JPH0270041A - Cobalt-based amorphous alloy reduced in magnetostriction and having high magnetic permeability - Google Patents

Abstract

PURPOSE:To reduce coercive force and magnetostriction, to increase magnetic permeability, and to improve the thermal stability of magnetic properties by incorporating specific amounts of one or more elements among B, Be, Al, Si, Ge, and Sn to an amorphous Co-Zr alloy. CONSTITUTION:An amorphous alloy has a composition consisting of, by atomic ratio, 5-15% Zr, 4-15% (where B content is regulated to <7%) of one or more elements among B, Be, Al, Si, Ge, and Sn, and the balance essentially Co. Respective additive alloys have amorphous substance-forming capacity, reduce the Curie temp., facilitate heat treatment, and have a magnetostriction-reducing effect. If necessary, <=10% Fe, <=20% Ni, <=10% Mn and/or Cu, <=10% of one or more elements among Ru, Rh, and Pd, and <=5% of one or more elements among Ti, Hf, Y, and lanthanides are incorporated to the above composition, or further, <5% of one or more elements among Cr, Mo, W, V, Nb, and Ta is incorporated to the above composition.

Description

DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a cobalt-based amorphous alloy, and particularly the present invention relates to an amorphous alloy for magnetic cores having low magnetostriction and high magnetic permeability.

[Conventional technology]

Conventionally, Mo permalloy (JISPC grade permalloy) has been mainly used as a material for small magnetic cores for weak electric currents, such as wound cores and magnetic heads, but these alloys must be subjected to extremely harsh conditions in order to obtain their properties. In particular, in order to minimize iron loss when used as a wound core, it must be made into a thin ribbon of 100 to 50 μm, and the rolling and heat treatment steps for this purpose are complicated. Another problem is that when used as a magnetic head for a long time, the recording characteristics deteriorate significantly due to wear caused by the magnetic tape.As a result, in addition to the above-mentioned permalloy alloys, ferrite and alperm are currently used as magnetic alloys for magnetic heads. Alternatively, highly hard materials such as Sendust are also used.

Among these, ferrite exhibits excellent electromagnetic properties at high frequencies, and has low wear and deformation, but it has low saturation magnetization, tends to cause recording distortion, and has a high signal-to-noise ratio (S/N). ) is a wood defect. Although Alperm and Sendust have excellent magnetic properties, these materials have the disadvantage of poor malleability and machinability.

As mentioned above, the conventionally used materials for small magnetic cores have various drawbacks, and a fully satisfactory material has not been obtained.

[Problems to be Solved by the Invention] In response to this problem, amorphous metal magnetic old materials have recently attracted attention. This material has high electrical resistance in addition to its high magnetic properties, and because it can be obtained essentially in the form of a thin strip due to its manufacturing process, it is mainly used as an AC magnetic core + O material. . Zunawara, Fe, C.

An amorphous alloy with a composition containing approximately 20 at.% of Ni and other amorphous elements such as P, C, B, and Si has a higher retention property than the various crystalline high permeability metal materials listed in -1-. The magnetic force is small,
It is known that equivalent magnetic properties with high magnetic permeability can be obtained.

However, although Gore et al.'s amorphous alloy generally needs to be heat treated at a temperature below its crystallization temperature in order to improve its magnetic properties, this heat treatment actually increases its brittleness.
The mechanical properties, especially the abrasion resistance, are low despite the high hardness. Furthermore, for example Feao) Jjao
It also has the disadvantage of poor magnetic thermal stability, as seen in the PI4Bb amorphous alloy.

Moreover, amorphous alloys containing approximately 20 atomic percent of metalloid elements such as P, C, B, and Si have a hardness of 800 to 1100.
Due to the high Hv, there is a problem that the life of the die used to punch out the desired shape is extremely short.

The present invention does not have the above-mentioned drawbacks of crystalline high permeability metal materials for small magnetic cores that have been in practical use, and also eliminates the above-mentioned drawbacks of known amorphous alloys, and has a high coercive force and magnetostriction. For small magnetic cores that are small, have high magnetic permeability, and have excellent thermal stability of these magnetic properties, as well as good machinability such as punching or cutting, and less embrittlement due to heat treatment. The purpose is to provide an amorphous alloy.

