KR100311922B1 - Bulk magnetic core and laminated magnetic core - Google Patents

Abstract

△ T _x = T _x -T _g at temperature intervals of the super-cooling liquid represented by the formula (where, T _x is the crystallization initiating temperature, T _g represents the glass transition temperature) (△ T _x) is more than 20 ℃, Fe, Sintering the powder of soft magnetic metal glass alloy containing one or two or more elements of Zr, Nb, Ta, Hf, Mo, Ti, V and Co containing Ni as main components A thin magnetic core and a thin magnetic metal glass alloy thin ribbon having a magnetic core body formed by cooling and solidifying the molten magnetic body formed by flowing the molten metal or the molten metal glass alloy into a predetermined mold, and wound in a toroidal shape. Laminated magnetic core comprising a magnetic core body made of, or a magnetic core body formed by laminating the thin ribbon

Description

Bulk magnetic core and laminated magnetic core {BULK MAGNETIC CORE AND LAMINATED MAGNETIC CORE}

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to bulk magnetic cores and laminated magnetic cores having soft magnetic metal glass alloys used in transformers, choke coils, magnetic sensors and the like.

Conventionally, 50% Ni-Fe permalloy magnetic core, 80% Ni-Fe permalloy magnetic core, and silicon steel have been used as magnetic core materials, such as a transformer, a choke coil, and a magnetic sensor.

However, the magnetic core made of these magnetic materials has a problem in that the core loss in the high frequency band is particularly large, and the temperature rise of the magnetic core is severe in the frequency band of several 10 Hz or more, which makes it difficult to use.

Therefore, recently, a thin core of Co-based amorphous alloy having a small core loss and a high square ratio, or a thin ribbon of Fe-based amorphous alloy having a high saturation magnetic flux density and a maximum permeability is wound in a toroidal shape, or a predetermined core body. The laminated magnetic core provided with the magnetic core body which laminates the thing blanked in the shape of is used.

However, when winding or laminating said thin ribbons, the gap of about 3 micrometers arises between adjacent thin ribbons because of the unevenness | corrugation of a thin ribbon surface.

If the volume occupied by the bakbak with respect to the volume of the core body is called the drip rate, and when the drip rate is calculated,

20 (μm) / (20 + 3 (μm)) × 100 = 87%

As a result, the volume of the gap occupied by the magnetic core body was large, and there was a problem that the magnetic core could not be miniaturized.

As described above, in the magnetic core formed by laminating amorphous thin ribbons, there is a problem that the core loss increases because the magnetic flux of leakage into the gap between the thin ribbons is large.

In addition, there has been developed a method of sintering the raw material powder obtained by pulverizing the thin ribbon and solidifying it into a bulk shape. However, since the raw material powder must be sintered at a relatively low temperature so that the raw material powder does not crystallize during sintering, a high density magnetic core cannot be obtained. There was a problem that the core loss would increase.

This invention is made | formed in order to solve the said subject, Comprising: It aims at providing a core bulk with a core core.

Moreover, this invention was made | formed in order to solve the said subject, and an object of this invention is to provide the laminated magnetic core which is small in core loss and which can be miniaturized.

1 is an exploded view showing the bulk magnetic core of the present invention.

Fig. 2 is a cross-sectional view showing the main part structure of an example of the discharge plasma sintering apparatus used for producing the bulk magnetic core of the present invention.

3 is a view showing an example of a bulk current waveform applied to the raw material powder in the discharge plasma sintering apparatus.

4 is an exploded view showing the laminated magnetic core of the present invention.

5 is an exploded view showing the laminated magnetic core of the present invention.

6 is 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 ₄₆ Co ₁₇ Ni ₇ Zr ₁₀ B ₂₀ It is a figure which shows the DSC curve of a metal glass alloy thin sample.

Fig. 7 shows the dependence of the content of Fe, Co and Ni on the value of ΔT _x (= T _x -T _g ) in the composition system (Fe _1-a-b Co _a Ni _b ) ₇₀ Zr ₁₀ B ₂₀ . The triangular composition diagram shown.

FIG. 8 is a diagram showing an X-ray diffraction pattern at various plate thicknesses of a quench strip of Fe ₅₆ Co ₇ Ni ₇ Zr ₄ Nb ₆ B ₂₀ .

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

10 is a view showing a core core of a bulk magnetic core manufactured from a magnetic core body having a composition of Fe ₅₆ Co ₇ Ni ₇ Zr ₈ Nb ₂ B ₂₀ .

Fig. 11 is a diagram showing the relationship between the plate thickness and the droplet rate of the metal glass alloy according to the present invention.

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

FIG. 13 is a view showing a relationship between core loss and Bm of a laminated magnetic core manufactured with a thin ribbon having a composition of Fe ₆₂ Co ₇ Ni ₇ Zr ₈ Nb ₂ B _14. FIG.

Explanation of symbols on the main parts of the drawings

1: bulk magnetic core 2, 22: storage case

3, 4, 13, 24, 33: magnetic core 4, 25: adhesive member

11: die 12: phase punch

13: lower punch 14, 15: punch electrode

16: raw material powder 17: thermocouple

21, 31: laminated core 23: bakdae

In order to achieve the above object, the first invention adopts the following configuration.

The bulk magnetic core of the present invention contains one or two or more elements in Fe, Co, and Ni as a main component, and contains one or two or more elements and Z in Zr, Nb, Ta, Hf, Mo, Ti, and V. The temperature interval (ΔT _x ) of the supercooled liquid represented by ΔT _x = T _x -T _g (wherein T _x represents the crystallization start temperature and T _g represents the glass transition temperature) is 20 ° C. or more. A magnetic core body is formed by sintering a powder of a magnetic metal glass alloy.

The bulk magnetic core according to the first aspect of the invention is the bulk magnetic core described above, wherein the soft magnetic metal glass alloy powder has a magnetic core body in which the powder of the soft magnetic metal glass alloy is heated and sintered at a heating rate of 10 ° C./min or more by the discharge plasma sintering method. do.

Further, in the first invention, it must contain a Zr or Hf with respect to the composition, △ T _x is even not less than 25 ℃.

Further, the bulk magnetic core of the first invention includes a magnetic core body in which the molten metal of the soft magnetic metal glass alloy described above is cooled and solidified.

