JPS60128248A - Low magnetostriction amorphous iron alloy - Google Patents

Abstract

PURPOSE:To obtain a low magnetostriction amorphous Fe alloy having high magnetic permeability comparable to that of an amorphous Co alloy by adding a specified element for accelerating the formation of an amorphous state and B to an Fe-Cr alloy or an Fe-Cr-Ni alloy. CONSTITUTION:An alloy having a composition represented by formula I (where G is at least one among Si, Ge, P and C, 0.08<=a<=0.17, 76<=x<=90 and y<=20) or by formula II (where G is at least one among Si, Ge, P and C, 0.08<=a<=0.17, b<=0.2, 76<=x<=90 and y<=20) is used as the material of the magnetic core of a magnetic head, a high-frequency transformer, a choke, a noise filter or the like. In the formula I , 0.09<=a<=0.15, 80<=x<=86 and 1<=y<=10 may be satisfied, and in the formula II, 0.09<=a<=0.15, 0.05<=b<=0.2, 80<=x<=86 and 1<=y<=10 may be satisfied. A molten alloy having said composition is made amorphous by rapid cooling on a roll rotating at a high speed because Si, Ge, P or C is contained, and an amorphous alloy having high magnetic permeability and a remarkably low saturation magnetostriction constant due to Cr is obtd.

Description

[Detailed description of the invention] [@Men's technical field] Fukumyo is! #lc-based low magnetostriction amorphous alloy (two related)

[Technical background of the 1996 Ming era and its problems] Conventional magnetic head, high frequency transformer, choke.

Irmo's (2, permalloy, ferrite, sendust, Kei A) are used as magnetic core materials for noise filters, etc.
There are crystalline materials such as m.

The AL characteristics required for this magnetic core material include magnetic permeability, magnetic flux density, etc. Permalloy as mentioned above.

Since sendust, silicon steel, and the like have a small resistivity, their magnetic permeability decreases in the high frequency region ζ2, resulting in an increase in iron loss. Further, since ferrite has a large resistivity, it is possible to obtain high-speed g & ratio and low iron loss in the high frequency region, but the magnetic flux density is as small as about 5000 G at most, and each has only advantages and disadvantages.

In contrast, amorphous alloys have been developed which exhibit excellent magnetic properties such as high magnetic permeability and low coercive force.

Among these, a Co-based amorphous alloy having a composition ratio of about Co:Fe = 9426 has a saturated magnetostriction strength (λ,).
is close to O and has a high magnetic permeability of 10′, so
Currently being used in audio magnetic heads, etc.

On the other hand, Fe-based amorphous negative alloys are being used as amorphous alloys with high magnetic flux density. Co-based amorphous alloys are at most Q KG
On the other hand, Fe-based amorphous negative alloys can obtain as much as 16 KGa degrees, for example, and are a promising material because they enable the miniaturization of magnetic cores. In addition, it is cheaper in cost than Co, and the Fe-based material has a smaller conductive magnetic anisotropy, so it has great manufacturing advantages.

However, F'e-based non-matrix crystalline alloys generally have a large λ. there were.

[Purpose of the invention]

The present invention has been made in consideration of the above points, and an object thereof is to provide an iron-based low 1a strained amorphous alloy with small magnetostriction and a heavy magnetic flux similar to that of a Co-based amorphous alloy. .

[Summary of the invention]

(7e1-a Cra)*QyBsoo-x-y Song"' ■ (G is at least one element selected from St, Ge, P, and C, &g) C@': j is each 0. 08
≦a≦0.17°76≦X≦90. It is an iron-based low magnetostriction amorphous alloy characterized by a number satisfying the relationship y≦20.

That is, the present invention makes it possible to realize a significantly small saturation@strain constant (λ) by substituting a specific amount of Cr for a part of Fe-based amorphous Fe. .

The reason for limiting each component of ζ2 will be shown below.