[Means to solve the problem]

As an amorphous alloy well suited for such purposes, the present invention includes (1) Zr in an atomic ratio of 5 to 15% and the following (a)
A cobalt-based amorphous alloy with low magnetostriction and high magnetic permeability, consisting of 4 to 15% of one or more selected from the group (b), and the remainder being substantially Co.

(b) Either one or two selected from B, C, and P
More than species: less than 7% (b) Be, Al, Si, Ge, Sn, S
b, any one or two or more selected from In =
15% or less (2) Atomic ratio: 5 to 15% of Zr, 4 to 15% of one or more selected from the following groups (a) and (b), and the following (c) , (d), (*)
, (f), ()), and (h) 20% or less of any one or two or more selected from the group, and the remainder is substantially Co.
A cobalt-based amorphous alloy with low magnetostriction and high magnetic permeability.

m Any one or two or more selected from B, C, and P: less than 7% (o) Be, Al, Si, Ge, Sn, S
b, One or more selected from In: 15% or less (c) Fe: 10% or less (d) Ni: 20% or less (*) Any one selected from Mn, CuO Or 2 types: 10% or less () Any one or more selected from Tc, Ru, Rh, PdO: 10% or less ()) Ti, Iff, Sc, Y, selected from lanthanide elements One or more types: 5
% or less (h) Any one or more selected from Cr, Mo, W, V, Nb, Ta: less than 5% (3) Atomic ratio, Zr is 5 to 15%, the following (I) )(n
) any one or two or more selected from the group of 4
-15%, 5-16% of one or more selected from the following group (H), and the remainder substantially C.

A cobalt-based amorphous alloy with low magnetostriction and high magnetic permeability. However, the sum of any one or more elements selected from the following groups C) and (B) and any one or more elements selected from the following group (H): is less than 20%.

(Any one or more selected from B, C, and P: less than 7%, (U) Be, Al, Si, Ge, Sn, S
b. Any one or more selected from In: 15% or less, (ch) Cr, Mo, W, V,
Any one or more selected from Nb and Ta = 16% or less (4) Zr in atomic ratio of 5 to 15%
, any one selected from the following groups (A) and (TI)
4 to 15% of one or more species; 5 to 16% of one or more species selected from the group (H) below;
Below (c).

20% or less of any one or more selected from the group of (d), (e), (f), and ()), and the remainder is essentially cobalt with low magnetostriction and high magnetic permeability. Base amorphous alloy. However, any one or more elements selected from the following groups (a) and (b) and the following (ch)
The total amount of one or more elements selected from the group is 20% or less.

(One or more selected from B, C, and P = less than 7% (o) Be, Al, Si, Ge, Sn, S
(c) Fc: 10% or less; (d) Ni: 20% or less; (n) Mn, Cu. Any one or two selected from: 10% or less, (to) Tc Ru, Rh, P (+ Any one or two or more selected from: 10% or less, ()) Ti, Iff , Sc, Y, any one or two or more selected from the lanthanide elements: 5
% or less, (ch) Cr, Mo, W, V, Nb, Ta
We suggest any one or two or more selected from: 16% or less.

[For production]

Normally, solid metal 2 alloys have a crystalline structure, but by rapidly cooling an alloy with an appropriate composition from a liquid state, or by using various techniques such as vapor deposition, sputtering, plating, etc. A solid with an amorphous structure without a periodic atomic arrangement similar to that obtained is obtained. Such metals are called amorphous metals or amorphous alloys (hereinafter, amorphous metals and amorphous alloys are collectively referred to as amorphous alloys).

It is well known that this amorphous alloy can be obtained by appropriately using various techniques as mentioned above (for example, Japanese Patent Laid-Open No. 49-91014). It is known that an amorphous alloy can be obtained in a wider composition range than that obtained by a liquid quenching method.

