JPS6041140B2 - Amorphous magnetic alloy thin plate for magnetic heads - Google Patents

Description

[Detailed description of the invention] 1 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 3 t% of a vitrifying element is known. ing.

A proposal has been made to add Mn to such an amorphous magnetic alloy (Special Seki No. 55-164051).
.

Such alloys with Mm added can reduce the Curie temperature Tc without affecting the saturation magnetic flux density, and the difference from the crystallization temperature Tx (Tx - Tc) increases, making heat treatment easier. , magnetic permeability is improved, and high saturation magnetic flux density can be obtained.

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

In other words, if rapid cooling is performed in the air without using a vacuum or an inert gas atmosphere as the atmosphere for injecting the sun from the injection nozzle to the cooling body, a slag layer will be formed at the tip of the injection nozzle. Continuous groove-like defects occur on the surface of the obtained thin plate, and the surface properties of the thin plate deteriorate. Moreover, this slag layer may stop the ejection of molten metal, making it impossible to manufacture the product. 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 punching properties of the resulting thin plates are poor, large burrs occur on the sheared end faces of the punched bodies, and the number of sheets that can be punched out with the same die is small due to damage to the die.

Furthermore, the wear resistance of the medium tank as a magnetic head is also unsatisfactory. 0 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. It is an object of the present invention 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 into such objects and have found that such objects can be achieved when Mn and N are added, 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 TxMnyMzX {In the above formula, T represents Co, or Co and Fe, or a combination of Co or Co and Fe with one or more other transition metal elements, and X represents one or more vitrification elements. represent.

x, y, and z = 10 t%, of which y is less than or equal to t%, z is less than or equal to pine t%, and ■ is 18 to 3 $t%. }m Specific Configuration of the Invention The specific configuration of the present invention will be described in detail below.

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

In this case, elements other than AI will not achieve the desired effects of the present invention. In the above formula, other additive elements added in combination with Fe and Co as necessary in T include transition metal elements other than Fe and Co and Mn (Sc~Zn:Y~Cd:La~ Hg: Ac or higher)
For example, Ni, Hf, V, Nb, Ta, Mo, W
, Rh, Pd, 0s, lr, Pt, etc. can be mentioned as specific examples. On the other hand, X is B, Si
and B, or a combination of B or Si and B and one or more other vitrifying elements.

In this case, examples of other vitrifying elements added as necessary in combination with B or Si and B include P,
One or more types of C, Q, Sn, etc. can be mentioned.

On the other hand, in the above formula, under the condition that x+y+z=10+t%, the Mn addition amount y is equal to or less than t%.

This is because when the skin t% is exceeded, the effect of lowering the Curie point without lowering the saturation magnetization becomes ineffective. In this case, if the Mn addition amount y is too low, the effect of the addition will not be significant, so y is 0. It is preferable that the amount is t% or more.

Further, when y is 1 to t%, even more favorable results are obtained. On the other hand, the amount of added ridges z is 2 t% or less.

When z exceeds t%, it becomes difficult to make the plate thinner. In addition, z
is 0. If it is less than $t%, the formation of a slag layer at the tip of the injection nozzle is not significantly eliminated, so z is preferably 0.5 to t%.

Further, the amount of the vitrifying element component X added is 18 to 3 t%.

When (2) is less than 1 t%, it becomes difficult to make it amorphous, and when it exceeds 3 t%, the saturation magnetic flux density decreases and it becomes difficult to make it amorphous.

In addition, the content x of T is 100-y-z-, and 5
7at% or more and less than 82t%, but 57 to 81at%
% is preferable. In this case, T includes Co or Co and Fe.

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

That is, the content of Fe is 0 or 5. skin t% or less.

Fe content is 5. If it exceeds T%, the magnetostriction will increase and the magnetic permeability will decrease due to various stresses in the magnetic head manufacturing process. Note that T contains Fe, and the Fe content is 1 .5 to 5.8t%, more preferably 2 to 5. &t%, more favorable results in terms of strain can be obtained.

On the other hand, the Co content is preferably 4 t% or more.

If the Co content is less than 4 t%, the saturation magnetic flux density will decrease. In this case, more preferable results are obtained when the Co content is 40 to 8 t%, more preferably 50 to 73 t%.

Furthermore, as mentioned above, within the above content range, T may consist of Co or only Fe and Co.
Alternatively, it may be Fe, Co, and one or more of the other elements listed above.

T is Co or 1 of other elements in addition to Fe and Co
When more than one species is included, one or more of the other transition metal elements can usually be contained up to a total of 1% by weight.

