JPS6329909A - Fe group amorphous magnetic core for saturable reactor and manufacture thereof - Google Patents

Abstract

PURPOSE:To reduce the dispersion of control magnetizing characteristics by constituting the title amorphous magnetic core of a specific amorphous alloy thin-band and bringing overall control magnetizing force at 50KHz and uncontrollable magnetic flux density to specific values. CONSTITUTION:The title amorphous magnetic core is shown in formula I, M represents at least one kind of an element selected from Mo, Nb, Ta, W in the formula, and the magnetic core is composed of an amorphous alloy thin-band having the relationship of 0.005<=a+b<=0.05, 2<=x<=6, y<=19, 7<=z<=25 and 20<=x+y+z<=30. Overall control magnetizing force Hr at 50 KHz extends over 20A/m or less and uncontrollable magnetic flux density DELTABd over 0. 2T or less. Ni or Ci is an essential element and reduces uncontrollable magnetic flux density DELTABd, and has an effect that a control range is extended and an effect that dispersion is minimized. Accordingly, the dispersion of the control magnetizing characteristics or the Fe group amorphous magnetic core which has been insufficient can be lowered.

Description

DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to an Fe-based amorphous magnetic core used in a saturable reactor used in a switching power supply or the like.

[Conventional technology]

Conventionally, saturable reactors used in switching power supplies, etc. have a 50% Ni permalloy core and an 80% N core.
It is used for i-permalloy magnetic cores, Co-based amorphous magnetic cores, etc. In recent years, especially switching power supplies have been driven at high frequencies, and Co-based amorphous magnetic cores with low loss and control magnetization force at high frequencies have been used. It has become to.

However, the Co-based amorphous magnetic core uses an expensive raw material such as CO, resulting in a high price, and has a low saturation magnetic flux density, resulting in a small maximum value of the controlled magnetic flux density.

On the other hand, Fe-based amorphous magnetic cores have a higher saturation magnetic flux density than Go-based amorphous magnetic cores, and as described in Japanese Patent Publication No. 1183/1983, heat treatment in a non-oxidizing cloud atmosphere improves DC magnetic properties with a high squareness ratio. known to be obtained.

[Problems to be Solved by the Invention] However, the above Fe-based amorphous magnetic core with a high squareness ratio has a characteristic that is important as a magnetic core for a saturable reactor at high frequencies, especially at 20 kHz, which is an important characteristic as a magnetic core for a saturable reactor. When used in a saturable reactor used in the magnetic amplifier of a switching power supply that is driven at a frequency higher than that, there is a problem in that the control current required to control the output voltage becomes large, which increases the burden on the control circuit and reduces efficiency. There's a problem. The present inventors have previously revealed that excellent controlled magnetization characteristics can be obtained with Fe-based amorphous material (Japanese Patent Application No. 21309/1982).

However, in the case of Fe-based amorphous magnetic cores, there is a problem of large variations in the longitudinal direction of the amorphous ribbon, and when producing a magnetic core after producing a large amount of amorphous ribbons, it is important that the variation in the control magnetization characteristics is small. come.

An object of the present invention is to provide an Fe-based amorphous magnetic core for a saturable reactor that has excellent control magnetization characteristics and small variations in control magnetization characteristics.

[Means for solving problems]

The present invention has the following compositional formula: % () where M is at least one element selected from Mo, Nb, Ta, and W, and 0.005≦a+b≦0.05. 2≦X≦6. y
Consisting of an amorphous alloy ribbon having the relationship of ≦19°7≦2≦25.20≦x+y+z≦30, 50kllz
This is an Fei amorphous magnetic core for a saturable reactor with excellent control magnetization characteristics, characterized in that the total control magnetization force Hr is 20 A/m or less and the uncontrollable magnetic flux density ΔBd is 0.2 T or less.

In the present invention, Si and B are elements necessary for amorphous formation, and the S amount y is y≦19. B amount Z is 5≦2≦
When the relationship 25.20≦x+y+z≦30 exists, it is easy to form an amorphous state, and when the relationship is outside this range, manufacturing becomes difficult, which is not preferable.

Ni or Co is an essential element and the uncontrollable magnetic flux soundness Δ
This has the effect of reducing Bd, increasing the control range, and reducing variation. Ni and C.

If the sum a+b of the composition ratios a and b exceeds 0.05, the total control magnetizing force will increase, which is undesirable, and if it is less than 0.005, the variation in the uncontrollable magnetic flux density ΔBd will increase, which is undesirable.

M has the effect of reducing the total control magnetizing force Hr, and the M amount x
If it is less than 2, there is no effect on HrJ, and if it exceeds 6, ΔB
This is because the variation in d increases.