The bulk magnetic core of the first aspect of the invention is the bulk magnetic core of the preceding description, wherein the soft magnetic metal glass alloy has a ΔT _x of 50 ° C. or more and is represented by the following composition.

(Fe _1-a-b Co _a Ni _b ) _100-x-y 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 Zr, Nb, Ta, Hf, Mo, Ti, V It is an element which consists of 1 type, or 2 or more types of.

The bulk magnetic core according to the first aspect of the invention is the bulk magnetic core described above, wherein the soft magnetic metal glass alloy exhibits the following composition in which ΔT _x is 50 ° C. or higher.

(Fe _1-a-b Co _a Ni _b ) _100-x-y-z M _x B _y T _z

However, 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, 0 atomic% ≤z≤5 atomic%, and M is Zr, Nb , Ta, Hf, Mo, Ti, an element consisting of one or two or more of V, T is one of Cr, W, Ru, Rh, Pd, Os, Ir, Pt, Al, Si, Ge, C, P It is an element which consists of a species or 2 or more types.

Further, in the first invention, ΔT _x is 60 ° C. or more, the value of a indicating the composition ratio of Co is 0.042 ≦ a ≦ 0.29, and the value of b indicating the composition ratio of Ni is 0.042 ≦ b ≦ 0.43. It is more preferable to do.

Next, in the bulk magnetic core of the first invention, the element M is represented by (M ′ _{1 -C} M ″ _C ), M ′ is one or two of Zr or Hf, and M ″ is Nb, Ta, Mo , Ti or V may be one or two or more elements, and 0 ≦ c ≦ 0.6.

In the above composition of the soft magnetic metal glass alloy, c may be in a range of 0.2 ≦ c ≦ 0.4, and c may be in a range of 0 ≦ c ≦ 0.2.

The bulk magnetic core of the first aspect of the invention may be obtained by subjecting the soft magnetic metal glass alloy to heat treatment at 427 to 627 ° C.

Further, in the composition of the soft magnetic metal glass alloy, 50% or less of element B may be replaced with C.

In order to achieve the above object, the second invention adopts the following configuration.

The laminated magnetic core of the second aspect of the invention has one or two or more elements of Fe, Co and Ni as a main component, and one or two or more elements of Zr, Nb, Ta, Hf, Mo, Ti, and V and B. And the temperature interval (ΔT _x ) of the supercooled liquid represented by the formula of ΔT _x = T _x -T _g (wherein, T _x represents the crystallization start temperature and T _g represents the glass transition temperature). A magnetic core body made of a thin magnetic metal glass alloy is provided.

In the present invention, Zr may be included in the composition, and ΔT _x may be 25 ° C. or higher.

The laminated magnetic core of the present invention includes a magnetic core body in which thin ribbons of the soft magnetic metal glass alloy described above are laminated in a toroidal shape.

The laminated magnetic core of the second invention is the laminated magnetic core described above, and the soft magnetic metal glass alloy has ΔT _x of 50 ° C. or more and is represented by the following composition.

(Fe _1-a-b Co _a Ni _b ) _100-x-y M _x B _y

However, 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, and M is Zr, Nb, Ta, Hf, Mo, Ti, V It is an element which consists of 1 type, or 2 or more types of.

Further, the core substrate into a multilayer stack before the magnetic core is of the second invention, the soft magnetic metallic glass alloys, △ T _x is greater than or equal to 50 ℃, when the composition described below.

(Fe _1-a-b Co _a Ni _b ) _100-x-y-z M _x B _y T _z

However, 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, 0 atomic% ≤z≤5 atomic%, and M is Zr, Nb , Ta, Hf, Mo, Ti, an element consisting of one or two or more of V, T is one of Cr, W, Ru, Rh, Pd, Os, Ir, Pt, Al, Si, Ge, C, P It is an element which consists of a species or 2 or more types.

Further, the second invention, wherein △ T _x is greater than or equal to 60 ℃, a represents the composition ratio of Co in 0.042≤a≤0.29, and it is more preferable that the b represents the composition ratio of the Nia 0.042≤b≤0.43.

Next, in the laminated magnetic core of the second invention, the element M is represented by (M ′ _{1 -C} M ″ _C ), M ′ is one or two of Zr and Hf, and M ″ is Nb, Ta, Mo , Ti or V may be one or two or more elements, and 0 ≦ c ≦ 0.6.

In the above composition of the soft magnetic metal glass alloy, c may be in a range of 0.2 ≦ c ≦ 0.4, and c may be in a range of 0 ≦ c ≦ 0.2.

The laminated magnetic core of the second aspect of the invention may be obtained by subjecting the soft magnetic metal glass alloy to heat treatment at 427 to 627 ° C.

Further, in the composition of the soft magnetic metal glass alloy, 50% or less of element B may be replaced with C.

EMBODIMENT OF THE INVENTION Hereinafter, the bulk magnetic core of this invention is demonstrated with reference to drawings.

The bulk magnetic core of the present invention is realized in a round ring shape, for example. Such a round-shaped bulk magnetic core is formed by sintering and molding a powder of a soft magnetic metal glass alloy described later to form a magnetic core body, or pouring a molten soft magnetic metal glass alloy into a predetermined mold, By cooling and solidifying to form a magnetic core body, a bulk magnetic core is obtained by carrying out insulation protection by covering these magnetic core bodies with resin of epoxy type, or sealing in a resin case.

In order to realize the bulk magnetic core of the EI core type, an E-type core and an I-type core are formed by sintering and molding a powder of a soft magnetic metal glass alloy, and a magnetic core body is formed by joining them.

The bulk magnetic core of the EI core type is obtained by covering such a magnetic core body with, for example, an epoxy resin, resin coating the necessary portion or enclosing the necessary portion in a resin case to insulate and protect the required portion.

Fig. 1 shows an example of a round ring bulk magnetic core. The bulk magnetic core 1 is a soft magnetic metal glass alloy which will be described later inside the hollow magnetic ring body storage case 2 made of resin. The magnetic core body (3) obtained by sintering the powder of or by pouring a molten soft metal glass alloy molten metal into a predetermined mold and cooling and solidified is housed.

The magnetic core body case 2 is preferably formed by using a resin such as polyacetal resin, polyethylene terephthalate resin, or the like.

Moreover, the adhesive member 4 for stably fixing the magnetic core body 3 and the magnetic core body storage case 2 is apply | coated to two places on the bottom face 2a of the magnetic core body storage case 2. It is preferable to make the number of the positions which apply | coat an adhesive member into the range of 2-4 places.

