liquid represented by the formula is 20K or more is provided with a magnetic core body wound in a toroidal shape or a laminated magnetic core body. In addition, the laminated magnetic core can be formed from a thin ribbon having a large thickness, and the space factor can be increased. Therefore, the core loss can be reduced and the size can be reduced.

Further, the soft magnetic metallic glass alloy of the present invention comprises:
One or more of Fe, Co, and Ni as main components, and one or more of Zr, Nb, Ta, Hf, Mo, Ti, and V, and B, and supercooling Since the temperature interval ΔTx of the liquid can be increased, a laminated magnetic core can be formed from a thin ribbon having a large thickness.
The space factor of the laminated magnetic core can be improved, and the core loss can be reduced.

The laminated core of the present invention has a temperature interval ΔTx of the supercooled liquid of 60 K or more, a composition represented by the following formula, a high magnetic permeability, a small coercive force, and a low saturation magnetic flux density. Since the magnetic core body made of a soft magnetic metallic glass alloy having high soft magnetic properties and excellent soft magnetic properties is provided, core loss can be reduced. _{(Fe 1-ab Co a Ni} b) 100-xy M x B y where, 0 ≦ a ≦ 0.29,0 ≦ b ≦ 0.43,5 atomic%
≦ x ≦ 20 atomic%, 10 atomic% ≦ y ≦ 22 atomic%, and M is an element composed of one or more of Zr, Nb, Ta, Hf, Mo, Ti, and V. _{Or, (Fe 1-ab Co a} Ni b) 100-xyz M x B y T z where, 0 ≦ a ≦ 0.29,0 ≦ b ≦ 0.43,5 atomic%
≦ x ≦ 20 at%, 10 at% ≦ y ≦ 22 at%, 0 at% ≦ z ≦ 5 at%, and M is Zr, Nb, Ta, H
f, Mo, Ti, an element composed of one or more of V, T is Cr, W, Ru, Rh, Pd, Os, I
It is an element composed of one or more of r, Pt, Al, Si, Ge, C, and P.

[Brief description of the drawings]

FIG. 1 is an exploded view showing a laminated magnetic core according to an embodiment of the present invention.

FIG. 2 is an exploded view showing a laminated magnetic core according to an embodiment of the present invention.

FIG. 3 Fe ₆₀ Co ₃ Ni ₇ Zr ₁₀ B ₂₀ , Fe ₅₆ Co ₇
Ni ₇ Zr ₁₀ B ₂₀ , Fe ₄₉ Co ₁₄ Ni ₇ Zr ₁₀ B ₂₀ , Fe
Is a diagram showing a _{46 Co 17 Ni 7 Zr 10 B} 20 becomes DSC curve of glassy alloy ribbon samples of each composition.

FIG. 4 is a triangular composition diagram showing dependency of the contents of Fe, Co, and Ni on the value of ΔTx (= Tx−Tg) in a composition system of (Fe _1-ab Co _a Ni _b ) ₇₀ M ₁₀ B ₂₀ It is.

FIG. 5 is a diagram showing X-ray diffraction patterns at various plate thicknesses of a quenched ribbon having a composition of Fe ₅₆ Co ₇ Ni ₇ Zr ₄ Nb ₆ B ₂₀ .

FIG. 6: Fe ₅₆ Co ₇ Ni ₇ Zr _10-x Nb _x B ₂₀ (x =
Nb content dependence of saturation magnetic flux density (Bs), coercive force (Hc), permeability at 1 kHz (μe), and magnetostriction (λs) of a sample having a composition of 0, 2, 4, 6, 8, and 10 atomic%) FIG.

FIG. 7 is a diagram showing the relationship between the thickness of the metallic glass alloy according to the present invention and the space factor.

FIG. 8 is a diagram showing a relationship between core loss and Bm of a laminated magnetic core manufactured from a ribbon having a composition of Fe ₅₆ Co ₇ Ni ₇ Zr ₈ Nb ₂ B ₂₀ .

FIG. 9 is a diagram showing a relationship between core loss and Bm of a laminated magnetic core manufactured from a ribbon having a composition of Fe ₆₂ Co ₇ Ni ₇ Zr ₈ Nb ₂ B ₁₄ .

[Explanation of symbols]

 Reference Signs List 1 laminated magnetic core 2 magnetic core main body storage case 3 thin ribbon 4 magnetic core main body 5 adhesive member

 ──────────────────────────────────────────────────続 き Continued on the front page (72) Inventor Akihiro Makino Alps Electric Co., Ltd., 1-7 Yukitani Otsuka-cho, Ota-ku, Tokyo (72) Inventor Akihisa Inoue 35 Kawamoto Moto Hasekura, Aoba-ku, Sendai, Miyagi Prefecture, Japan House 11-806

Claims (4)

[Claims] 1. One or two of Fe, Co, and Ni
With at least three or more elements as main components, Zr, Nb, Ta, Hf,
One or more elements of Mo, Ti, V and B
And a soft magnetic metallic glass alloy having a temperature interval ΔTx of a supercooled liquid represented by a formula of ΔTx = Tx−Tg (where Tx represents a crystallization start temperature and Tg represents a glass transition temperature) of 20K or more. Wherein the thin ribbon comprises a magnetic core body wound in a toroidal shape. 2. A laminated magnetic core comprising a magnetic core main body formed by laminating thin ribbons of the soft magnetic metallic glass alloy according to claim 1. 3. The laminated magnetic core according to claim 1, wherein the soft magnetic metallic glass alloy has a ΔTx of 6
A laminated magnetic core having a composition of 0K or more and represented by the following composition. _{(Fe 1-ab Co a Ni} b) 100-xy M x B y where, 0 ≦ a ≦ 0.29,0 ≦ b ≦ 0.43,5 atomic%
≦ x ≦ 20 atomic%, 10 atomic% ≦ y ≦ 22 atomic%, and M is an element composed of one or more of Zr, Nb, Ta, Hf, Mo, Ti, and V. 4. The laminated magnetic core according to claim 1, wherein the soft magnetic metallic glass alloy has a ΔTx of 6
A laminated magnetic core having a composition of 0K or more and represented by the following composition. _{(Fe 1-ab Co a Ni} b) 100-xyz M x B y T z where, 0 ≦ a ≦ 0.29,0 ≦ b ≦ 0.43,5 atomic%
≦ x ≦ 20 at%, 10 at% ≦ y ≦ 22 at%, 0 at% ≦ z ≦ 5 at%, and M is Zr, Nb, Ta, H
f, Mo, Ti, an element composed of one or more of V, T is Cr, W, Ru, Rh, Pd, Os, I
It is an element composed of one or more of r, Pt, Al, Si, Ge, C, and P.