As an example of the liquid quenching method, a liquid is placed on the outer peripheral surface of one disc rotating at high speed as shown in Figure 1 (al), or between two rolls rotating at high speed in opposite directions as shown in Figure 1 (bl).
There is a method in which liquid metal is continuously jetted out and rapidly solidified on the surface 1- of a rotating disk or twin rolls at a cooling rate of about 104 to 06°C/sec.

Looking at the composition of this amorphous alloy, it is an alloy system that combines transition metal elements and metalloid elements (the amount of metalloids is approximately 10 to 3
Two types of alloy systems are known: 0 atomic %) and an alloy system that combines two or three types of transition metal elements with different atomic radii.

As an example of the latter alloy system, an amorphous alloy consisting of an iron group element, which is a transition metal element, and zirconium is known. It was newly discovered that there are alloys with ferromagnetism in
, -30734; Patent No. 1314339),
A patent application was filed first.

The present inventors have conducted more detailed research on amorphous alloys containing Co as a main component among the above-mentioned amorphous alloys containing iron group elements and zirconium, in order to mainly use them as small magnetic core materials. , an amorphous alloy obtained by ultra-quenching an alloy having a predetermined composition from the liquid phase or gas phase, or an alloy obtained by subjecting it to a predetermined heat treatment in a magnetic field or under stress,
It has low coercive force and magnetostriction, high magnetic permeability, thermally and temporally stable magnetic properties, high wear resistance, and is less susceptible to embrittlement than conventional amorphous alloys containing large amounts of metalloid elements. (And the machinability of punching, polishing, cutting, etc. is good.) This was newly discovered and the present invention was conceived.

In addition to the above features, the amorphous alloy of the present invention also has the following features. Mechanical pressure hardly changes the above properties. For example, magnetic permeability, coercive force, residual magnetic flux density, etc. remain almost constant even when tension is applied to the alloy, and are insensitive to external stress. Therefore, the alloy of the present invention
Since the magnetic properties are hardly deteriorated by machining such as cutting, punching, or polishing, it is very advantageous when using thin pieces obtained by punching, polishing, or cutting the alloy into a predetermined shape by any method. Further, the alloy of the present invention has an electrical resistance of 20 to 14. High OpΩcm and 20
Since it can be manufactured into a ribbon shape of about 40 μm, it is an extremely suitable alloy as a small magnetic core material with good high frequency characteristics.

Next, the amorphous alloy of the present invention will be explained based on experimental data.

The amorphous alloy used in this experiment was a ribbon sample with a width of about 2 ays and a thickness of about 20 μm. The sample was prepared by continuously jetting a molten alloy having the composition of the present invention onto the outer peripheral surface of a disk rotating at high speed as shown in FIG. 1(a).
It was obtained by rapid solidification on the surface of a rotating disk at a cooling rate of about 105 to 106°C/sec.

Furthermore, the amorphous alloy obtained by ultra-quenching is about 350 to 50%
After annealing in the temperature range of 0° C. and below the crystallization temperature of the alloy, it was cooled to room temperature and the magnetic properties were measured.

Table 1 shows the component composition and magnetic properties of the amorphous alloy of the present invention, some known metal-metalloid amorphous alloys, and various crystalline high magnetic permeability metal materials commonly used in the past. showed that.

(Left below) In Table 1, M1 to 5 are alloys of the present invention, 78 is a known Fe-N1-P-B system and Co-4e-5i3 system amorphous alloy, and lt and 9.10 are respectively Commercially available high hardness permalloy and ferrite.

As can be seen from Table 1, the alloy of the present invention has superior magnetic properties compared to commercially available high permeability metal materials. for example,
The alloy of the present invention has a coercive force equal to or higher than that of the high hardness permalloy of Comparative Examples Mo and No. 9. Moreover, it can be said that it is an alloy that has a high maximum magnetic permeability and a saturation magnetic flux density of less than I-.