As the adhesive member 4, epoxy resin, silicone rubber, or the like is used.

Next, the method of manufacturing the bulk magnetic core 1 which concerns on this invention by the plasma sintering method is demonstrated.

Fig. 2 shows the main parts of an example of a discharge plasma sintering apparatus suitable for use in producing the bulk magnetic core 1 according to the present invention. The discharge plasma sintering apparatus of this example includes a cylindrical die 11 and a die ( 11) the upper punch 12 and the lower punch 13 inserted into the inside, the punch electrode 14 serving as one of the electrodes when supporting the lower punch 13 and flowing the pulse current described later; The thermocouple 17 for measuring the temperature of the punch electrode 15 serving as the other electrode through which the upper punch 12 is pushed downward and the pulse electrode flows, and the raw material powder 16 sandwiched by the upper and lower punches 12 and 13. ) Is composed mainly of.

On the surface where the upper punch 12 and the lower punch 13 face each other, a mold corresponding to the shape of the magnetic core body to be obtained is formed.

Moreover, the main part of said discharge plasma sintering apparatus is accommodated in the chamber which is not shown in figure. This chamber is connected to a vacuum exhaust device (not shown) and an atmosphere gas supply device, and keeps the raw material powder (powder) 16 filled between the upper and lower punches 12 and 13 under a desired atmosphere such as an inert gas atmosphere. It is configured to be.

In order to manufacture the bulk magnetic core 1 using the discharge plasma sintering apparatus of the said structure, the raw material powder for shaping | molding is prepared. The raw material powder 16 is obtained by casting a soft magnetic metal glass alloy having a predetermined composition, which will be described later, by a casting method, a quenching method using a single roll or a double roll, a liquid spinning method or a solution extraction method, or a high pressure gas. By the spray method, it is obtained by the process of manufacturing into various shapes, such as a bulk shape, a ribbon shape, a linear body, and a powder, and the process of grind | pulverizing and powdering other than powder form.

The soft magnetic metal glass alloy used in the present invention has a remarkable temperature interval in which the temperature interval (ΔT _x ) of the supercooled liquid of the alloy is 20 ° C or higher, depending on the composition, 40 ° C or higher, and even 50 ° C or higher. Unexpectedly from other alloys known from the standpoint of. In addition, the soft magnetic property has excellent characteristics at room temperature and is a novel one not seen from the viewpoint of the present.

Next, if the raw material powder 16 of the said composition was prepared, it puts in between the upper and lower punches 12 and 13 of the discharge plasma sintering apparatus shown in FIG. 2, and makes the inside of a chamber vacuum, and punches 12 and 13 are carried out. The mold is formed by applying pressure from above and below the furnace, and for example, a pulse current as shown in FIG. 3 is applied to the raw material powder and heated to form a magnetic core body 3 of a desired shape.

In this discharge plasma sintering process, the raw material powder 16 can be quickly heated up at a predetermined speed by the energizing current, and the temperature of the raw material powder 16 can be strictly managed according to the value of the energizing current. Therefore, temperature control can be performed more accurately than heating with a heater, and thus sintering can be performed under conditions close to an abnormality as previously designed.

In the present invention, the sintering temperature is required to be 300 ° C. or higher in order to solidify the raw material powder 16, but the soft magnetic metal glass alloy used as the raw material powder 16 has a temperature interval ΔT of a large subcooled liquid. _{Since it has x} (T _x -T _g ), the high-density magnetic core body 3 can be obtained suitably by press-sintering in this temperature range.

However, when the sintering temperature is close to the crystallization temperature, magnetic anisotropy occurs due to the generation of crystal nuclei (structural short-range ordering) or crystal precipitation, which may deteriorate soft magnetic properties.

Moreover, on the mechanism of the discharge plasma sintering apparatus, since the monitored sintering temperature is the temperature of the thermocouple 17 provided in the die 11, it is lower than the temperature applied to the raw material powder 16.

Therefore, the sintering temperature in the present invention is preferably in the range of T ≦ T _x when the crystallization start temperature is T _x and the sintering temperature is T.

In the present invention, the temperature increase rate at the time of sintering is preferably at least 10 ° C / min because a crystal phase is produced at a low temperature increase rate.

Moreover, about the pressure at the time of sintering, since the magnetic core body cannot be formed when the pressing force is too low, it is preferable to set it as 3t / cm <2> or more.

The magnetic core body 3 thus obtained may be subjected to heat treatment, whereby the magnetic properties can be improved. At this time, the heat treatment temperature is equal to or higher than the Curie temperature and is equal to or lower than the temperature at which crystals deteriorating the magnetic properties are precipitated. Specifically, the range of 427 to 627 ° C is preferable, and more preferably 477 to 527 ° C.

Since the magnetic core body 3 thus obtained has the same composition as the soft magnetic metal glass alloy used as the raw material powder 16, it has excellent soft magnetic properties at room temperature and exhibits better magnetic properties by heat treatment.

For this reason, since the bulk magnetic core 1 which consists of this magnetic core body 3 has the outstanding soft magnetic characteristic, it can apply widely to the magnetic core of a transformer, the magnetic core of a choke coil, the magnetic core of a magnetic sensor, etc., and It is possible to obtain a magnetic core of superior characteristics compared to the material.

In addition, in the above description, the method of forming the raw material powder 16 made of the soft magnetic metal glass alloy by discharge plasma sintering was used. However, the present invention is not limited to this, and is also bulk-sintered by pressing and sintering by a method such as an extrusion method. The core body (3) can be obtained.

The bulk magnetic core 1 of the present invention can also be obtained by providing the magnetic core body 3 obtained by flowing the molten metal of the soft magnetic metal glass alloy into a predetermined mold and cooling and solidifying it.

In the molten soft metal glass alloy, a predetermined amount of Fe, Co, Ni, and Zr single pure metals, pure boron crystals, etc. are respectively weighed as a raw material, and the raw materials are, for example, a high frequency induction heating apparatus under a reduced pressure Ar atmosphere. It is obtained by melting with an arc furnace, a crucible furnace, a reflection furnace, or the like.

Next, the magnetic core body 3 of a desired shape is obtained by pouring the obtained molten alloy into the mold of a predetermined shape, and cooling slowly and solidifying.