Especially 8≦y≦16.8≦2≦10.20≦X+y+z≦
Is it illegal to have a relationship of 30? Changes over time in the In 65'f properties are small, and favorable results can be obtained.

Usually, the amorphous alloy ribbon according to the present invention is produced by the double-hole method.
It is produced by a method such as a single roll method.

In the case of the present invention, the plate thickness is preferably 25 μm or less. In some cases, a powder such as alumina or SiO□ or an oxide film may be formed to provide interlayer insulation.

In the magnetic core of the present invention, a magnetic core made of an amorphous alloy ribbon is held in an inert gas atmosphere or vacuum for a certain period of time until the stress is almost completely relaxed above the Curie temperature, and a DC or AC magnetic field is applied in the direction of the magnetic path. 1℃/mi
Cooling at an average cooling rate of not less than n and not more than 20°C/min,
At a temperature of 200℃ or higher and lower than the Curie temperature for 0.5 hours or more5
It is produced by keeping it for less than h and then cooling it to room temperature.

It is preferable that the heat treatment be carried out in an inert gas atmosphere or vacuum, and if the heat treatment is carried out in an extremely oxidizing atmosphere, the uncontrollable magnetic flux density ΔBd will increase, which is undesirable.

The reason why the stress is maintained for a certain period of time until the stress is almost completely relaxed above the Curie temperature is to reduce the uncontrollable magnetic flux density ΔBd in the next heat treatment process in a magnetic field, and to reduce the variation in the control magnetization characteristics and increase the total control magnetization force Hr. This is to make it smaller.

At a temperature of 200℃ or higher and lower than the Curie temperature for 0.5 hours or more5
The reason why the temperature is kept below h and then cooled to room temperature is to reduce the uncontrollable magnetic flux density ΔBd and to reduce the total control magnetizing force Hr, as described above.

If the retention time is less than 0.5h, ΔBd will be large, and if it exceeds 5h, Hr will be large, so the retention time should be 0.5h or more.
Less than h is desirable.

The heat treatment method described above has little effect on magnetic cores with compositions other than those of the present invention; for example, in the case of Fe-Cr-5i-B system or amorphous, ΔBd tends to become large (and when used in a saturable reactor, the control range becomes small). A problem arises in that not only is the temperature of
In the case of i-B type amorphous, there is a problem that the total control magnetization force Hr at high frequencies becomes large even if the above heat treatment is performed. Therefore, when this manufacturing method is applied to an amorphous alloy ribbon having the composition of the present invention, it is possible to obtain excellent characteristics as a magnetic core for a saturable reactor with small variations.

In addition, it is held in an inert gas atmosphere or vacuum for a certain period of time until the stress is almost completely relaxed above the Curie temperature, then rapidly cooled to room temperature, and then heated to a temperature above 200°C while applying a direct current or alternating current magnetic field in the direction of the magnetic path. Similar characteristics can be obtained by heat treatment in which the temperature is raised to a temperature lower than that temperature, maintained for 0.5 hours or more and less than 5 hours, and then cooled to room temperature.

〔Example〕

The present invention will be explained below according to examples.

Embodiment 1 FIG. 1 shows a control magnetization characteristic measuring circuit, which is suitable for evaluating a control magnetic core. Figure 2 shows an arbitrary DC control current engineer. FIG. 2 is a schematic diagram of the operation of the magnetic core when the flow is flowing through the control circuit.

In FIG. 1, sample S is provided with three types of windings: NL + NG and Nv.

NL corresponds to the output winding of the magnetic amplifier, and the AC type aE9 with frequency f (period Tp) is connected via resistor RL and rectifier.
It is connected to the. The value of E9 is set to a large value so that the magnetic core reaches saturation at a phase angle within 90° of the sine wave voltage of the applied voltage in the gate half period Tg.

Nc is a control winding, which is connected to a DC power source Ec through an inductance Lc that is sufficiently large compared to the core inductance seen from the control circuit, and provides a DC magnetomotive force under the constrained magnetization condition. Nv is a winding for measuring the reset magnetic flux amount Δφ corresponding to the human control power, and is connected to an AC voltmeter (■) of the average value rectification method.

FIG. 3 shows a schematic diagram of a controlled magnetization curve obtained by measurement using this measurement circuit.

Letting the reciprocal of Hr be β0, then βo=1/Hr As for the control magnetic core, the larger β0 (the smaller Hr), the smaller the control current and the better the characteristics.

On the other hand, if α0 is the parameter indicating the degree of rectangularity of the magnetic core's magnetization characteristics, then αo = 1 - ΔBb/ΔBm For a control core, α0 is large (ΔBb/ΔBm is small)
The smaller the uncontrollable magnetic flux density, the better the characteristics.

The product of Q'Q and β0 is expressed as Go, and SpecificC
It is called "ore gain", and it can be judged that the larger Go = α0 Keyaki β0, the better it is as a control magnetic core.

