JPS6229105A - Co radical amorphous wound magnetic core - Google Patents

Abstract

PURPOSE:To improve the high frequency magnetic characteristics and the time stability of the titled magnetic core as well as to reduce its iron loss by a method wherein a Co radical amorphous magnetic alloy thin band, partially containing a crystal phase and having specific coercive force, is wound around. CONSTITUTION:When an amorphous ribbon is formed using a liquid quick- cooling method or a heat treatment is performed, a Co amorphous magnetic alloy thin band partially containing a crystal phase and having the coercive force of 0.20 (e) or below is wound around. The Co radical amorphous magnetic alloy indicated by the formula (Co1-x-y-zFexMnyNiz)100-a-b-cMaSib which satisfies the relation of 0<=x<=0.1, 0.001<=y<=0.2, 0<=z<=0.13, 0<=a<=6, 8<=b<=18, 7<=c<=18, and 18<=b+c<=30 is considered suitable as the material of the wound magnetic core. As a result, the wound magnetic core having excellent high frequency magnetic characteristics, a low iron loss and the excellent rime stability can be obtained.

Description

[Detailed Description of the Invention] "Industrial Application Field" The present invention relates to a Co-based amorphous wound magnetic core that has excellent high-frequency magnetic properties and stability over time and is suitable as a magnetic core for high-frequency transformers, noise filter chokes, etc. .

``Prior Art'' Conventionally, ferrite cores have been mainly used for magnetic cores in high-frequency transformers, noise filter chokes, and the like. However, since the ferrite magnetic core has a low saturation magnetic flux density, for example, when a large voltage noise is input to a noise filter, the magnetic core becomes saturated and the noise cannot be effectively blocked.

For this reason, recently, as a solution to this problem,
A magnetic core formed by winding an amorphous magnetic alloy ribbon (
In this specification, this is referred to as an "amorphous wound core")
A method using
In other words, since the amorphous wound magnetic core is formed by winding a thin ribbon as mentioned above, it exhibits relatively excellent high frequency characteristics, and its saturation magnetic flux density is much higher than that of the ferrite magnetic core. Due to its high cost, its application to these applications has been attracting attention and proposals.

By the way, since it is desirable that magnetic cores for high frequency transformers, noise filter chokes, etc. have higher saturation magnetic flux density, what has been proposed so far is mainly Fe-based amorphous wound magnetic cores. However, although Fe-based amorphous magnetic alloys have a high saturation magnetic flux density, they have a large core loss.
As shown in Japanese Patent No. 707, there are drawbacks such as the need to take measures such as precipitating microcrystals and subdividing magnetic domains to reduce iron loss. Further, even if a magnetic core subjected to such treatment is used, there is a problem in that a ferrite magnetic core is more advantageous in terms of iron loss in a region of 100 kI-rz or higher.

"Problems to be Solved by the Invention" In view of the above circumstances, the present inventors did not take any special measures such as precipitating microcrystals, although the saturation magnetic flux density is not as good as that of Fe-based amorphous wound cores. We also attempted to apply a CO-based amorphous-wound core, which has smaller iron loss than an Fe-based amorphous-wound core because the magnetic domains are subdivided.

As a result, it was found that the CO-based amorphous wound magnetic core has very excellent initial magnetic properties and can obtain properties equivalent to or better than ferrite even at high frequencies of several 100 kHz.

However, it has been newly discovered that the Co-based amorphous wound magnetic core has a large change in iron loss over time, and that there is a big problem when it is used at relatively high temperatures.

The present invention solves the above-mentioned problems and provides a low-loss carbon fiber with excellent high-frequency magnetic properties and stability over time, which is suitable as a magnetic core for high-frequency transformers, noise filter chokes, etc.
The object of the present invention is to provide an o-group amorphous as-wound magnetic core.

In order to achieve the above object, the present invention provides an amorphous ribbon with a coercive force of 0, which partially contains a crystalline phase when producing an amorphous ribbon by a liquid quenching method or during heat treatment. It is characterized by forming an amorphous wound magnetic core by winding a thin ribbon of a Co-based amorphous magnetic alloy of 20 e or less, and with this configuration, the iron loss w z at a frequency of 100 kHz and a peak value of magnetic flux density of 2 kG / to
Low loss with ot of 500 mW/cc or less,
A CO-based amorphous wound core with excellent high-frequency magnetic properties and excellent stability over time has been realized.

In the present invention, the Co-based amorphous magnetic alloy is
Formula (Cot-x-7-Z FexMnyNx2)□,.

-a-b-QM 11 S lb B c [where,
M is Ti, Zr, Hf, V, Nb, Ta, Cr, Mo
, W, Cu, Ag, Au, Y, and rare earth elements], and 0≦X
≦o, i, 0.001≦y≦0.2.0≦Z≦0.1
3.0≦a≦6, 8≦b≦18, 7≦C≦18.18≦
It is preferable to use a material that satisfies the relationship b+c≦30 because it can particularly reduce changes over time.

In the present invention, the crystalline phase can be confirmed by X-rays, and it is preferable that the crystalline phase be present to such an extent that a slight crystalline peak can be detected above the halo peak characteristic of amorphous. Partial inclusion of the crystalline phase can be done either during heat treatment or during ribbon production, but it is easier to control the properties if the crystalline phase is precipitated by heat treatment. This heat treatment is usually carried out at a temperature of one Curie temperature or higher, and by adjusting the amount of crystalline phase by adjusting the temperature and time, a product containing a crystalline phase and a low loss can be obtained. Further, after this heat treatment, heat treatment in a magnetic field at a temperature below one Curie temperature may be performed to improve magnetic properties and the like.

In the present invention, if the number of crystal phases increases too much, iron loss will increase, so the advantage of using it at high frequencies will be diminished.