The magnetic core body 3 thus obtained has a high density and excellent soft magnetic characteristics similarly to the magnetic core body obtained by sintering an alloy powder, and thus can be used as a magnetic core for transformers, choke coils, magnetic sensors and the like.

Next, the laminated magnetic core of this invention is demonstrated with reference to drawings.

The laminated magnetic core according to the present invention is realized in a round ring shape, for example. Such a ring-shaped laminated magnetic core is manufactured by using a liquid quenching method of a soft magnetic metal glass alloy thin ribbon to be described later, and then wound the soft magnetic alloy thin ribbon in a toroidal shape to form a magnetic core body, or a soft magnetic alloy thin ribbon. Press blanking to obtain a ring, lamination of the required number of rings to form a magnetic core body, and lamination cores are obtained by coating the magnetic core body with resin of epoxy type or encapsulating it in a resin case for insulation protection.

In order to realize the laminated core of the EI core type, the soft magnetic metal glass alloy thin ribbon is press-blanked so as to be of E type or I type, and a plurality of E type flakes and I type flakes are prepared and then E type flakes. E-type cores and I-type cores are formed by stacking pieces or I-shaped flakes together, and the magnetic core bodies are formed by joining them.

An EI core type lamination core is obtained by covering such a magnetic core body with a resin of epoxy type, for example, by covering a required portion with a resin or by encapsulating the required portion in a resin case.

4 shows an example of a round ring-shaped laminated magnetic core. The laminated magnetic core 21 is a soft magnetic metal glass alloy, which will be described later, inside a hollow hollow ring-shaped magnetic core storage case 22 made of resin. The magnetic core body 24 formed by winding the thin ribbon plate 23 formed in a toroidal shape is housed.

The magnetic core body storage case 22 is formed using resin, such as polyacetal resin and polyethylene terephthalate resin, for example.

Moreover, the adhesive member 25 for stably fixing the magnetic core body 24 and the magnetic core body storage case 22 is apply | coated to two places on the bottom face 22a of the magnetic core body storage case 22. As shown in FIG. It is preferable to make the number of the positions which apply | coat an adhesive member into the range of 2-4 places.

As the adhesive member 25, epoxy resin, silicone rubber, or the like is used.

Fig. 5 shows another example of a round ring-shaped laminated magnetic core. The laminated magnetic core 31 is a soft magnetic metal glass, which will be described later, inside the hollow hollow ring-shaped magnetic core lower case 12 made of resin. It is obtained by storing the magnetic core body 33 formed by laminating the ring obtained by blanking from the thin ribbons 23 made of alloy, and fitting the magnetic core upper cover 34 to the magnetic core body lower case 32. The magnetic core lower case 32 and the magnetic core upper cover 34 are preferably formed using resins such as polyacetal resin and polyethylene terephthalate resin.

Conventionally, Fe-based alloys such as Fe-P-C, Fe-P-B and Fe-Ni-Si have been known to cause glass transition, but the temperature of the supercooled liquid region of these alloys is known. The width DELTA T _x is very small and cannot be constructed as a metallic glass alloy in practice.

In contrast, the soft magnetic metal glass alloy according to the present invention has one or two or more elements of Fe, Co, and Ni as a main component, and ΔT _x = T _x -T _g (wherein T _x is the crystallization start temperature). , T _g represents the glass transition temperature), and the temperature range (ΔT _x ) of the supercooled liquid region represented by the formula is 20 ° C or more, and 25 to 60 ° C or more depending on the composition. Molding becomes possible, and it becomes possible to produce the comparatively thick ribbon-shaped or linear shaped object.

In order to increase the spot ratio, the thickness of the thin ribbon of the amorphous alloy used for the laminated magnetic cores 21 and 31 may be increased.

In the conventional amorphous alloy, as described above, since the temperature width (ΔT _x ) of the supercooled liquid region is very small, in the case of rapidly cooling an alloy molten metal having a predetermined composition by a liquid quenching method, a thin ribbon is produced. In order not to reduce a soft magnetic characteristic, it was necessary to make thickness of a thin ribbon 50 micrometers or less, and there existed a limit to improvement of a droplet ratio.

In the soft magnetic metal glass alloy according to the present invention, it is possible to obtain a thin ribbon having a thickness of about 100 to 200 µm, and the magnetic core bodies 4 and 13 obtained by winding or laminating such thin ribbons have a high drop rate. Miniaturization of parts is possible. Moreover, since the specific resistance is high, when thin ribbons of the same thickness are used, the core loss can be made smaller than that of the conventional amorphous alloy.

In the method for producing thin ribbon 23 of the soft magnetic metal glass alloy of the laminated magnetic core of the present invention, for example, an elemental powder of each component is prepared, and these elemental powders are mixed so as to be within the above composition range, and then The mixed powder is dissolved in an inert gas atmosphere such as Ar gas, and dissolved in a crucible or the like to obtain a predetermined molten alloy molten alloy. The molten alloy is quenched using a single roll method to obtain a thin magnetic metal glass alloy thin ribbon. Can be. The single roll method is a method of obtaining a thin metal glass in which a molten metal is quenched by blowing a molten metal onto a rotating metal roll.

One of the soft magnetic metal glass alloys used for the bulk magnetic cores and the laminated magnetic cores is based on one or two species of Fe, Co, and Ni-based elements, and includes Zr, Nb, Ta, Hf, Mo, Ti, It is realized by the component system which added 1 type (s) or 2 or more types of V, and B predetermined amount.

One of the soft magnetic metal glass alloys according to the present invention is

(Fe _1-a-b Co _a Ni _b ) _100-x-y M _x B _y

In this general formula, a relationship of 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic% is preferable, and M is Zr , Nb, Ta, Hf, Mo, Ti, V or an element consisting of two or more.

In the above component system, the temperature interval (ΔT _x ) of the supercooled liquid region represented by ΔT _x = T _x -T _g (where T _x represents the crystallization start temperature and T _g represents the glass transition temperature). This needs to be 20 degreeC or more.

In the above in composition, it is preferably not less than necessarily contain Zr or Hf, and, △ T _x is 25 ℃.

In addition, it is more preferable from the in composition of △ T _x is not less than 60 ℃. In addition, the relationship is in the _{(Fe 1-a-b Co} a Ni b) 0.042 ≤a≤0.29, 0.042≤b≤0.43 in a _{100-x-y M x B} y the composition formula is preferably made.

