JPS58167744A - Amorphous magnetic alloy thin plate for magnetic head - Google Patents

Abstract

PURPOSE:To provide an amorphous magnetic alloy thin plate free from undesired slag formation at the leading end of a jet nozzle in forming the same into a thin film in the atmosphere according to a high speed quenching process, constituted by combining Mn, Al and vitrifiable elements with an Fe group transition metal element. CONSTITUTION:Mn and Al are added to an Fe group transition metal element comprising Co or/and Fe and a vitrifiable element is combined with the resulting composition to obtain an amorphous magnetic alloy thin plate for a magnetic head having a composition shown by the formula. The plate thickness of this thin plate is about 10-200mum and usually prepared by a method wherein an alloy having a corresponding composition is usually melted and the resulting melt is subjected to super-quenching at a cooling speed of 10<4> deg.C/sec from a liquid phase to be solidified. This thin plate is easy in heat treatment, high in saturation magnetic flux density and extremely good in anti-wear property, corrosion resistance or punchability and, therefore, extremely favorable as a material for a magnetic head.

Description

[Detailed description of the invention] ■ Background of the invention Technical field The present invention relates to an amorphous magnetic alloy thin plate for a magnetic head.

Prior art and its problems As one of the magnetic head forming materials, an amorphous magnetic alloy thin plate containing mainly Co as an iron group transition metal element and further containing about 20 to 5 Oat% of a lath element is known. There is.

A proposal has been made to add Mn to such an amorphous magnetic alloy (Japanese Patent Application Laid-Open No. 164051/1982).
.

This alloy to which more Mn is added can reduce the Chieri temperature Tc without affecting the saturation magnetic flux density, and the difference from the crystallization temperature Tx (TX - Tc) is large. The magnetic permeability is improved, and a high saturation magnetic flux density can be obtained.

However, when KMn is added in this way and a molten Mn-containing master alloy is attempted to be made into a thin plate using a high-speed quenching method, the following disadvantages occur.

In other words, if the atmosphere in which WI hot water is injected from the injection nozzle to the cooling body is a vacuum or inert atmosphere, and rapid cooling is performed in the atmosphere without using surrounding air, a slag layer will be formed at the tip of the injection nozzle. , Continuous groove-like defects are generated on the surface of the thin plate obtained by this, and the surface properties of the thin plate are deteriorated.
This slag layer may stop the molten metal from ejecting, making production impossible. For this reason, there are inconveniences such as not being able to manufacture a large amount of thin plates all at once and having to replace the nozzle frequently.

In addition, the punchability of the obtained thin plate is poor, large burrs occur on the sheared end face of the punched body, and the number of sheets that can be punched with the same die is small due to damage to the die.

Furthermore, the wear resistance against sliding contact of the medium as a magnetic head is also unsatisfactory.

U. Purpose of the Invention The present invention was made in view of the above circumstances, and
The main purpose of this is to eliminate the inconvenience of forming a slag layer at the tip of the injection nozzle during thinning using the high-speed quenching method, which deteriorates the surface properties of the thin plate and makes manufacturing impossible. The present invention aims to provide a Mn-added amorphous magnetic alloy thin plate for a magnetic head, which has improved punchability, wear resistance, and the like.

The inventors of the present invention have conducted extensive research on such objects, and have found that such objects can be achieved by adding Mn and minerals, leading to the present invention.

That is, the present invention is an amorphous magnetic alloy thin plate for a magnetic head characterized by having a composition represented by the following formula.

Formula TxMnyA-13zXa+ (In the above formula, T is Co, or CO and]Fe
, or CO represents a combination of CO and Pa with 111 or more of other transition metal elements, and X represents one or more lath-forming elements. x+y+z+a+=I Go
Among these, y is less than 6 at%, 2 is less than 2 at%, and ω is 18ν35at%. ) ■Specific structure of the invention The physical structure of the present invention will be explained in detail below.

The amorphous magnetic alloy thin plate of the present invention has a composition represented by the above formula and contains peaks in addition to 1Mn.

In this case, the effect prescribed by the present invention cannot be achieved with any other element other than i6.

In the above formula, TIK is Pe and C as necessary.
Other additive elements added together with O are IFe
and 1 and CO and other transition metal elements other than [Mn, fi
g (5czZn; Y~cd: La~HP;
Ac or higher), such as Ni, Hf, V,
Nb, TalMo, W, Rh*Pd,
One or more types of Os, Ir, Pt, etc. can be mentioned as examples of the gas.