It can be seen that the M9 hardness of the alloy of the present invention is approximately 1.7 to 2 times higher than that of high-hardness permalloy, and is approximately equal to that of ferrite. For example, the Vickers hardness of the alloys M2 or 1.5 in Table 1 is 670.678, respectively, and these values are almost the same as the hardness of ferrite.

Co□+, MOloBs, which are alloys similar to the alloy of the present invention
Zr.

Figure 2 shows the change in effective magnetic permeability at I Ktlz when a thin strip sample of an amorphous alloy was wound into a coil shape and annealed for 20 minutes each in the range of 150 to 490°C. .

The effective permeability of quenched material without heat treatment is 1500-50
However, by annealing this alloy at a temperature below the crystallization temperature in a non-oxidizing atmosphere or in vacuum, the magnetic properties can be greatly improved. The effective permeability of the sample is 3
It can be seen that the value increases to about 0,000 to 40,000.

FIG. 3 shows Coa1MO9Zrl, which is a similar alloy system to the present invention. Regarding quenching materials for amorphous alloys,
The results of investigating the influence of tension on coercive force and residual magnetic flux density are shown.

According to the results, almost no effect of tension was observed in the similar alloy systems, and therefore, it is predicted that the magnetic properties of the alloys of the present invention will hardly deteriorate due to mechanical processing such as cutting and punching. Therefore, it is extremely advantageous to use the alloy of the present invention as a magnetic core material.

As shown in FIG. 4, the effective i3 boric rate of MO permalloy is 1. OKt(Z
rl.

It was found that the effective magnetic permeability of the amorphous alloy does not change up to a frequency of around 20 KHz, and has excellent properties within the audible frequency range. On the other hand, it can be seen that it has a much higher effective magnetic permeability over a wide frequency range than Alperm.

From this, it can be seen that the alloy of the present invention is a material suitable for magnetic throats, small lances for home appliances, and the like.

Below, the alloy according to claim 1 (alloy of the first invention), which describes the reason for limiting the composition of the alloy of the present invention, contains Zr having the same effect as well as Zr having the ability to form an amorphous state. B, C, P
(Group A elements), Be, △l, Si, Sn, 5
Since it is an alloy consisting of elements such as bIn (an element in the oral group), the content of Zr can be particularly kept low.

That is, when Zr is 5% or more, an amorphous alloy having high magnetic permeability can be obtained. On the other hand, if it exceeds 15%, the magnetic flux density will drop significantly, so it needs to be within the range of 5 to 15%, and even better magnetic properties can be obtained within the range of 6 to 12%.

Next, the (A) group and (■) group elements will be explained.

B, C, and F belonging to group (a) are elements that have the ability to form amorphous materials, or if they are contained in an amount of 7% or more, they do not cause a decrease in magnetic flux density and do not affect the thermal properties of magnetic properties. It also deteriorates the stability over time, or lowers the embrittlement temperature, so it should be less than 7%.

(11) Belonging to group Be, Al, Si, Ge,
Sn, Sb, and In are elements that promote amorphization, but if they exceed 15%, the magnetic flux density will drop significantly and the alloy will become brittle, so they must be kept at 15% or less. It is desirably less than 10%.

J- B, C, P belonging to groups (a) and (b),
BeAl Si Ge, Sn, Sb, and In, like the V and Vl group elements, are elements that lower the Curie temperature, facilitate heat treatment, and have the effect of reducing magnetostriction, but the total amount of these elements is If it is less than 4%, the effect will be small, while if it is more than 15%, the magnetic flux density will be significantly lowered and the embrittlement temperature will be significantly lowered. Therefore, the total amount of these elements needs to be in the range of 4 to 15%, more preferably in the range of 5 to 13%, and optimally in the range of 5 to 10%.

Next, (c), (d), (ne), (f), )) Explain the reason for limiting the elements in the group.

Fe belonging to group (c) has the effect of increasing magnetic flux density, but it also increases magnetostriction at the same time, so it is preferable to keep it at 10% or less, more preferably 5% or less.

Ni belonging to group (d) reduces magnetostriction, but at the same time it also reduces crystallization temperature and magnetic flux density, so 20%
It is preferable that the content be below, more preferably 10% or less.