Maximum value of gate magnetic field Hm −(NL−i L (max) l / /!e
・・・・・・(1) I! e: Maximum value Bm of magnetic flux density corresponding to the average magnetic path length of the sample and control magnetic field Hr =
(Nc ・Ic) / le −(
If the magnetic flux density difference between the magnetic flux density Bc determined by
3) A: Effective cross-sectional area of the magnetic core In an actual control magnetic core, the characteristic H in the region where the magnetic field H is positive
m-ΔBm characteristics and characteristics Hr-ΔB in the region where the magnetic field H is negative
It is necessary to understand the characteristics.

ΔBd = Bm −Br...
-(4) and EvdoCC-NV -A・ΔB d −・
・-+51.

On the other hand, ΔB1000ΔBcm−ΔBd...
- (6).

The control magnetic core is better if the curve in the first quadrant shown in FIG. 3 is on the lower side, the curve in the second quadrant is closer to the right, and the slope is steeper.

Example 2 By single roll method (Feo, 47Nio, 02COO
, o+LzMo3SilJq amorphous alloy ribbon (thickness: 18 μm, width: 51 mm, length: 10100 mm) was prepared.

The obtained alloy ribbon was wound into a wound core having an outer diameter of 19 tm and an inner diameter of 15 tm, and was heat-treated in an N2 gas atmosphere. The heat treatment was first held at 500°C for 1 hour, cooled to 250°C while applying a magnetic field of 100e in the direction of the magnetic path, and then held at 250°C for 2 hours to obtain a magnetic core of the present invention.

The 50kHz control magnetization characteristics of the obtained 190 wound magnetic cores were measured, and the total control magnetization force Hr and uncontrollable magnetic flux density ΔBd were measured.
I asked for

The obtained characteristic ranges of Hr and ΔBd are shown in Table 1.

In addition, for comparison, FetJo was produced using the same manufacturing method.
3Sx I 4Bs Hr of amorphous wound core, Δ
The characteristic range of Bd is also shown in Table 1.

Table 1 Example 3 An amorphous alloy ribbon shown in the table below with a width of 5N, a thickness of about 15 μm and a length of 500 m was produced by a single roll method, and an outer diameter of 19 m.
-1 is wound to an inner diameter of 151 m, held until the horns are almost 100% relaxed at temperatures above the Curie temperature and below the crystallization temperature, and then 5°C/5°C while applying a magnetic field of 100 e in the direction of the magnetic path.
Cool to 250'C at a cooling rate of min for 0.5 h.
After maintaining the temperature at 250° C., the core was air-cooled to room air to produce a wound magnetic core of the present invention.

The produced wound magnetic core was placed in a phenol case and its controlled magnetization characteristics were measured using the measurement circuit shown in FIG.

Table 2 shows the characteristic variation ranges of the total control magnetization force Hr and the uncontrollable density density ΔBd in the longitudinal direction of the ribbon.

For comparison, FetzNb*Si+. Also shown are variations in the longitudinal direction of ΔBd and Hr of the 13+s amorphous-wound magnetic core Fe7Jn+Sj+Jq amorphous-wound magnetic core.

It can be seen that the Fe-based amorphous wound magnetic core according to the present invention has small variations in the total control magnetizing force Hr related to the control current, and small variations in the uncontrollable magnetic flux density ΔBd related to controllability.

As can be seen from the table, the Fe-based amorphous wound magnetic core according to the present invention has small variations in the total control magnetization force Hr related to the control current, and has a small variation in the total control magnetization force Hr related to the control current. The variation in the ff1l-impossible magnetic flux density ΔBd is also small, making it suitable for a magnetic core for a saturable reactor.

Example 4 (Feo, q
qsNio, 005) 72.5M0ssi+ 3.
A 5BI+ amorphous alloy ribbon was prepared, wound to an outer diameter of 19N and an inner diameter of 151, held at 500°C for 1 hour, and then cooled for 28 hours at different cooling rates while applying a magnetic field of 100e in the direction of the magnetic path.
The sample was cooled to 0°C, held at 280°C for 1 hour, and then cooled in air and measured for controlled magnetization characteristics. Table 3 shows the average values of the total control magnetization force Hr and the uncontrollable magnetic flux density ΔBd obtained from the control magnetization characteristics for 20 samples.

Table 3 shows that if the cooling rate is less than 1°C/min, the Hr will increase, which is undesirable, and if the cooling rate exceeds 5°C/mjn, the Hr will increase.
It can be seen that r becomes large, which is not preferable.

Example 5 (Fe+-a
-bNia Cob)t4.5Mo3st+x,sBq
An amorphous alloy ribbon was made with an outer diameter of 19 mm and an inner diameter of 1.
It was wound around a 5-thick tube, kept at 490°C for 1 hour, and then air-cooled to room temperature.