If the content exceeds this range, problems such as decreased Bs and poor surface properties will occur. One example of such an element is Ni. Addition of Ni has the effect of reducing material costs by replacing Co, but as the amount of Ni increases, Bs decreases, so the Ni content is preferably adjusted to t% of the sheath.
It is as follows. On the other hand, one or more of the other elements may be transition metal elements other than iron group (Fe, Co, Ni) and Mn; % or less.

At this time, the decrease in Bs is small, and excellent effects unique to each additive element are realized. Among these elements, in particular,
One or more of Ta, W, Mo, etc. can be mentioned.

On the other hand, the vitrification element component x has B or Si and B as essential components.

In this case, the B content is 18 to 3 t% and the Si content is 0.
When the content is 7 at%, Bs becomes high, the surface properties of the thin plate improve, and favorable results are obtained.

The B content is 15.2 to 2 t%, and the Si content is 0.1 to 4. When it comes to spotty t%, Bs becomes even higher,
The surface properties are further improved, and the effect of adding additional elements such as Mn and AI is also significant, resulting in more favorable results.

In addition, the Si/(Si+B) ratio in X is 0 or 0.
Preferably at the bottom of the mountain. And especially 0.01~0
．． 3, more preferably from 0.05 to 0.2, to obtain even more preferable results. Note that the vitrification element component x may contain one or more elements other than Si and B, if necessary.

However, the total is 0. If it exceeds $t%, it will become amorphous, so its content should be 0. It is preferable that it is less than t%. A thin plate having a composition as detailed above is an amorphous material having substantially no long-range regularity.

Further, the plate thickness is approximately 10 to 200 m. Such an amorphous magnetic alloy thin plate is usually manufactured as follows. That is, an alloy of a corresponding composition is ultra-quenched from the gas phase or liquid phase.

In this case, the alloy is usually made into a melt, and one pi is removed from the liquid phase. C
An amorphous magnetic alloy thin plate is obtained by ultra-quenching and solidifying at a cooling rate of at least 1 piq/sec, usually from 1 to 1 piq/sec. In order to ultra-rapidly cool a molten alloy, the molten alloy is injected from a nozzle, and the twin roll method, single roll method, deep D
The quenching method may be quenched using various known methods, particularly the single roll method. Note that the atmosphere during manufacturing does not matter.

That is, even if the sheet is thinned by rapid cooling in the atmosphere, there is almost no formation of a slag layer at the tip of the injection nozzle. W. Specific operation of the invention Such an amorphous magnetic alloy board is layered together, preferably through an insulating adhesive layer, to form a core half of a desired shape, and the core halves are butted together to form a magnetic core. It is used as a core for a head, especially for a magnetic head such as an audio one.

Alternatively, the thin plates are not laminated, but the thin plates themselves are used as core halves of a desired shape, and the core halves are butted together to form a core for a magnetic head, particularly for a video magnetic head. Incidentally, FIG. 1 shows an example in which the present invention is applied to an audio magnetic head.

In the figure, 2 and 2' are a magnetic head core formed by laminating amorphous magnetic alloys, 3 is a dummy block, 4 is a shield case, and 5 is a support part, from which a magnetic head l is formed. ing. A magnetic head can usually be manufactured as follows.

First, preferably, a predetermined heat treatment is performed on a thin plate obtained by an ultra-quenching method.

This heat treatment may be, for example, a hammer treatment in a non-magnetic field at a temperature below the crystallization temperature and above the Curie point, particularly for the purpose of removing internal strain, or a heat treatment at a temperature below the crystallization temperature and above the Curie point. It may also be a hammering process performed at high temperature in a magnetic field for the purpose of removing strain and improving magnetic properties. For this latter annealing treatment in a magnetic field, either a static magnetic field, a rotating magnetic field, or the like may be used. These competitive annealing heat treatments and their conditions may be appropriately selected from the composition of the amorphous magnetic alloy and the desired magnetic properties. Next, such an amorphous magnetic alloy thin plate is usually punched out using a die.
A plurality of core halves are generally formed into a predetermined shape and laminated with an insulating adhesive so as to form a predetermined track.

Note that the above heat treatment may be performed after this punching.
In some cases, if necessary, photoetching may be used instead of punching, or when a laminated core is produced, a core half may be obtained by grinding the laminated thin plates. Furthermore, especially when 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 the core holder, and the gap butt surfaces polished.
A gap-forming material is provided in the gap by a predetermined gap, the core halves are butted together to form a core, and the core is housed in a shield case and resin molded to produce a magnetic head. The magnetic head core produced in this manner is extremely useful in any application, particularly as a core for contact type heads such as audio, video, electronic computers, and card readers.