Mn, which belongs to group (e), has the effect of increasing resistivity and decreasing coercive force, and Cu is an element that improves wear resistance without impairing magnetic permeability and coercive force, but both If the amount is larger than 1, the saturation magnetic flux density will decrease and the alloy will become brittle.
It is preferable to make it 0% or less.

If the amount of any one of Tc, Ru, Rh, and Pd belonging to the group (f) is more than 10%, the magnetic permeability will increase, but the magnetic flux density will decrease, so it is preferable to make it less than 10%.

In addition, Ti, t(f, Sc, Y) belonging to group (G)
and lanthanide elements are elements that promote amorphization and increase hardness; however, if either of these elements is present in a small amount (if one of these elements exceeds 5%, the alloy will become brittle, so it should be kept below 5%). is preferred.

Next, Cr, Mo, IA, V, Nb, and Ta belonging to group (H) are selectively included as one of the other elements (C) to (G) in the second invention alloy.
Group or group III elements are elements that facilitate heat treatment because they assist in amorphization and have the effect of lowering the Curie temperature. Especially when you want to obtain an alloy with high magnetic flux density,
5% of at least one element selected from this group (H)
It is preferable to make it less than

In the alloy of the second invention, one or more elements selected from the groups (c), (d), (ne), (f), (g), and (h) are: Their total amount is 20
If it exceeds 20%, the magnetic flux density or magnetic permeability will drop significantly, so it needs to be 20% or less. Preferably 15
% or less, and preferably 10% or less to obtain a higher magnetic flux density.

On the other hand, in the fourth invention alloy, Cr, Mo, IA, V, Nb, Ta belonging to the group (H)
As in the case of the second invention, the V or group III element facilitates heat treatment because it aids amorphization and has the effect of lowering the Curie temperature, and also has the effect of reducing magnetostriction. However, in the fourth invention, if the content of the (H) group element is less than 5%, the effect will be small, and if it is more than 16%, the saturation magnetic flux density will be significantly reduced. Therefore, the content of these (H) group elements needs to be 5 to 16%.

In addition, in this fourth invention alloy, the total amount of at least one element selected from groups (A) and (D) and at least one element selected from group (H) If it exceeds 20%, the alloy will become brittle or the magnetic flux density will drop significantly, so the total must be 20% or less. The content is desirably 15% or less.

And (c), (d), (*), (to), ()), (
H) If the total content of any one or more elements selected from the group exceeds 20%, the magnetic flux density or magnetic permeability will decrease significantly, so it is necessary to limit the content to 20% or less.

As explained above, the alloy of the fourth invention of the present invention contains an appropriate amount of the metalloid, the above-mentioned ■ and/or group ■ element, and the above-mentioned (c), (d), (e), (h), (). Since it contains at least one element selected from the group ), it is not only easy to manufacture, but also has equivalent characteristics such as high magnetic permeability and almost zero magnetostriction.

Next, regarding the alloy of the third invention of the present invention, B, C, P, Be, AlS belonging to group (a) and group (b)
Elements such as i, Sn, Sb, and In that have the ability to form an amorphous state, and Zr that also has the ability to form an amorphous state.
The contents of are the same as in each of the above-mentioned inventions 1.2.4. That is, when Zr is 5% or more, an amorphous alloy having high magnetic permeability is formed. On the other hand, if it is more than 15%, the magnetic flux density will drop significantly, so it needs to be in the range of 5 to 15%, and even better magnetic properties can be obtained within the range of 6 to 12%.

(If B, C, and P in the above groups are contained in an amount of 7% or more, they not only cause a decrease in magnetic flux density, but also deteriorate the thermal and temporal stability of magnetic properties, or cause a decrease in embrittlement temperature. Less than % is better.

In addition, (TI) group Be, Al, Si, Ge,
If Sn, Sb, or In exceeds 15%, the magnetic flux density will significantly decrease and the alloy will become brittle, so it is necessary to keep the content to 15% or less, and preferably less than 10%.