Or greatly contributes to the reduction of magnetostriction, and when 0 formula or a is less than 0.08, λ#>5X10-' is large, and the deterioration of magnetic permeability and iron loss due to stress is significant. becomes. When a exceeds 0.17 t-, the magnetic flux density increases, for example, by 50
It drops below 00 G and becomes unusable. Therefore, 0.
The range is 08≦a≦0.17.

In addition, the content of Fe and Cr is not shown ■ xr in the formula: Yes, but
If X is less than 76, even if Cr i is changed, λ3
cannot be lower than 5 X 10-', and X is 9
Above 0 t- the amorphization is in the inner cone. Therefore, 76≦
The range is X≦90.

Further, G in the formula 0 is at least one element selected from Si*Ge and P+C, and has the effect of facilitating amorphization. When the '6a y of G exceeds 20, the melting point becomes high and it becomes difficult to make it amorphous. Therefore, it is set as 11 circles with y≦20. G starts to be effective with a small amount of indigo,
Practically speaking, the range of y≧1, particularly the range of l≦y≦10, is preferable. Furthermore, when St is selected as G, it becomes easier to become amorphous and the thermal stability of ζ improves.

Special 1Z 0.09≦a≦0.15, 80≦X≦86.
When satisfying the relationship 1≦y≦10, λ, ≦3 X 1
Since it shows a corrupted temporality as 0=, it is very preferable from a practical point of view.

Furthermore, by including Ni, it contributes to a reduction in magnetostriction together with Cr, increases the Curie temperature (T6), and facilitates the production 4 of an amorphous alloy.

That is, (Fe+-a-b Nba N1b)x Gy Bso
o-x-y・Song・■(G is St @ Ge * P
@ At least one element selected from C, a s
b*X*y are each 0. o8≦a゛≦OA7
e b ≦0.2 * 75 ≦x S 9t),
V ≦20 tl) What is indicated by IJJJ? It is an iron-based low magnetostriction amorphous alloy characterized by:

(2) In the formula, &, X, and y are limited for the same reason as in formula 0.

Tck can be increased by adding Ni t-, but if the addition 1itb exceeds 0.2, R
will decrease. Further, when N1 is added, λ decreases, and when b is less than 0.2, the magnetic flux intensity increases in the range.

In particular, in the range of 0.05≦b≦0.2, it is possible to obtain an excellent amorphous alloy with a magnetic flux density of 9 kG or more, λ, ≦2 X IF', and Tc≧150°C.

The iron-based low magnetostriction amorphous alloy according to the present invention can be obtained by preparing a molten alloy having a desired composition ratio, as is generally practiced.
It is obtained by cooling. For example, a single roll method is often used.

When used as a single-handed throw, for example, an amorphous alloy thin strip is wound into a desired shape (==) and then hardened by applying a resin mold. Even when stress is applied during molding, the degree of deterioration of magnetic permeability is small, making it very effective in practice.

〔Effect of the invention〕

The iron-based low magnetostriction amorphous alloy of the present invention described in detail above has a significantly small I'lJ magnetostriction foot;
It has features such as an extremely high a-rate and a small degree of deterioration of magnetic permeability due to stress, and since it is a material made from iron, it is inexpensive, and conventionally cobalt-based amorphous alloys were used. In addition to being used in various fields such as magnetic heads and saturable reactors, it can also be used as a magnetic core material for transformers, chokes, noise filters, etc., and is an extremely versatile material in industry.

[Embodiments of the invention]

Hereinafter, the present invention will be explained based on the implementation series. (Implementation row 1
~12 and Comparative Examples 1, 2.3) Amorphous alloys having the compositions shown in the table below were produced by a single roll method. That is, 1・−
Argon gas (gas pressure 0.81c9/cr/l)
), and the resulting thin layer was quenched to a width of 12
uIL, a thin strip sample with a thickness of approximately μm and a length of approximately 10 m 0) was prepared.

From this sample, the outer diameter is 10 myφ and the inner diameter is 61! A ring sample of Iφ was prepared and treated in the absence of a magnetic field at a temperature lower than the crystallization temperature and higher than the Curie point for 10 minutes. A secondary coil was wound around this, and the effective permeability of the 4Ia leather was measured using a Maxwell bridge (bias magnetic field = 2m06).

