JPS58193337A - Amorphous magnetic alloy thin plate for magnetic head - Google Patents

Abstract

PURPOSE:To improve the surface properties of the titled thin plate by reducing the formation of a slag layer in the leading end of a jet nozzle in preparing the titled thin plate according to a high speed quenching method, by forming the titled thin plate from a composition containing Co, Cr, Mn, Ti, B or B and Si. CONSTITUTION:This amorphous magnetic alloy thin plate for a magnetic head has a composition shown by the formula. In the formula, T shows Co or a combination of Co and Fe, Co or Co and Fe and one kind or more other transition metal elements while X shows B or a combination of B and Si, B or B and Si and one kind or more other vitrifiable elements. X+Y+Z+W+V is 100at%, Y is 8at% or less, Z is 6at% or less, W is 0.8at% or less and V is 16-35at%. In addition, when Fe is contained in T, Fe is 5.6at% or less.

Description

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

Prior art and its problems One of the magnetic head forming materials mainly contains CO as an iron group transition metal element, and further contains /S~J, 5at%
Amorphous magnetic alloy thin sheets containing vitrifying elements of about 100% are known.

When Or is added to such an amorphous magnetic alloy, corrosion resistance is improved and extremely good properties are exhibited.

On the other hand, when Mq is added to the above-mentioned amorphous magnetic alloy, the Curie temperature Tc can be reduced without affecting the saturation magnetic flux density, and the difference from the crystallization temperature Tx (Tx- It is also known that Tc) increases by 11, heat treatment becomes easier, magnetic permeability improves, and high saturation magnetic flux density can be obtained.

Therefore, if Mn and Cr are added in combination to the above-mentioned amorphous magnetic alloy, it is expected that it will exhibit extremely good characteristics.

However, when trying to obtain a thin plate from WIs of a master alloy containing 1Mn and Cr by adding tic Mn and Cr in combination, the following problems occur.

In other words, K
When rapid cooling is performed in the atmosphere, a slag layer is formed at the tip of the injection nozzle.

As a result, continuous groove-like defects occur on the surface of the obtained thin plate, resulting in poor surface finish and thickness accuracy of the thin plate. Also,
This slag layer may stop the ejection of molten metal, making production impossible.

For this reason, it is not possible to manufacture a large amount of thin plates all at once,
There is also the inconvenience of having to frequently replace the nozzle.

■ Purpose of the invention The present invention was made in view of the above-mentioned circumstances, and its main purpose is to
A slag layer forms at the tip of the injection nozzle, deteriorating the surface quality of the thin plate.

Mn −, which eliminates the inconvenience that made manufacturing impossible
C! It is an object of the present invention to provide an amorphous magnetic thin plate for use in an r-complex doped magnetic head.

The inventors of the present invention conducted intensive research on such objects and found that such objects can be achieved when KTi is added in addition to Mn and Or, 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 Tz Cry Mnz 'riwXy(・
In the above formula, T, Co, Co and Fe, or CO or CO and Fe and other transition metal elements 7
Represents a combination with more than one species, X is B, B and Si
, or a combination of B or B and Sl with seven or more other lath-forming elements. x+y+z+w+v
= 100at,%, of which y is g at%t
% or less, Fibat at 1 or less.

W is θgat% or less, and V expansion is 16 to j5at%.

Furthermore, if Fe is included in T, ye i is left b
at%t% or less. ) In addition, JP-A-56-GLLT,! / Issue Publication Kti.

[B to ■B group elements (IIIa to yHb group elements)
An amorphous magnetic alloy thin plate containing seven or more types of Mn and Mn is described.

However, only T1 is contained together with 1Mn and Or to achieve the above purpose; other ll[B~
Group VIB elements 1 such as Nb, Ta, etc.

The above-mentioned problems caused by the formation of a slag layer at the tip of the injection nozzle have been eliminated.

■Specific structure of the invention Hereinafter, a specific configuration of the present invention will be explained in detail.

The amorphous magnetic alloy thin plate of the present invention has a composition represented by the above formula, and contains T1 in addition to Or and Mn. In this case, the desired effect of the present invention cannot be achieved with elements other than No. 1.

In the above formula, it is necessary in T! ! Depending on i', other additive elements added in combination with Fe and co are F
'e and Co and other transition metal elements other than Mn, Or and T1 (5e-1nt Y~Cd; L
a = Hff; Ac or higher), for example Ni.

Zr −Hf r V t Nb, Ta + Mo
+ W, Ru, Rh+Pd, Os, Ir,
Specific examples include seven or more types such as Pt.