If the total amount of each element belonging to the above groups (A) and (TI) is less than 4%, the effect will be small. However, 15%
When the amount is larger than that, the magnetic flux density and the embrittlement temperature are significantly lowered. Therefore, the total amount of these elements is 4~
It needs to be within a range of 15%, more preferably within a range of 5 to 15%, and optimally within a range of 5 to 10%.

(H) Cr, Mo, IA, V, Nb belonging to group
, Group III or Group III elements such as Ta facilitate amorphization and have the effect of lowering the Curie temperature, making heat treatment easier, and also have the effect of reducing magnetostriction;
If it is less than 16%, the effect will be small, and if it is more than 16%, the saturation magnetic flux density will decrease significantly.
It needs to be in %.

Further, in the third invention alloy, the above (a) and (o)
If the total of any small element selected from the group (both group 1 and at least one element selected from group (H)) exceeds 20%, the magnetic flux density will decrease significantly.

Therefore, it is necessary to reduce the total amount to 20% or less. The content is desirably 15% or less.

As described above, since the alloy of the third invention of the present invention contains an appropriate amount of semimetal and group V and/or group II elements, it is not only extremely easy to manufacture, but also has high magnetic permeability and almost zero magnetostriction. Obtainable.

Table 2 shows the relationship between the configurations of the first to fourth inventions described above.

The amorphous alloy of the present invention can be obtained by annealing an amorphous alloy material obtained using the various techniques described above at a temperature below the crystallization temperature of the alloy material, and then rapidly or slowly cooling it. can. In this case, it is advantageous that the annealing atmosphere is non-oxidizing or that the annealing is carried out in a vacuum. However, if the magnetic properties are not impaired even if the surface of the amorphous alloy is oxidized by a small amount of oxygen, the oxide film formed thereby has an effect as an insulating film.

When the amorphous alloy of the present invention is annealed at a temperature of 150° C. or lower than the crystallization temperature and then rapidly or slowly cooled, processing strain can be removed and magnetic properties can be improved. Furthermore, when the amorphous alloy of the present invention is annealed at a temperature below the crystallization temperature under the action of at least one of a magnetic field or stress, and then rapidly or slowly cooled, an alloy with better magnetic properties can be obtained. .

As a method for improving the magnetic properties by annealing in the magnetic field, a method invented by one of the inventors of the present invention and disclosed in Japanese Patent Application Laid-Open No. 5173923 can be used.

〔Example〕

Example 1 Co8.0 of the alloy of the present invention. Mo. Zroo amorphous alloy and FeaoNiaoPxBb amorphous alloy as a comparative example.
Table 3 shows the results of a bending test performed after heat treatment at 0°C and 400°C for 30 minutes each.

Note that the amorphous alloy used in Examples 1 to 4 was
1j This is a ribbon sample with a thickness of approximately 20 μm.

Generally, as a method for evaluating the embrittlement of amorphous alloys, the distance between two parallel plates is measured, and the L value when the specimen breaks is determined.
A method of determining the fracture strain (where t indicates the thickness of the specimen) using the following formula was adopted, and the results shown in Table 2 were also based on this method.

In Table 2, ε, >1 indicates that the sample will not break even if it is bent until it is completely in contact with the sample.

As is clear from Table 2, the alloys of the present invention hardly become brittle even when subjected to heat treatment to obtain predetermined magnetic properties.

Example 2 Co77Mo in the alloy of the present invention. B2 Zro + amorphous alloy was annealed in a magnetic field at 420°C for 30 minutes, resulting in a coercive force of 10 mOe and effective permeability (I KHz) of 27.0.
00, but when it was then aged at 150° C. for 10,000 minutes, there was no change at all in both coercive force and effective magnetic permeability.

Example 3 CoBOMO9, sZroo, which is one of the alloys of the present invention,
s amorphous alloy, and C070,:+Fe as a comparative example
4.7sj+sB+.

The amorphous alloys were tested for wear resistance against magnetic tape, and the results are shown in Table 4.