In addition, it is better to use a CO-based amorphous magnetic alloy with a direct current coercive force of 0.2 Oe or less; in this case, one frequency is 10
At 0kHz, the iron loss at peak values of magnetic flux density of 2 to 9 is 50
It becomes 0mW/cc or less.

Furthermore, when a crystalline phase is partially included during ribbon production by the molten metal quenching method, the molten metal temperature is increased.

Slow down the roll peripheral speed. Increase the jet pressure. Increase roll temperature. Any of the following methods may be used, and it is preferable to perform stress relaxation heat treatment after forming the wound core.

Further, in the present invention, it is advantageous to use an amorphous alloy ribbon having a thickness of 30 μm or less, especially in terms of reducing high frequency loss.

"Example" Hereinafter, the present invention will be explained based on examples.

Example 1 FIG. 1 shows partially crystalline (Co,
,,,Fel,,,6)7. Sin, B, amorphous wound core and conventional (Co,...
Fe0. . ,),.

X-ray diffraction pattern of Si, BS amorphous wound core.

DC B-H curve and iron loss W2/□. It is a diagram showing a comparison of Ok (iron loss at a frequency of 100 kHz and a peak value of magnetic flux density of 2 kG). The amorphous alloy ribbon used in this example had a thickness of 18 μm and was manufactured by a single roll method.

As is clear from FIG. 1, the wound magnetic core X according to the present invention,
In the W diffraction pattern, a slight crystalline peak is observed near the halo peak characteristic of amorphous, indicating the presence of a crystalline phase. In addition, one direct current B- of the wound magnetic core according to the present invention
Although the H-curve has a lower squareness ratio and a larger coercive force than a conventional wound core, the initial iron loss is almost the same, and it is clear that the presence of the crystal phase has almost no effect.

(Example 2) Table 1 shows the initial iron loss W0□7i of the CO-based amorphous wound magnetic core partially containing a crystalline phase according to the present invention and the conventional CO-based spring-wound magnetic core that does not contain a crystalline phase. ,and.

It is a table comparing iron loss W8□7□oat after holding at 120°C for 8 hours.

The wound magnetic core according to the present invention has an initial iron loss equivalent to that of a conventional Co-based spring-wound magnetic core that does not contain crystals, but the iron loss after being held at 120°C for 8 hours is small and stability over time has been improved. Recognize.

In particular, in the present invention, the CO-based amorphous wound magnetic core containing Mn has good stability over time.

(Example 3) Table 2 shows the initial iron loss W''□7 of the Co-based amorphous wound magnetic core partially containing a crystalline phase according to the present invention and the conventional Fe-based amorphous wound magnetic core partially containing a crystalline phase. □. . 1 and the iron loss after impregnation W9□7□. . This is a table comparing the

The wound magnetic core according to the present invention has a conventional partially crystalline phase-containing Fe core.
Iron loss is smaller than the base amorphous wound core.

Moreover, it is clear that the deterioration after impregnation is also small.

Therefore, it can be seen that the amorphous wound magnetic core of the present invention is suitable for high frequency magnetic cores such as cut cores and coated cores.

(Example 4) FIG. 2 shows CoG, 5Fe4. . Ni,0,Si,,
,,B,,,.

Coercive force Hc of Mo4.2 amorphous wound core, and iron loss W27□. . 2 is a diagram showing an example of the dependence of , on the heat treatment temperature Ta. The crystal peak by X-ray diffraction in this example was observed at 495°C. As can be seen from the figure, if the heat treatment temperature is too high and the crystalline phase increases too much, the core loss will increase rapidly and the high frequency magnetic properties will deteriorate. however,
When the coercive force is in a range of 0.2 Oe or less, the iron loss is 500 mW/cc or less even if a crystalline phase is included. Therefore, it is clear that the coercive force of the CO-based amorphous wound core in the present invention may be 0.2 Oe or less.

"Effects of the Invention" As described above, according to the present invention, a wound core with excellent high-frequency magnetic properties, low iron loss, and good stability of iron loss over time can be obtained, compared to conventional products. The effect is significant because it becomes possible to realize electrical components such as high-frequency transformers that have better characteristics in the high-frequency range.

[Brief explanation of the drawing]

FIG. 1 shows a partially crystalline (Co., 54 FeO, 06)755ii5 B! according to the invention. Amorphous wound magnetic core and conventional (C'00.94
FeO,QG)7GSi1. B, X-ray diffraction pattern for amorphous wound core, DC B-H curve, iron loss W
27□. . , Figure 2 shows CoG, , GFe
4. ,Ni,,1Si,,. B engineering. , z M 01. Z Coercive force He and iron loss W27□ of the amorphous wound core. . FIG. 2 is a diagram showing an example of the heat treatment temperature dependence of .

Claims (2)

[Claims] (1) A low-loss Co-based amorphous with excellent stability over time, which is formed by winding a Co-based amorphous magnetic alloy ribbon that has a coercive force of 0.2 Oe or less and partially contains a crystalline phase. Wound magnetic core. (2) The above amorphous magnetic alloy has a compositional formula (Co_1
＿−＿x＿−＿y＿−＿zFe_xMn_yNi_z)
_1_0_0_-_a_-_b_-_cM_aSi_b
B_c [However, M is Ti, Zr, Hf, V, Nb, Ta
, Cr, Mo, W, Cu, Ag, Au, Y, and rare earth elements], and 0≦x≦0.1, 0≦a≦6 , 18≦b+
c≦30, 0≦y≦0.2, 8≦b≦18, 0≦z≦0
．． 13. The Co-based amorphous wound magnetic core according to claim 1, which is a Co-based amorphous magnetic alloy satisfying 7≦c≦18.