On the other hand, X is B, Si and B, or B or Si
A combination of B and 19 or more of other vitrifying elements is preferred.

In this case, seven examples of other vitrifying elements added as necessary in combination with B or Sl and B include:
Seven or more types can be mentioned, such as P, Cj, Go, and sn.

On the other hand, in the above formula, X0Y+Z+w+v=1
Under the condition of 00at%, g at
This is because if it exceeds %t%, the corrosion resistance will decrease.In this case, the amount of Cr added should be 0.5 to 5 at%, more preferably 7 to 5 at%. This will give you even more favorable results.

On the other hand, in the above formula, the Mn addition amount 2 is equal to or less than 1, Bt. This exceeds 4at%.

This is because the effect of lowering the Curie point without lowering the saturation magnetic flux density BS no longer occurs.

In this case, 1Mn addition amount 2 is too low.

Since the effect of its addition is no longer significant, 2 is Q, 3
It is preferable that at%t% or less.

When 2 becomes /~II at%, even more favorable results are obtained.

On the other hand, the amount of Ti added is less than θzat%t%.

W is 0. If g at % is exceeded, the formation of a slag layer at the tip of the injection nozzle will increase. Also.

The saturation magnetic flux density will decrease.

Note that when W is θ/at%t%, the effect of eliminating the formation of a slag layer at the tip of the injection nozzle is not significant, so W is θ/at%t%.
~Q1ge,t,%, preferably 0.7~0Aat
% is preferable.

Furthermore, the addition amount V of the 2S element component X is /6 to 3Sa
It's a pigeon.

When ■ is less than /Aaz%, it becomes difficult to make it amorphous,
Further, when V exceeds 33 at%, sufficient saturation magnetic flux density cannot be obtained.

In this case, more preferable results are obtained when V is /g to 30 at%.

In addition, the content X of T is / 0O-y-z -w-■
Adashi! ; 0.2at% or more and less than -f+az%, but 5θ co~g2. qat,% is preferred.

In this case, T includes Co or Co and PCI.

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

That is, the Fe content is 0 or less than Aa, t%. When the Fe content exceeds S:bat%, magnetostriction increases. In the magnetic head manufacturing process 8, magnetic permeability decreases due to various stresses.

In addition, Fe is included in T, and the Fe content is lil~! L
l*at%, more preferably a~53at%, provides more favorable results in terms of magnetostriction.

On the other hand, the Co content is preferably 4 COat% or more. If the Co content is less than I/Oas%, the saturation magnetic flux density B8 will decrease.

In this case, more preferable results are obtained when the Co content is O-GOES%, preferably 30 to 70 at%.

Furthermore, as mentioned above, even if T consists only of CO or IFe and CO within the above content range,
It may consist of Co or 1.Homare, CO, and seven or more of the other elements listed above.

T is COl or ye and OOK plus 7 of other elements
If more than one species is included, seven or more of the other transition metal elements can be included, typically up to a total of up to 1/Oat%.

If the content is higher than this, B8 will decrease and problems such as poor surface quality will occur.

One example of such an element is N. Adding N1 has the effect of replacing Co and reducing material costs, but as the amount of Ni increases, BS decreases, so N1
The content is preferably less than or equal to GAT.

On the other hand, as seven or more other elements, iron group (we, C
o, ui), (!r, m, and rt may be other transition metal elements, but it is preferable that the total amount of 7 or more of these other transition metal elements is less than or equal to /Oat%. At this time , the decrease in Bs is small, and excellent effects unique to each additive element are realized.

Such elements include 1% 4C, Ru, and Ta.

Seven or more types including Zr, W, and Mo can be mentioned.

Among these other elements, the addition of Ru is particularly advantageous.

By adding 1゛0 composite, the amount of wear on the magnetic 11 head due to media sliding is significantly reduced. Also, as described below,
K forms a magnetic head from a thin plate.

It is advantageous to punch out thin sheets into a predetermined shape and stack them as required, but the addition of Ru makes the edge of the thin sheet punched during punching extremely small.

Note that the Ru content is θS-zat%, preferably o
, 5-5 at%.

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

In this case, the B content is /6~3Sa傻, and the B1 content is θ
When the content is 6 at%, the Ba content is high, the surface properties of the thin plate are improved, and favorable results are obtained.

Then, the B content is 1/Lat%, and the 81 content is 0. /~IA g at%, the B8 force ζ becomes even higher, the surface properties further improve, and Or.