On the other hand, X is B, 81 O! and B, t or B or day 1
A combination of B and another lath-forming element is preferred.

In this case, if necessary, h is an example of a disulfide element that is added in combination with B 81 and B,
Iff or higher such as p*a r ae+ sn can be mentioned.

On the other hand, in the above formula x + y + z + ω = 100
Under the condition of at%, the amount y of Mn added is 6 at% or less. This is because when @at% is exceeded, the effect of lowering the Curie point by one point without lowering saturation becomes ineffective.

In this case, if the Mn addition amount y is too low, the effect of the addition becomes insignificant, so y is preferably 0.5 at% or more. And y is 1 to 4 at%
In this case, even more favorable results will be obtained.

On the other hand, the addition amount 2 is 2 at% or less.
When 2 exceeds 2 at %, it becomes difficult to make the plate thinner.

Note that if 2 is less than O,Sat%, the formation of a slag layer at the tip of the injection nozzle will not be significantly eliminated, so if 2 is less than 0. S~
Preferably, it is 2 at%.

Further, K is the amount ω added of the lath forming element component X'.

It is 18-5 sat%.

When ω is less than l@at%, it becomes difficult to become amorphous,
Further, when V exceeds l 5 at %, the saturation magnetic flux density decreases and it becomes difficult to make the material amorphous.

In addition, the content X of T is 100-y-z-ω, and 5
? at% or more and less than 82 at%, but 87 to II
Preferably, it is 1 at%.

In this case, Te includes COI or Co and Fe.

The elemental composition ratio in T is selected so that the magnetostriction is close to zero.

That is, the Fe content is Ol or! L6at% or less. 1. Content! If it exceeds 16 at%,
Magnetostriction increases, and magnetic permeability decreases due to various stresses during the magnetic head manufacturing process.

In addition, Fe is included in T, and the Fe content is.

Is~&6at%, preferably 2~&5a, yields favorable results in terms of magnetostriction.

On the other hand, the Co content is preferably 40 at 5G or more. If the Co content is less than 40 at %, the saturation magnetic flux density Bs decreases.

In this case, more favorable results can be obtained when the Co content is 40 to 7 Oat%, more preferably 50 to 7 Oat%.

Furthermore, as mentioned above, within the above content range, T may consist of only OO or Fs and CO;
or 1I11 of re and CO and other elements mentioned above.
It may consist of the above.

When T contains one or more other elements in addition to Oo or IFe and coK, one or more of the other transition metal elements is 1
Usually, the total content can be up to 10 at%.

If the content exceeds this range, problems such as lower Bs and poor surface properties will occur.

One example of such an element is Ni.

The addition of N1 has the effect of replacing CO and reducing material costs, but as the amount of Ni increases, Bs decreases, so the N1 content is preferably less than or equal to Sat.

On the other hand, as one or more other elements, iron group ("-IFe
Although transition metal elements other than Mn and Mn may be used, it is preferable that the total amount of one or more of these other transition metal elements is 10 at% or more. At this time, the decrease in Bs is small, and excellent effects unique to each additive element are realized.

Such elements include, in particular, Ta, W, and M.

11!1 or more can be mentioned.

On the other hand, the lath-forming element component X has Bt or Sl and B as necessary f1 components.

In this case, when the B content is 18 to 35 at% and the 81 content is θ to 7 at%, Bs is high and the surface properties of the thin plate are improved, resulting in favorable results.

When the B content becomes 2 to 24 at% for 1 and 0.1 = 48 at% for 81, the Bs becomes even higher, the surface properties are further improved, and the addition of additional elements such as K, Mn, and AI is further improved. The addition effect also becomes SV, and more favorable results are obtained.

In addition, the s*/(si + B) ratio in X is 0.
It is preferably 4 or less. And especially 0.01
~0.3, preferably 0.05-0.2,
Even better! get better results.

In addition, in the vitrification element component X, it is mandatory! According to 81
It is preferable that one or more of other elements other than B are included. However, if the total amount exceeds 0.5 at%, it becomes amorphous and becomes K<, so the content is preferably 0.5 at% or less.

The thin plate having the composition described in detail above is an amorphous material having substantially no long-range regularity.