Next, as the other soft magnetic metal glass alloy, in the general formula,

(Fe _1-a-b Co _a Ni _b ) denoted by _100-x-y-z M _x B _y T _z , and in this general formula, 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x ≤ 20 atomic%, 10 atomic% ≤ y ≤ 22 atomic%, 0 atomic% ≤ z ≤ 5 atomic%, and M consists of one or two or more of Zr, Nb, Ta, Hf, Mo, Ti, and V The element, T, is one, or two or more of Cr, W, Ru, Rh, Pd, Os, Ir, Pt, Al, Si, Ge, C, P. In addition, the present invention has a relationship of 0.042 ≦ a ≦ 0.29, 0.042 ≦ b ≦ 0.43 in the above formula (Fe _1-a-b Co _a Ni _b ) _100-x-y-z M _x B _y T _z It may be done.

Next, the said element M is represented by (M'1 _- CM " _C ), M 'is 1 type or 2 types of Zr or Hf, M" is 1 type of Nb, Ta, Mo, Ti, V, or An element consisting of two or more species may be characterized by being 0 ≦ c ≦ 0.6.

In the above composition, c may be in a range of 0.2 ≦ c ≦ 0.4, and c may be in a range of 0 ≦ c ≦ 0.2.

In the present invention, 0.042? A? 0.25 and 0.042? B? 0.1.

In the present invention, the soft magnetic metal glass alloy may be heat treated at 427 ° C (700K) to 627 ° C (900K). The heat treatment performed at the temperature in this range shows high permeability. In the above composition, up to 50% of the atoms B may be replaced with C.

(Reason for limitation)

In the composition system of the present invention, the main components Fe, Co, and Ni are elements that are responsible for magnetic properties, and are important for obtaining high saturation magnetic flux density and excellent soft magnetic properties.

Specifically, in order to obtain ensure the △ T _x of 50 ℃ ~ 60 ℃, the range of the value of b represents the composition ratio of the value of a represents the composition ratio of Co 0≤a≤0.29, Ni 0≤b≤0.43 in order to obtain surely the above 60 ℃ △ T _x, it is preferable that the value of a represents the composition ratio of Co the value of b represents the composition ratio of 0.042≤a≤0.29, Ni in the range of 0.042≤b≤0.43.

Within the above range, in order to obtain good soft magnetic properties, it is preferable that the value of a indicating the composition ratio of Co be in the range of 0.042 ≦ a ≦ 0.25, and in order to obtain high saturation magnetic flux density, It is more preferable to make the value of b shown into the range of 0.042 <= b <= 0.1.

M is an element consisting of one or two or more of Zr, Nb, Ta, Hf, Mo, Ti, and V. These are effective elements for producing amorphous, and may be in the range of 5 atomic% or more and 20 atomic% or less. In order to obtain high magnetic properties, it is more preferable to set it as 5 atomic% or more and 15 atomic% or less. Among these elements M, Zr is particularly effective. If the composition ratio of Zr is, but it can be substituted a part of the element such as Nb, substituting (c) is in a range of 0≤c≤0.6, can normally be obtained with a high △ T _x, in particular △ T _x 80 In order to make it ideal, the range of 0.2 <= c <= 0.4 is preferable.

B has high amorphous forming ability, and in this invention, it adds in 10 atomic% or more and 22 atomic% or less. When B is less than 10 atomic%, ΔT _x is reduced and the high-density magnetic core body 3 is not obtained, which is not preferable, and when it is larger than 22 atomic%, it is not preferable. In order to obtain higher amorphous forming ability and good magnetic properties, it is more preferable to set it as 16 atomic% or more and 20 atomic% or less.

In addition to the above composition system, one or two or more elements of Cr, W, Ru, Rh, Pd, Os, Ir, Pt, Al, Si, Ge, C, and P represented by T may be added.

In this invention, these elements can be added in 0 atomic% or more and 5 atomic% or less. These elements are mainly added for the purpose of improving the corrosion resistance, and if out of this range, the soft magnetic properties deteriorate. Moreover, it is unpreferable since it deteriorates amorphous forming ability beyond this range.

The soft magnetic metal glass alloy of the composition used in the present invention has magnetic properties at room temperature, and exhibits better magnetic properties by heat treatment.

In addition, in terms of the method for producing the soft magnetic metal glass alloy, a suitable cooling rate is determined depending on the composition of the alloy, the means for production, the size and shape of the product, etc., but it is usually 10 ² to 10 ⁶ ° C / s. It can be based on a range of degrees.

Bulk magnetic core (1) of the _{above, △ T x = T x -T} g of the super-cooling liquid temperature interval represented by the formula (where, T _x is the crystallization initiating temperature, T _g represents the glass transition temperature) (△ T _x ) Since the powder of the soft magnetic metal glass alloy having a temperature of 20 ° C. or more is sintered by the plasma sintering method, a bulky magnetic core body 3 having a high density can be obtained, so that the core loss can be made small.

In the above-described bulk magnetic core (1), the sintering temperature is arbitrarily selected from the temperature range where T≤T _x satisfies the relationship when the crystallization start temperature is T _x and the sintering temperature is T, and lead is a raw material. Since the magnetic core body 3 having the same composition as that of the magnetic metal glass alloy, having a high saturation magnetic flux density and excellent magnetic permeability can be obtained, the core loss can be made small.

Furthermore, by heat-treating the magnetic core body 3 shape | molded by sintering, higher saturation magnetic flux density and excellent permeability can be exhibited.

In the bulk magnetic core 1, the magnetic core body 3 is obtained not only by the plasma sintering method but also by the so-called casting method of cooling and solidifying the molten alloy, so that the manufacturing cost of the bulk magnetic core 1 can be lowered.

Moreover, the soft magnetic metal glass alloy of this invention has 1 type or 2 or more types of elements in Fe, Co, and Ni as a main component, and 1 type (s) or 2 or more types in Zr, Nb, Ta, Hf, Mo, Ti, V Since the element and B are contained and the temperature interval (ΔT _x ) of the supercooled liquid can be increased, the sintering temperature can be increased when the alloy powder is sintered, and a higher density magnetic core body 3 is obtained. The core loss of the bulk magnetic core 1 can be made small.