The amorphous alloy samples used were all about 20 μm thick and about 2 mm wide, and after being subjected to optimal heat treatment to obtain the desired magnetic properties, they were placed on an AutoReply 1 type Cassent tape recorder (Akai GXC). -715D), and the sliding speed of the magnetic tape was 4.95 cm.
After testing for 50 hours and 100 hours at a speed of 100 mm/sec, the amount of wear on the specimens was measured.

As shown in Table 4, the wear amount of the alloy of the present invention is Co7o,
17 compared to 3Fe4.7S115BIO amorphous alloy
It can be seen that it has excellent abrasion resistance of 3 or less.

Table 4 Example 4 C0eoCrooZroo and C08oV in the alloy of the present invention
+oZro.

Amorphous alloy and C070, *Fea, 7 as a comparative example
si+sB+.

Table 5 shows the results of cutting tests for three types of amorphous alloys.

The test method is to repeatedly cut a specimen approximately 20 μm thick and 21 pieces wide using a shear (shearing machine) until the upper and lower blades bite into the specimen due to blade wear and reach a state where cutting becomes impossible. The number of cuts was investigated. The Vickers hardness of the blade used was 650.

As shown in Table 5, all of the alloys of the present invention are C0Fe-5
The blade life of Beshear is more than four times longer than that of the i-B amorphous alloy, and it can be seen that the machinability of the alloy of the present invention is superior to that of conventionally known amorphous alloys. .

Table 5 While applying a magnetic field of 200 De in the longitudinal direction, each alloy was heated at a temperature 50°C lower than its crystallization temperature for 20 minutes, cooled, and then wound into a thin ribbon to form a toroidal sample to examine its magnetic properties. Ta. It was found that all the alloys had a high saturation magnetic flux density of 8000 G or more, a low coercive force, and a high maximum magnetic permeability, and were useful as wound magnetic cores.

Table 6 Invention Alloy Inner Box For amorphous alloys having the compositions shown in Table 6, a thin ribbon with a shaft fishing IQmm and a thickness of approximately 30 μm was used as a thin ribbon of CreJbz Mob Zrq amorphous alloy of the present invention alloy (
A magnetic head core (15 mm thick, approximately 30 μm thick) was punched out into a magnetic head core shape using the first cutting and notching method, and then assembled into a magnetic head core for cassette tapes together with commercially available sendust and permalloy cores of the same shape. C2
Abrasion resistance tests were carried out using the γ-iron oxide tape under two different environments: 50% relative humidity and 75% relative humidity at 40° C. using a skein, a knotweed, and a stick. The result is the fifth
As shown in the figure.

The alloy of the present invention has better wear resistance than the alloy of Permalonite Sendust, and exhibits particularly good wear resistance, especially in hot and humid environments where other alloys are very susceptible to wear. I understand that.

〔Effect of the invention〕

As described above, the alloy of the present invention not only has excellent soft magnetic properties such as low coercive force and high magnetic permeability, but also has particularly high wear resistance. It is easier to manufacture and easier to cut and punch than conventional amorphous alloys containing large amounts of metalloid elements.

Since it has the great feature that machining such as polishing is much easier, it can be used very suitably as a magnetic core material for magnetic joints, high frequency transformers, etc.

[Brief explanation of the drawing]