In addition, using the strain gauge method, the saturation magnetostriction constant is calculated as D
The crystallization temperature of each sample was measured using a TA (differential thermal analyzer).

Furthermore, the ring samples after the above-mentioned treatment were molded using epoxy resin, and then the effective magnetic permeability was measured using a Maxwell bridge to examine the degree of deterioration due to stress during resin molding. These results are shown in the table below. As is clear from the above table, the amorphous layers of Higakuya 1 to 3 have a magnetostriction constant (λ,) of 5
10-"i, the effective magnetic permeability is low even before resin molding, and the degree of deterioration of the effective magnetic permeability after +MJl1w molding is also large. In contrast, the amorphous magnetic permeability of Examples 1 to 12 The quality alloy has a saturation magnetostriction constant (λ,) of 5X
A high effective magnetic permeability of less than lO-' can be obtained, and the degree of deterioration of the effective magnetic permeability of the resin mold section is also very small.

In addition, the same method as described above (2yo') (Fe1-
A non-crystalline gold alloy (Cr, ) as Siy &o was prepared, and the Shōwa acupuncture strain rotation number λ and the sum magnetization σ were measured. Note that a sample vibrating magnetic force type was used to measure the saturation magnetization. The results are shown in Figure 1.

As is clear from Fig. 1, λ decreases by 1 as the content of Or increases, and when a≧0.08, λ becomes 5
It is below XlO-6.

Furthermore, (F'e(1,
o+-bCro, ooNib) 84siaBtt amorphous stitch was produced, and the magnetostriction constant λ of the cell 4u was measured. The results are shown in FIG.

As is clear from Figure 2, the saturation magnetostriction constant λ8 decreases as the Ni content increases, and by adding Ni, λ can be finely adjusted.

Also, (Feo, oo-b cro, 1°N1b) as
The change in T, (C) when changing N1fbe in the composition system of sisBtt is shown in the ks3 diagram. As is clear from Fig. 3, with the addition of NL (2Tc increases, b >
It can be seen that when it becomes 0.2, To decreases again.

Therefore, the range b≦0.2 is preferable, particularly 0.05≦b
In the range of ≦0.2, other characteristics (2) are also modified.

[Brief explanation of the drawing]

Figures 1 and 2 are diagrams showing the A ratio between the alloy composition and magnetic properties of the iron-based low magnetostriction amorphous alloy of the present invention, and Figure 3 is a diagram showing the A ratio between the alloy composition and magnetic properties of the iron-based low magnetostriction amorphous alloy of the present invention. FIG. 2 is a diagram showing the relationship between the chemical composition and the Curie temperature. Agent: Patent Attorney Noriyuki Kon (and 1 other person) Figure 1 Cr ((1) Figure 2

Claims (1)

[Claims] (1) (FJ -a Cra) x Gy n, oO
−、−. (G is 5ieGe, at least one element selected from P+C, a, x+y are each 0.08≦a≦0-17
+76≦x≦90 e y≦20 '7) An iron-based low magnetostrictive amorphous alloy. (2nd 0-09 ≦ a ≦ 0-15 + 80
The iron-based low magnetostrictive amorphous alloy according to claim 1, which satisfies the following relationship: ≦ x ≦ 86 * 1 ≦ y ≦10. f3) (FeJ-a-b CraNlb)zGyB
soo-ry (wherein, G is E3s r Get P
r C ka b A han le at least one element, &
*b*XeV is each 0.08 ≦a ≦0.17
, b≦0.2, 76≦x≦90, y≦
An iron-based low magnetostriction amorphous alloy characterized by having a number satisfying the relationship of 20). (4) 0.09≦a≦0.15, 0.05≦b≦
The iron-based low magnetostrictive amorphous alloy according to claim 3, which satisfies the following relationship: 0.2.80≦X≦86.1≦y≦100).