The effect of adding additional elements such as Mn and 'ri is also significant, and very favorable results are obtained.

In addition, the si/(st+B) ratio in X is preferably less than or equal to θ. And especially, 0.0/~
Even more preferable results are obtained when θ3, preferably θos to θko.

Note that the vitrification element component X may contain seven or more elements other than Sl and B, if necessary. However, if the total amount exceeds o, sa%%, it becomes amorphous and becomes K<, so it is preferable that the content is B5 at% or more.

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 /θ to 200μ.

Such an amorphous magnetic alloy thin plate is usually manufactured as follows.

That is, an alloy of the corresponding composition is ultra-quenched from the gas cap or liquid phase. In this case, the alloy is usually in the form of a melt, and the flow rate from the liquid phase to /0"C/sec or more, usually 104 to I
An amorphous magnetic alloy thin plate is obtained by ultra-quenching and solidifying at a cooling rate of 06° C./sec. To ultra-rapidly cool a molten alloy, the molten alloy is injected from a nozzle using the twin roll method.

The quenching may be carried out by various known methods such as the single roll method and the centrifugal quenching method, particularly the single roll method.

Note that the atmosphere during manufacturing does not matter. That is, even if the plate is made thinner by rapid cooling in the atmosphere, there is almost no slag layer shape Fs at the tip of the injection nozzle.

■Specific operation of the invention Such amorphous magnetic alloy thin plates are laminated, preferably through an insulating adhesive layer, to form a half-core core of a desired shape, and these are butted together to form a core for a magnetic head. In particular, it is used as a core for magnetic heads such as those for audio. or,
The thin plates are not laminated, but the thin plates themselves are used as a core body having 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°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.
A magnetic head 1 is formed from a block, 4 a shield case, and 5 a support portion.

The magnetic head may be manufactured in the following manner.

First, preferably, the thin film obtained by the ultra-quenching method is subjected to a predetermined heat treatment.

This heat treatment is carried out, for example, at a temperature below the crystallization temperature and above the Curie point in a non-magnetic field.

In particular, it may be used as a blunt process for the purpose of removing internal distortion.

Alternatively, annealing treatment may be performed in a magnetic field at a crystallization temperature and a temperature below one Curie point for the purpose of removing strain and improving magnetic properties. and.

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 annealing treatments and their conditions may be appropriately selected from the composition of the amorphous magnetic alloy and the desired magnetic properties.

Next, amorphous 5 like this! A magnetic alloy thin plate is punched into a predetermined shape using a die, and generally a number of the sheets are laminated with an insulating adhesive so as to have a predetermined track width to produce a half core.

Note that the above heat treatment may be applied to this punched material.
Father, as the case may be.

When forming a core using punching and photo-etching, or a laminated core, a thin core can also be obtained by grinding the laminated thin plates.

Furthermore, when used as a video magnetic head or the like, there is usually no need to laminate thin plates.

After this, the core body is usually wound, and this is inserted into the core holder. A magnetic head is fabricated by combining them to form a core, storing them in a cold case, and molding them with resin.

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.

V. Air Effect of the Invention According to the present invention, the formation of a slag layer at the tip of the 1wN 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 and the possibility of unmanufacturability, and it is possible to produce large quantities of thin sheets, increase the number of times the nozzle is used, and reduce the need for nozzle replacement. This is extremely advantageous in terms of manufacturing, as there is no need to re-grind the thin plate.

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

In addition, it has extremely high corrosion resistance.

When -Ru is added, the material exhibits even better properties such as wear resistance and punchability, making it extremely useful as a material for magnetic heads.

(2) Specific Examples of the Invention Hereinafter, specific examples of the present invention will be shown to explain the present invention in further detail.

EXAMPLE An amorphous magnetic alloy thin plate having a composition shown in the following table/table 2 and having a thickness of 100 mm was obtained.

The sheet was thinned according to the high-speed quenching method using a single roll method, and the slit length of the injection nozzle was set to 0.7 mm, and the slit width was set to 0.7 mm. Nine, the cooling roll uses a roll made of mild steel. The number of rotations is 3
000 rpm.

For each seventh round, the corresponding master alloy of SOf was melted and injected onto a cooling roll in the atmosphere at a jetting speed of j l /ff1 in to obtain a thin plate.

The surface properties after such high-speed quenching were measured using a surface roughness meter.

Table the results/and II! Shown here.