Further, the plate thickness is generally about 10 to 200 #■.

Such an amorphous magnetic alloy thin plate usually has a K of less than 5
Manufactured by

That is, an alloy having a corresponding composition is ultra-quenched from the liquid phase before the gas phase. In this case, the alloy is usually made into a melt, and the temperature from the liquid phase is lθ°C/sec or more.

An amorphous magnetic alloy thin plate is obtained by ultra-quenching and solidifying at a cooling rate of usually 10 to 10° C./sec. To super-quench the molten alloy, the molten alloy can be injected from a nozzle and quenched according to various known methods such as the twin-roll method, the two-piece four-wheel method, and the centrifugal quenching method, including the medium-single-roll method. good.

Note that the V enclosure during manufacturing does not matter. In other words, even if the plate is thinned by high-speed cooling in the atmosphere.

There is almost no slag layer formed at the tip of the injection nozzle.

■Specific operation of the invention Such amorphous magnetic alloy thin plates are laminated with an insulating adhesive layer interposed therebetween to form a half-core core of a desired shape, which is then butted together to form a magnetic head. It is used as a core for magnetic spatula r for audio use, etc. Alternatively, instead of laminating the thin plates, the thin plates themselves are used as the core body of the desired shape, and the core halves are butted together to form a core for a magnetic head.
*It is said to be the core for magnetic heads for video use.

Note that FIG. #11 shows an example when an audio magnetic head PK is applied. In the figure, 2°2' is a magnetic head core formed by laminating amorphous magnetic alloys, and 3 is a magnetic head core formed by laminating amorphous magnetic alloys.
- Zorotsuk, 4 is the shield case, 5 is the support part,
A magnetic head l is formed from these.

The magnetic spatula r may normally be manufactured as follows.

First, preferably, a thin plate obtained by an ultra-quenching method is subjected to a predetermined heat treatment. This heat treatment may be, for example, an annealing treatment in a non-magnetic field performed at a temperature below the crystallization temperature and above the Curie point for the purpose of eliminating I\IK internal strain.

It may be annealing treatment in a magnetic field for the purpose of removing strain and improving magnetic properties at a temperature below the crystallization temperature and one Curie point. Either a static magnetic field, a single rotation magnetic field, etc. may be used. These annealing heat treatments and their conditions may be appropriately selected from the composition of the amorphous magnetic alloy and the desired magnetic properties.

Next, 1, such an amorphous magnetic alloy thin plate is usually punched with a die into a predetermined shape, and generally, a plurality of sheets are laminated with an insulating adhesive so as to have a predetermined track width, and the core is semi-circumscribed. Make a work.

Note that the above heat treatment may be applied to this punching ilK.

Further, in some cases, if necessary, photo-etching may be used instead of punching, or when a laminated core is made, the core may be semi-deformed by grinding from the laminated thin plates. Furthermore, when K is used as a video magnetic head, there is usually no need to laminate thin plates.

After this, the core halves are usually wound, inserted into a core holder, and the abutting surfaces of the cores are polished. After that, a ear-forming material is placed in the gap by a predetermined gap, and the core halves are butted.

A magnetic head is produced by forming a core, storing it in a shield case, and molding it with resin.

The core for the magnetic spatula R produced in this way is extremely useful in any application, especially as a core for a contact type spatula P for use in audio, video, electronic computers, and curl readers.

(2) Specific Effects of the Invention According to the present invention, the formation of a slag layer at the tip of the book and the injection nozzle is extremely reduced when the book is thinned by the high-speed quenching method in the atmosphere.

For this reason, there are fewer defects on the surface of the thin plate and less possibility of production being impossible, and it is possible to produce in large quantities and there is less need to replace nozzles.

Alternatively, it is extremely advantageous in terms of manufacturing, since it does not require re-polishing of the thin plate.

Moreover, the thin plate can be easily heat treated and has a high saturation magnetic flux density.

Furthermore, it exhibits extremely good properties in terms of wear resistance, corrosion resistance, and punchability, making it extremely useful as a material for magnetic heads.

V. Practical Examples of the Invention Hereinafter, specific examples of the present invention will be shown and the present invention will be explained in further detail.

EXAMPLE An amorphous magnetic alloy thin plate having a composition shown in Table 1 below and having a thickness of 4 μm was obtained.