Next, while applying a magnetic field of 5 Oe in the direction of the magnetic path, the temperature was raised and maintained at 280° C. for 4 hours, and then cooled to room temperature.

The obtained wound magnetic core was placed in a core case made of phenol resin, and after winding, the controlled magnetization characteristics were measured.

FIG. 4 shows the dependence of the total control magnetizing force Hr and the uncontrollable magnetic flux density ΔBd on the sum a+b of Ni and Co.

If a+b is less than 0.05, ΔBd tends to become somewhat large and the variation becomes large, which is not preferable. a+b
If it exceeds 0.05, the total control magnetizing force increases, which is not preferable.

Example 6 (Feo,
qqNio, o+)az, s-zMOzTa1s
i13. A sBz amorphous alloy ribbon was prepared, wound around an outer diameter of 19 mm and an inner diameter of 15 mm, held at 490'C for 1 hour, and heated at 3°C/m while applying a magnetic field of 100 e in the direction of the magnetic path.
Cool to 250'C at a cooling rate of 4 in.
After holding for a time, the core was cooled to room temperature to produce a magnetic core of the present invention, and the total control magnetization force Hr was measured. Next, the total control magnetization force Hr5°0 after being held at 120°C for 500 hours was measured.

Figure 5 shows the rate of change over time Δ0r (=IIr500-Hr)
/) Shows the B ii z dependence of Ir.

It is particularly preferable that 2 be in the range of 8 or more and 10 or less because the change over time in the total control magnetizing force is small.

〔Effect of the invention〕

According to the present invention, it is possible to reduce variations in the controlled magnetization characteristics of Fe-based amorphous magnetic cores, which have been insufficient in the past, and the effect is significant.

[Brief explanation of drawings]

Fig. 1 is a control magnetization characteristic measurement circuit, Fig. 2 is a schematic diagram of the operation of the magnetic core when an arbitrary DC control current 1c flows through the control circuit, Fig. 3 is a schematic diagram of the control magnetization curve, and Fig. 4 is a diagram showing the dependence of the total control magnetization force Hr and the uncontrollable magnetic flux density ΔBd on the sum a+b of Ni+Co, and FIG.
It is a figure showing the B amount 2 dependence of r/Hr. Figure 1 Figure 2 Figure 3 Figure 4 0 0.010.020.030.040.050.0
60.07a+b Figure 5

Claims (1)

[Claims] 1. Composition formula (Fe_1_-_a_-_bNi_aCo_b)_1_
0_0_-_x_-_y_-_zM_xSi_yB_z
(atomic %), where M is at least one element selected from Mo, Nb, Ta, and W, 0.005≦a+b≦0.05, 2≦x≦6, y≦19
, 7≦z≦25, 20≦x+y+z≦30.
An Fe-based amorphous magnetic core for a saturable reactor with small variations in control magnetization characteristics, characterized in that the total control magnetization force Hr at Hz is 20 A/m or less, and the uncontrollable magnetic flux density ΔBd is 0.2 T or less. 2. Composition formula (Fe_1_-_z_-_bNi_aCo_b)_1_
0_0_-_x_-_y_-_zM_xSi_yB_z
(atomic %), where M is at least one element selected from Mo, Nb, Ta, and W, 0.005≦a+b≦0.05, 2≦x≦6, 8≦y ≦
16, 8≦z≦10, 20≦x+y+z≦30 An Fe-based amorphous magnetic core for a saturable reactor according to claim 1, characterized in that it is made of an amorphous alloy ribbon having the following relationships. 3. Hold in an inert gas atmosphere or vacuum for a certain period of time until the stress is almost completely relaxed above the Curie temperature, and apply a direct current or alternating current magnetic field of 0.5 Oe or more in the magnetic path direction at 1°C/min or more. Production of the above-mentioned Fe-based amorphous magnetic core for a saturable reactor, characterized in that it is cooled at an average cooling rate of 20°C/min or less, maintained at a temperature of 200°C or higher and lower than the Curie temperature for 0.1 hours or more and less than 5 hours, and then cooled to room temperature. Method. 4. Hold in an inert gas atmosphere or vacuum for a certain period of time until the stress is almost completely relaxed above the Curie temperature, then rapidly cool to room temperature, and heat the Curie temperature at 200°C or above while applying a direct current or alternating current magnetic field in the direction of the magnetic path. The method for producing the Fe-based amorphous magnetic core for a saturable reactor as described above, characterized in that the Fe-based amorphous magnetic core for a saturable reactor is cooled to room temperature after being heated to a temperature equal to or lower than the above temperature and maintained for 0.1 h or more and less than 5 h.