Figure 1 is a route diagram showing two examples of equipment used for ultra-quenching the alloy of the present invention from a molten state, and Figure 2 is a diagram showing two examples of equipment used to ultra-quench the alloy of the present invention from a molten state. Figure 3 shows the change in effective magnetic permeability (I KHz) during annealing at 150 to 490°C for 20 minutes in a magnetic field. Figure 4 shows the relationship between frequency and effective magnetic permeability of Co76We B6 Zroo amorphous alloy. Figure 5 shows the influence of coercive force and residual magnetic flux density on magnetic head core materials. FIG. 3 is a diagram showing a comparison of abrasion properties. 1... Molten alloy, 2... Rapidly solidified alloy, 3...
... Cooling rotating disk, 4... rolls. Patent Applicant Masumoto Kakukai Applicant Sumitomo Special Metals Co., Ltd. Agent Patent Attorney Jun Ogawa Tamayo Patent Attorney Morio Nakamura G D1 Hori IT! Sanjima nη ○I-( f-7 [!) 7 Condolences (90111E) 9,7 * 猾'iRr (14 Procedural Amendment June 28, 1999 Commissioner of the Japan Patent Office Yoshi 1) Moon Takeshi Paragraph 1 Patent application pursuant to the provisions (2) Name of the invention Relationship to the case of a person who corrects a cobalt-based amorphous alloy with low magnetostriction and high magnetic permeability Patent applicant address 3-8-22 Uesugi, Aoba-ku, Sendai, Miyagi Prefecture Name Ken Masumoto Address: 4-7-19 Kitahama, Chuo-ku, Osaka-shi, Osaka Name: Sumitomo Special Metals Co., Ltd.

Claims (1)

[Claims] 1. In terms of atomic ratio, Zr is 5 to 15%, and any one or two or more selected from the following groups (a) and (b) are 4
A cobalt-based amorphous alloy with low magnetostriction and high magnetic permeability, consisting of ~15% and the remainder substantially Co. (a) One or two selected from B, C, and P
Species or more: Less than 7% (b) Any one or two or more selected from Be, Al, Si, Ge, Sn, Sb, In: 15% or less 2, Zr in atomic ratio 5 to 15 %, any one or two or more selected from the following groups (a) and (b) 4
~15%, 20% or less of any one or more selected from the following groups (c), (d), (e), (f), (g), and (h), the remainder being A cobalt-based amorphous alloy with low magnetostriction and high magnetic permeability, consisting of Co. (a) One or two selected from B, C, and P
Species or more: less than 7% (b) Any one or more selected from Be, Al, Si, Ge, Sn, Sb, In: 15% or less (
c) Fe: 10% or less (d) Ni: 20% or less (e) One or two selected from Mn and Cu
Species: 10% or less (f) Any one or more selected from Tc, Ru, Rh, Pd: 10% or less (g) Selected from Ti, Hf, Sc, Y, lanthanide elements Any one kind or two or more kinds: 5% or less (h) Any one kind or two or more kinds selected from Cr, Mo, W, V, Nb, Ta: less than 5%3, atomic ratio, Zr 5 to 15%, one or more selected from the following groups (a) and (b) to 4
A cobalt-based amorphous alloy with low magnetostriction and high magnetic permeability, consisting of 15% to 15%, 5 to 16% of one or more selected from the group (H) below, and the remainder substantially Co. However, the sum of any one or more elements selected from the following groups (a) and (b) and any one or more elements selected from the following group (h) is less than 20%. (a) One or two selected from B, C, and P
Species or more: Less than 7% (B) Any one or more selected from Be, Al, Si, Ge, Sn, Sb, In: 15% or less, (H) Cr, Mo, W, Any one or more selected from V, Nb, Ta: 16% or less 4. Zr in atomic ratio of 5 to 15%, selected from the following groups (a) and (b) 4 of any one or two or more types
~15%, any one selected from the group (H) below
Species or two or more: 5-16%, below (c), (d),
Any one selected from the group of (E), (F), (G)
A cobalt-based amorphous alloy with low magnetostriction and high magnetic permeability, consisting of 20% or less of a species or two or more species, and the remainder substantially of Co. However, the sum of any one or more elements selected from the following groups (a) and (b) and any one or two or more elements selected from the following group (h) is less than 20%. (a) One or two selected from B, C, and P
Species or more: Less than 7%, (B) Any one or more selected from Be, Al, Si, Ge, Sn, Sb, In: 15% or less, (H) Cr, Mo, W, One or more selected from V, Nb, Ta: 16% or less, (c) Fe: 10% or less, (d) Ni: 20% or less, (n) Mn, Cu. One or two of your choice
Species: 10% or less (f) Any one or more selected from Tc, Ru, Rh, Pd: 10% or less (g) Ti, Hf, Sc, Y, lanthanide elements One or more selected types: 5% or less