1.For thin plate formation, follow the high-speed quenching method using the single roll method.

The slit length of the injection nozzle is 5■, and the slit width is 0, 1-
And so. Further, the cooling roll was made of annealed copper, and the rotation speed was 3000 rpm.

For each melt, sot of the corresponding master alloy was melted and injected onto a cooling roll at a jetting speed of 517 ml in the atmosphere to obtain a thin plate.

The surface roughness based on defects on the surface of the thin plate during one high-speed quenching was measured using a surface roughness needle. Table 1 shows the results.
Shown below.

Furthermore, using the same nozzle, the production was repeated several times, and the number of times the nozzle was used in which the accuracy of the plate thickness due to defects on the surface of the obtained thin plate was within ±3 μm is shown in the table IK below.
show. Note that the number of times of use is 0 means that there were many defects on the surface during one production, and a plate thickness accuracy of ±3 μm or more could not be obtained.

Further, Table 1 IK shows the Curie point Tc, crystallization temperature Txk, and saturation magnetic flux density of the obtained thin plate.

On the other hand, various types of audio magnetic head r as shown in FIG. 1 were manufactured using each thin plate.

That is, each thin plate was heat treated at a temperature between Tc (!r Tx) and punched into a C-shape using a cemented carbide die.

Next, using a plurality of sheets of each punched body, epoxy adhesive was applied to one side of the punched body and laminated to a thickness of 6 ms at t7.0, and this was cured by heating to obtain a half-core core. Ta.

Each of the half-core cores was wound, placed in a core holder, and the abutting surfaces of the half-core cores were polished and bored to a mirror finish. Then, the core halves were butted together with a predetermined gap in accordance with a conventional method to form a magnetic head core 2, and an audio magnetic head 1 made of each thin plate was produced.

%, y for each audio head obtained by pressing
-The amount of wear was measured using a coated tape containing Fe, O, as magnetic powder.

In other words, this tape was heated at 25°C and relative humidity 60-65.
%, 1 at a running speed of 4.75 tyn/sec
After running for 000 hours, the wear depth of the running edge was measured using a surface roughness meter. The result is the value per xooaF (converted to
It is shown in Table 1 and below.

Na&, IIIK is defined as the punching property by the parity (μm ) are shown. Note that "knee" in the table indicates that punching was impossible.

From the results shown in Table 1, the thin plate of the present invention has
The formation of a slag layer at the tip of the nozzle is small, the surface properties of the thin plate are good, the number of times the nozzle can be used is high, and at the same time, the TcmTxO difference is large, heat treatment is easy, B8 is also high, and K has wear resistance as a magnetic head. and good punching properties,
Overall, it can be seen that it exhibits extremely good characteristics.

[Brief explanation of the drawing]

be·
Su1...Magnetic spatula P2...Core for magnetic head Applicant Tokyo Denki Kagaku Kogyo Co., Ltd. Representative Patent attorney Yo Ishii -

Claims (1)

[Claims] 1. An amorphous magnetic alloy thin plate for a magnetic head, characterized by having a composition represented by the formula F1. Formula TxMnyAezXω (In the above formula, T is COI or CO and Pa,
or represents a combination of CO or co and Fe with one or more other transition metal elements, and X is one of the vitrification elements.
-1-y+2+ω=100at% for 3, which represents more than species, where y is less than Sat%, and 2 is 2at%
Hereinafter, F1ω is 18 to 35 at%. 2. The amorphous magnetic alloy thin plate for a magnetic head according to claim 1, wherein T includes Pe and the Fe content is 16 at% or more F. and an amorphous magnetic alloy thin plate for a magnetic head according to claim 2, wherein the Fe content is 1.5 to 56 at. It is a combination of Sl and one or more other vitrifying elements, and the 81 / (Si + B) ratio in X is 0.
The amorphous magnetic alloy thin plate for a magnetic spatula r according to any one of claims 1 to 3, wherein Fio is 4 or less. &81/(S1+B) ratio is 0.01-0.3, the amorphous magnetic alloy thin plate for magnetic heat exchangers P according to claim 4. The amorphous magnetic alloy thin plate for a magnetic head according to any one of claims 1 to 5, wherein ay is 0.5 to 8 at%. ? , z is O, S~2 at%, an amorphous magnetic alloy thin plate for a magnetic head according to any one of claims 1 to #16.