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

For this reason, there are fewer defects on the surface of the thin plate or production failures, large quantities can be manufactured at once, fewer nozzles need to be replaced, and sometimes the thin plate does not need to be re-polished. This is extremely advantageous in terms of manufacturing.

Moreover, the thin plate is easy to heat treat and has a high saturation magnetic flux density.

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

V Specific 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 A 45-m thick amorphous magnetic alloy thin plate having the composition shown in Table 1 below was obtained.

The slit length of the injection nozzle was 5 columns, and the slit width was 0.1 mm in accordance with the thinning and high-speed quenching method using a single roll method.

The cooling roll was made of mild steel and had a rotational speed of 300 pm. For each melt, 50 mm of the corresponding master alloy was melted, and this was injected onto a cooling roll at a jetting speed of 5 mm/min 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 meter.

The results are shown in Table 1. Furthermore, the same nozzle was used to perform the manufacturing several times, and the number of times the nozzle was used is shown in Table 1 below, where the accuracy of the thickness of the obtained thin plate due to defects on the surface was within ±3 French meters. .

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 m or more could not be obtained. Table 1 also shows the Curie point Tc, crystallization temperature Tx, and saturation magnetic flux density of the obtained thin plate.

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

That is, each thin plate was heat treated at a temperature between Tc and Tx, and then punched into a substantially C-shape using a cemented carbide die. Next, using multiple sheets of each punch, apply epoxy adhesive to one side of the punch and apply a layer to a thickness of 0.6 mm, and heat and harden this to form a core half. I got it.

Thereafter, each of the core halves was wound and housed in a core holder, and the gap abutting surfaces of the core halves were polished and polished 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. For each audio head obtained in this way, y-Fe203
The amount of wear was measured using a coated tape containing magnetic powder.

That is, this tape was heated at 25 pm, with a relative humidity of 60 to 65 pm.
*%, it was run for 100 hours at a running speed of 4.75 skins/sec, and the wear depth after running was measured using a surface gauge.

The results were converted into values per 10 feeding hours and are shown in Table 1 below. Table 1 shows the punching properties when 100,000 sheets were punched into the shape described above using the mold.
The average burr (1 m) on the sheared end face of the female punched body of No. 1 up to the 100,000th sheet is shown.

In addition, in the table: - indicates that punching was impossible. Table 1 From the results shown in Table 1, the thin plate of the present invention has less slag layer formation at the nozzle tip, good surface properties of the thin plate, high number of nozzle uses, and at the same time a large difference in Tc and Tx.
It is easy to heat treat, has a high density, and has good wear resistance and punchability as a magnetic head.
It can be seen that it exhibits extremely good characteristics.

[Brief explanation of the drawing]

FIG. 1 is a perspective view showing an example in which the amorphous magnetic alloy thin plate of the present invention is applied to a magnetic head. 1... Magnetic head, 2... Core for magnetic head.

Claims (1)

[Claims] 1. An amorphous magnetic alloy thin plate for a magnetic head, characterized by having a composition represented by the following formula. Formula TxMnyAlzXω {In the above formula, T represents Co, or Co and Fe, or a combination of Co or Co and Fe with one or more other transition metal elements, and X represents one or more vitrification elements. . x+y+z+ω=100at%, of which y is 6at% or less, z is 2at% or less, and ω is 18 to 35at%.
%. }2 T contains Fe and the Fe content is 5.6
% or less, an amorphous magnetic alloy thin plate for a magnetic head according to claim 1. 3 Fe content is 1.5-5
．． 6 at % of the amorphous magnetic alloy thin plate for a magnetic head according to claim 2. 4 X is B, or B and Si, or a combination of B or B and Si and one or more other vitrification elements, and the Si/(Si+B) ratio in X is 0 or 0
．． 4 or less, an amorphous magnetic alloy thin plate for a magnetic head according to any one of claims 1 to 3. 5. The amorphous magnetic alloy thin plate for a magnetic head according to claim 4, wherein the Si/(Si+B) ratio is from 0.01 to 0.3. 6. The amorphous magnetic alloy thin plate for a magnetic head according to claim 1, wherein y is 0.5 to 6 at%. 7. The amorphous magnetic alloy thin plate for a magnetic head according to claim 1, wherein z is 0.5 to 2 at%.