The bulk magnetic core 1 of the present invention is a soft magnetic metal having ΔT _x of 50 ° C. or more and a composition represented by the following general formula and having excellent magnetic permeability, small coercive force, and excellent soft magnetic properties. Since the magnetic core body 3 which consists of glass alloys is provided, a core loss can be made small.

(Fe _1-a-b Co _a Ni _b ) _100-x-y M _x B _y

However, 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, and M is Zr, Nb, Ta, Hf, Mo, Ti, V It is an element which consists of 1 type, or 2 or more types of.

or,

(Fe _1-a-b Co _a Ni _b ) _100-x-y-z M _x B _y T _z

However, 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, 0 atomic% ≤z≤5 atomic%, and M is Zr, Nb , Ta, Hf, Mo, Ti, an element consisting of one or two or more of V, T is one of Cr, W, Ru, Rh, Pd, Os, Ir, Pt, Al, Si, Ge, C, P It is an element which consists of a species or 2 or more types.

The laminated magnetic cores 21 and 31 are formed by the temperature interval of the subcooled liquid represented by ΔT _x = T _x -T _g (where T _x represents the crystallization start temperature and T _g represents the glass transition temperature). T _x) a, 20 ℃ or more soft-magnetic metal having a thin ribbon of glass alloy, it comprises a magnetic core main body 24, the magnetic core main body comprising the or a lamination 33 made wound in a toroidal shape, the plate is laminated magnetic core from thick thin ribbon thickness It is possible to create a, so that the droplet ratio of the laminated magnetic cores 21 and 33 can be increased, so that the core loss can be reduced and the size can be reduced.

The soft magnetic metal glass alloy is composed of one or two or more of Fe, Co, and Ni as a main component, and one or two or more elements of Zr, Nb, Ta, Hf, Mo, Ti, and V; Since the temperature gap (ΔT _x ) of the supercooled liquid can be increased, it is possible to prepare the laminated magnetic cores 21 and 31 from a thin plate with a large plate thickness, and thus the point of the laminated magnetic cores 21 and 31. The moment ratio can be improved to reduce the core loss.

The laminated magnetic cores 21 and 31 of the present invention have a temperature interval (ΔT _x ) of the supercooled liquid of 50 ° C. or more and the composition thereof is expressed by the following formula, and have a high permeability, a small coercive force, and a saturation magnetic flux density. Since the magnetic core bodies 4 and 13 made of a soft magnetic metal glass alloy having high and excellent soft magnetic properties are provided, the core loss can be made small.

(Fe _1-a-b Co _a Ni _b ) _100-x-y M _x B _y

However, 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, and M is Zr, Nb, Ta, Hf, Mo, Ti, V It is an element which consists of 1 type, or 2 or more types of.

or,

(Fe _1-a-b Co _a Ni _b ) _100-x-y-z M _x B _y T _z

However, 0≤a≤0.29, 0≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, 0 atomic% ≤z≤5 atomic%, and M is Zr, Nb , Ta, Hf, Mo, Ti, an element consisting of one or two or more of V, T is one of Cr, W, Ru, Rh, Pd, Os, Ir, Pt, Al, Si, Ge, C, P It is an element which consists of a species or 2 or more types.

Example

Example 1

The pure alloy and pure boron crystals of Fe, Co, Ni, and Zr were mixed in an Ar gas atmosphere and arc-dissolved to prepare a master alloy.

Next, the mother alloy is melted with a quartz nozzle, and argon gas is quenched by blowing at a pressure of 0.39 × 10 ⁵ Pa from a 0.4 mm diameter hole at the bottom of the nozzle to a copper roll rotating at 40 m / S in an atmosphere. By performing the roll method, a sample of a metal glass alloy thin ribbon having a width of 0.4 to 1 mm and a thickness of 13 to 22 µm was prepared. The obtained sample was analyzed by differential scanning calorimetry (DSC).

6, each of 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 , and Fe ₄₆ Co ₁₇ Ni ₇ Zr ₁₀ B ₂₀ , respectively. DSC curve of metal glass alloy thin sample of composition is shown.

In any of these samples, it was confirmed that a wide supercooled liquid region existed by increasing the temperature, and it became clear that it crystallized by heating over the supercooled liquid region. The temperature interval ΔT _x of the supercooled liquid region is expressed by the formula ΔT _x = T _x -T _g , but the value of T _x -T _g shown in FIG. It is in the range of 68 ° C. The substantial equilibrium state representing the supercooled liquid region was obtained in a wide range of 596 ° C (869K) to 632 ° C (905K) which was slightly lower than the temperature indicating crystallization by the exothermic peak.

Fig. 7 shows the dependence of the content of Fe, Co and Ni on the value of ΔT _x (= T _x -T _g ) in the composition system (Fe _1-a-b Co _a Ni _b ) ₇₀ Zr ₁₀ B ₂₀ . The triangular composition diagram shown.

As apparent from the results shown in FIG. 7, the value of ΔT _x is greater than 25 ° C. in all ranges of the composition system of (Fe _{1 -a -b} Co _a Ni _b ) ₇₀ Zr ₁₀ B ₂₀ .

In addition, with respect to the value of T _g, it became clear that the T _g increases monotonically increased by the Co in the range of about 50 atomic%, from about 7 at%. On the other hand, with respect to ΔT _x , it can be seen that it is a large value in a composition system containing a large amount of Fe, as shown in FIG. 5, in order to make ΔT _x at 60 ° C. or higher, the Co content is 3 atomic% or more, It turns out that it is preferable to set it as 20 atomic% or less and Ni content to 3 atomic% or more and 30 atomic% or less.

Further, in the _{(Fe 1-a-b Co} a Ni b) 70 Zr 10 B 20 composition formula in order to make the Co content is not less than 3 at%, 70 at.% Of _{(Fe 1-a-b Co} a Ni b) Therefore, in order to make Co composition ratio (a) 0.042 or more and Co content to 20 atomic% or less, Co composition ratio (a) becomes 0.29 or less. Similarly, in order to make Ni content 3 atomic% or more, Ni composition ratio (b) becomes 0.042 or more and 30 atomic% or less, and Ni composition ratio (b) becomes 0.43 or less.

Example 2

The pure metal and pure boron crystals of Fe, Co, Ni, Zr, and Nb were mixed in an Ar gas atmosphere and arc-dissolved to prepare a mother alloy having a composition of Fe ₅₆ Co ₇ Ni ₇ Zr ₄ Nb ₆ B ₂₀ .