Furthermore, the same nozzle was used to perform the manufacturing process several times, and the number of times the nozzle was used for which the accuracy of the thickness of the obtained thin plate was within ±3 μm is shown in Table 1 and Table 2 below.
In addition, the number of uses θ means ±3 when manufacturing 7 times.
This means that a plate thickness accuracy of μm or higher could not be obtained.

Further, Table/Table 2 shows the cue and ri point Tc (°C) - crystallization temperature Tx (°C') and saturation magnetic flux density BS (KG) of the obtained thin plate.

On the other hand, using each thin plate ll! / Various audio magnetic heads as shown in the figure were manufactured.

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

Next, using a plurality of each of the punched bodies, epoxy adhesive was applied to one side of each of the punched bodies, stacked to a thickness of 06 mm, and cured by heating.

I got a half-day break from my core.

Each of the cores was then wound, housed in a core holder, and the gap abutting surfaces of the half cores were ground and polished to a mirror finish. Then, take a half-day core break according to the usual method.

A magnetic head 2 was made by holding the ear 41 and a magnetic head 1 made of each thin plate.9 For each audio head obtained in this way, r
-Fe, 0. The amount of wear was measured using a coated tape containing magnetic powder.

In other words, this tape is 2! ℃, relative humidity 60~
7 at a travel speed of 75 ax/sec at 63%
After running for 000 hours, the wear depth after running was measured using a surface roughness meter. Convert the result to the value of 700 hours,
Separately, each magnetic head was left at 70°C and a relative humidity of qO to qS% for ibg hours, and then
A; Corrosion resistance was evaluated by measuring the f-force (aB) at Hz//1KHz. The results are not shown in the table below.

In addition, 12 tables/and! ! The same mold is used here,
Each thin plate is punched at a rate of 1/10,000 sheets, and a total of io punches are selected from the 700,000th sheet for each thin sheet, and the height of the punch at the punched end face is shown. In this case, Paris (μ冨)ha.

This is the average value measured by an electric micrometer or meter.

From the results shown in Tables 1 and 2, the thin plate of the present invention is:
The formation of a slag layer at the nozzle tip is small, the surface quality of the thin plate is good, the number of nozzle uses is high, and the simultaneous 1/CTc, Tx
The difference is large, heat treatment is easy, and Ba is also high.
Furthermore, it can be seen that it has good corrosion resistance as a +, + magnetic head, and exhibits extremely good characteristics overall.

It is also seen that when Ru is further added, the wear resistance and punchability are improved.

[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 Applicant
Tokyo Denki Kagaku Kogyo Co., Ltd.

Claims (1)

[Claims] L An amorphous magnetic alloy thin plate for magnetic spacing, characterized by having a composition represented by the following formula. Formula TXCryMn2Ti,
is Go, Go and Fe, 9 Id Co or c
X represents a combination of o and Fe with seven or more other transaxial elements, and X represents a combination of B, B and Sl, or B or B and sl and seven or more other lath elements . x 1y + z 10vr-tv= / 00 at%
Of these, y is less than %, 2 is 6at%
Hereinafter, W is 0g at% or less, ■ is 76 to 35 at-
It is. Furthermore, when Fe is included in T, the amount of Fe is. It is 5.6 at% or less. ) λ Fe content is /j'=! The amorphous magnetic alloy thin plate for a magnetic head according to claim 1, wherein the amorphous magnetic alloy thin plate has a diameter of 6at. 1 x is B, B and sl, or a combination of B or B and 81 with other vitrifying elements of 181 or more, and the si/(Bi + B) ratio in I is
Claim 1 that is less than or equal to F! The amorphous magnetic alloy thin plate for a magnetic head according to item 2. Table Claim # where the Bi/(Bi + B) ratio is θθ/~θ3! The amorphous magnetic alloy thin plate for a magnetic head according to item 3. &7 is 0. ! ;-Eat, % Claim 1
An amorphous magnetic alloy thin plate for a magnetic head according to any one of items 1 to 9. The amorphous magnetic alloy thin plate for a magnetic head according to any one of claims 1 to 5, wherein aZ is 0.5 to &at%. 7. w is θ/~0. The amorphous magnetic alloy thin plate for a magnetic spatula r according to any one of claims 1 to 6, which has a % get. B, T are −Co + Fe and Ru, or Cor
The amorphous magnetic alloy thin plate for a magnetic head according to any one of claims 1 to 17, which is a combination of Fe and Ru and seven or more other transition metal elements. 9. Ru content is θ! ;-gat% 4?
III! A magnetic head according to claim g.