Next, a sample of a metal glass alloy thin ribbon was prepared by dissolving the mother alloy in a quartz nozzle and performing a quenching method by spraying an alloy molten metal on a copper roll rotating in an argon gas atmosphere.

At this time, the alloy thickness of 20-195 micrometers of plate | board thickness was obtained by adjusting nozzle diameter, the distance (gap) of a nozzle tip and a roll surface, roll rotation speed, injection pressure, atmospheric pressure, etc. suitably.

Each sample was analyzed by X-ray diffraction. The results are shown in FIG.

From Fig. 8, it can be seen that the sample has a uniform pattern with 2θ = 38 to 52 degrees and has an amorphous single phase structure.

Example 3

A metal glass alloy ribbon was obtained in the same manner as in Example 1 except that the atomic composition ratio was Fe ₅₆ Co ₇ Ni ₇ Zr _10-x Nb _x B ₂₀ (x = 0, 2, 4, 6, 8, 10 atomic%). Samples of were prepared.

Next, the obtained sample was heat-processed for 5 minutes at the temperature of 527 degreeC (800K).

9 shows the Nb content dependence of the saturation magnetic flux density (Bs), coercive force (Hc), magnetic permeability (μe) at 1 Hz, and magnetostriction (λs) of the produced sample.

The saturation magnetic flux density (Bs) decreases with addition of Nb in both the quenched state and the heat-treated sample, and is about 0.75 (T) in a sample containing Nb not less than 0.9 (T) and containing 2 atomic% Nb. )

The value of the magnetic permeability (mue) was 2228 for the sample containing Nb at 5031 and Nb in the sample containing Nb in the quenched state, and decreased to 906 in the sample containing 10 at% in Nb. However, by performing heat treatment, the permeability (mue) is further improved, and in particular, a sample containing 2 atomic% Nb can obtain a permeability (μe) of about 25000.

Regarding the coercive force (Hc), in the quenched sample, both the sample containing Nb and the sample containing 2 atomic% Nb were 50 A / m (= 0.625 Oe), which was a low value. In particular, the sample whose Nb is 2 atomic% or less has shown the very favorable value at 5 A / m (= 0.0625 Oe). When the heat treatment is performed, excellent coercive force (Hc) can be obtained even in a sample containing 4 atomic% or more of Nb.

As mentioned above, in this alloy sample, in order to acquire favorable soft magnetic characteristics, it turns out that Nb has a more preferable range of 0 or more and 2 atomic% or less. Therefore, it is possible to obtain a bulk magnetic core and a laminated magnetic core having a soft magnetic metal glass alloy having a high saturation magnetic flux density, a small coercive force, and a high permeability, and when the transformer is manufactured using the bulk magnetic core and the laminated magnetic core In this case, it is possible to obtain a transformer having a small core loss and an excellent power transfer rate.

Example 4

A thin ribbon of a metal glass alloy was obtained in the same manner as in Example 1 except that the atomic composition ratio was Fe ₅₆ Co ₇ Ni ₇ Zr ₈ Nb ₂ B ₂₀ .

Next, the obtained thin ribbon was ground finely by grinding in air | atmosphere using the rotor mill. The particle | grains of 53-105 micrometers of particle diameters were selected from the obtained powder, and it used as a raw material powder for a post process.

About 2 g of the above-mentioned raw powder is filled into a die made of WC using a hand press, then loaded into the die shown in Fig. 2, and the inside of the chamber is punched up and down in an atmosphere of 3 x 10 ^-5 torr. At the same time as the pressure was applied, a pulse wave was energized from the power supply device to the raw material powder and heated. As shown in Fig. 3, after the 12 pulses were flowed, the 2 pulses were stopped, and the raw material powder was heated at a current of up to 4700-4800 A.

Sintering was performed by heating a sample from room temperature to a sintering temperature in the state which applied 6.5-t / cm <2> pressure to the sample, and holding for about 5 minutes. The temperature increase rate was 100 degreeC / min.

From the obtained sintered compact, the hollow-cylindrical sample of the outer diameter of 10 mm, the inner diameter of 6 mm, and the thickness of 2 mm as shown in FIG. 1 was produced by wire discharge processing, and the magnetic core body was obtained.

This magnetic core body was accommodated in the hollow round ring-shaped magnetic core body storage case made of polyacetal resin as shown in FIG. At this time, epoxy resin was applied to two places of the bottom surface of the magnetic core body storage case, and the magnetic core body storage case and the magnetic core body were fixed. Thus, three bulk magnetic cores which were subjected to the same treatment were obtained.

The measurement result of the core magnetic of the bulk magnetic core of a present Example is shown in FIG.

Moreover, as a comparative example, the relationship between the operating magnetic flux density of the magnetic core obtained by laminating | stacking a silicon steel plate (Si 3.5%), and a core loss was shown in FIG.

As is clear from Fig. 10, the cores of the present embodiment and the comparative example increase in the core loss with the increase of the operating magnetic flux density, but the bulk magnetic cores of the three examples are all within the range of the operating magnetic flux density measured than the magnetic cores of the comparative example. You can always see that the corerose is small.

Example 5

In the same manner as in Example 1, with a composition of Fe ₅₆ Co ₇ Ni ₇ Zr ₄ Nb ₆ B ₂₀ , thin ribbons of metal glass alloy having various plate thicknesses were obtained.

Next, each of the thin ribbons was blanked in a ring shape to stack the required number of sheets, and after impregnating a resin of epoxy or polyimide between the layers for insulation and fixing of each layer, the outer diameter 12 as shown in FIG. A circular ring-shaped laminated magnetic core having a mm, an inner diameter of 4 mm, and a thickness of 5 mm was prepared.

In Fig. 11, the relationship between the thickness of the thin plate of the laminated magnetic core obtained as described above and the droplet rate is shown. The measurement of the spot rate was obtained by observing the cross section of the laminated magnetic core under a microscope.

As shown in Fig. 11, the droplet rate improves with the increase of the plate thickness, and when it exceeds 100 mu m, the droplet rate becomes almost constant at 97% or more. In the laminated magnetic core made of the soft magnetic metal glass alloy according to the present invention, even if the thickness of the thin ribbon sheet exceeds 100 µm, the soft magnetic properties do not deteriorate as described above. Thus, a laminated magnetic core having a small core loss can be obtained. .

On the other hand, since the amorphous alloy of the prior art known as Fe ₇₈ Si ₉ B ₁₃ can only be obtained with a sheet thickness of about 20 μm, the droplet ratio in this case is lowered to 87%.

The conventional amorphous alloy has a small temperature width (ΔT _x ) of the subcooled liquid region, and thus does not lower the soft magnetic properties in the case of rapidly cooling the molten alloy of a predetermined composition by the liquid quenching method. In order to achieve this, the thickness of the thin plate needs to be 50 µm or less. If the thickness exceeds this thickness, the soft magnetic properties deteriorate, so that the increase of the droplet rate and the improvement of the soft magnetic properties cannot be realized simultaneously, and the cores are small. You can't gain self-esteem.

Example 6

In the same manner as in Example 1, a thin ribbon having a thickness of 20 ㎛ of _{Fe 56 Co 7 Ni 7 Zr 8} Nb 2 B 20, 20 ㎛ of _{Fe 62 Co 7 Ni 7 Zr 8} Nb 2 B 14 a metallic glass alloy of the following composition thickness After obtained, it blanked and laminated | stacked in the ring shape like Example 5, and these thin ribbons were heat-processed for 5 minutes at the temperature of 527 degreeC (800K).

Next, these thin ribbons were impregnated into a polyimide resin as in Example 5 to obtain a laminated magnetic core.

12 and 13 show the relationship between the operating magnetic flux density (Bm) of these laminated magnetic cores and the core loss.

In addition, the result of the core loss of the laminated magnetic core produced using the silicon steel (Si 6.5%) was shown simultaneously in FIG. 12 and FIG. 13 as a comparative example.

12 and 13 show the results of three samples subjected to the same treatment.

12 and 13, it can be seen that the laminated magnetic core according to the present invention has a smaller core loss than the laminated magnetic core of the comparative example.

In addition, this invention is not limited at all by the above example, Of course, various aspects are possible with respect to the composition, the manufacturing method, heat processing conditions, a shape, etc ..

According to the present invention, it is possible to obtain a bulk magnetic core and a laminated magnetic core having a soft magnetic metal glass alloy having a high saturation magnetic flux density, a small coercive force, and a high permeability. In the case of production, it is possible to obtain a transformer having a small core loss and an excellent power transfer rate.

Claims (8)

The temperature interval (ΔT _x ) of the supercooled liquid represented by the formula ΔT _x = T _x -T _g (where T _x represents the crystallization start temperature and T _g represents the glass transition temperature) is 50 ° C. or more, the soft magnetic metal powder is made of a glass alloy, the sintering temperature T and the start of the crystallization temperature T _x equation, a bulk amorphous magnetic core having a magnetic core composed of a body is sintered in a range of _x T ≤T, The soft magnetic metal glass alloy is (Fe _1-a-b Co _a Ni _b ) _100-x-y M _x B _y However, 0.042≤a≤0.29, 0.042≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, and M is Zr, Nb, Ta, Hf, Mo, Ti, V The bulk magnetic core characterized by being represented by the composition which is an element which consists of 1 type, or 2 or more types of. The temperature interval (ΔT _x ) of the supercooled liquid represented by the formula ΔT _x = T _x -T _g (where T _x represents the crystallization start temperature and T _g represents the glass transition temperature) is 50 ° C. or more, the soft magnetic metal powder is made of a glass alloy, the sintering temperature T and the start of the crystallization temperature T _x equation, a bulk amorphous magnetic core having a magnetic core composed of a body is sintered in a range of _x T ≤T, The soft magnetic metal glass alloy is (Fe _1-a-b Co _a Ni _b ) _100-x-y-z M _x B _y T _z However, 0.042≤a≤0.29, 0.042≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, 0 atomic% ≤z≤5 atomic%, and M is Zr, Nb , Ta, Hf, Mo, Ti, an element consisting of one or two or more of V, T is one of Cr, W, Ru, Rh, Pd, Os, Ir, Pt, Al, Si, Ge, C, P The bulk magnetic core characterized by the composition which is a species or an element which consists of 2 or more types. The method of claim 1, The bulk magnetic core characterized in that ΔT _x is 60 ° C. or more. The method of claim 2, The bulk magnetic core characterized in that ΔT _x is 60 ° C. or more. △ T _x = T _x -T _g at temperature intervals of the super-cooling liquid of the formula (where, T _x is the crystallization initiating temperature, T _g represents the glass transition temperature) (△ T _x) is more than 50 ℃, open A laminated magnetic core provided with an amorphous magnetic core body made of a thin metal magnetic alloy alloy ribbon, The thickness of the ribbon is 100-200 μm, the ribbon is made of a laminate or wound in a troidal shape, The composition of the soft magnetic metal glass alloy is (Fe _1-a-b Co _a Ni _b ) _100-x-y M _x B _y However, 0.042≤a≤0.29, 0.042≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, and M is Zr, Nb, Ta, Hf, Mo, Ti, V It is represented by the composition which is an element which consists of 1 type, or 2 or more types of, The laminated magnetic core characterized by the above-mentioned. △ T _x = T _x -T _g at temperature intervals of the super-cooling liquid of the formula (where, T _x is the crystallization initiating temperature, T _g represents the glass transition temperature) (△ T _x) is more than 50 ℃, open A laminated magnetic core provided with an amorphous magnetic core body made of a thin metal magnetic alloy alloy ribbon, The thickness of the ribbon is 100-200 μm, the ribbon is made of a laminate or wound in a troidal shape, The soft magnetic metal glass alloy, (Fe _1-a-b Co _a Ni _b ) _100-x-y-z M _x B _y T _z However, 0.042≤a≤0.29, 0.042≤b≤0.43, 5 atomic% ≤x≤20 atomic%, 10 atomic% ≤y≤22 atomic%, 0 atomic% ≤z≤5 atomic%, and M is Zr, Nb , Ta, Hf, Mo, Ti, an element consisting of one or two or more of V, T is one of Cr, W, Ru, Rh, Pd, Os, Ir, Pt, Al, Si, Ge, C, P A laminated magnetic core characterized by being represented by a composition which is a species or an element consisting of two or more species. The method of claim 5, The ΔT _x is 60 ° C. or more, the laminated magnetic core. The method of claim 6, The ΔT _x is 60 ° C. or more, the laminated magnetic core.