JPS6020882B2 - Manufacturing method of magnetic head using high magnetic permeability amorphous alloy - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method of manufacturing a magnetic head using a high magnetic permeability amorphous alloy.

Conventionally, Fe-
Si alloy, Fe-Ni alloy, Fe-needle alloy "Fe-S
J-AI alloys and the like are used in many fields depending on their properties, but each of these alloys still has drawbacks in terms of properties and use. Fe-Si alloys are used in the largest amount among high permeability alloys as iron cores for transformers, motors, etc., but the manufacturing process is complicated and the amount of fuel and electricity required to manufacture them is large. , the end result is an expensive alloy in terms of raw material cost.

Fe-Ni alloys are used as iron cores for weak electrical equipment, and permalloy, which contains 78% Ni, has extremely high magnetic permeability and is used for transformers and magnetic heads, as well as for deltamax (containing 50% Ni and iron). (trade name of a magnetic alloy) has a sharp hysteresis curve and is used as the iron core of magnetic amplifiers, etc. However, the manufacturing method is complicated and expensive, just like Fe-Si alloy. Since it uses a large amount of Ni, it is a very expensive material, which is a practical problem, and especially as an alloy for a magnetic head, the hardness is low and head wear is high, which is a problem in use.
Alperm, an e-AI alloy, is a high permeability alloy containing about 16% AI, but it is extremely difficult to plastically work, and Sendust (Fe-Sj-AI alloy)
Since 10% Si-5% (Yama) has the disadvantage that it cannot be plastically worked at all, it is used after special processing only in special applications where its characteristics of high hardness and high specific resistance are utilized. There is.

That is, the former is manufactured by warm processing as a magnetic head for sickle drawings, and the latter is manufactured by electric discharge machining or grinding as a magnetic head for card readers, but the above-mentioned drawbacks limit their use. An object of the present invention is to provide a magnetic head using a novel high magnetic permeability alloy that does not have the above-mentioned drawbacks of conventionally used high magnetic permeability metal materials for magnetic heads. This is the first time that an alloy has been used as a high magnetic permeability metal material, and the high hardness, which is an attribute of the alumofous alloy,
The above object can be achieved by providing a method for manufacturing a magnetic head using a high magnetic permeability amorphous alloy that advantageously utilizes Takaoka resistance.

The present invention contains 7 to 35 at% of any one or more of phosphorus, carbon, and boron, 25% or less of silicon (excluding 0%), and the balance is only cobalt or the balance is cobalt and iron ( However, the cobalt content is higher than the iron content), and this molten metal is cooled at an ultra-high speed to achieve high magnetic permeability, low coercive force, high hardness, commercial resistance, and excellent high frequency characteristics. Create an amorphous alloy with
The present invention relates to a method of manufacturing a magnetic head using a high magnetic permeability amorphous alloy, which is characterized by molding this amorphous alloy. Still another object of the present invention is to ``contain 7 to 3 of any one or more of phosphorus, carbon, and boron.
5 at%, silicon 25% or less (but not including 0%), and the remainder cobalt alone or cobalt and iron (however, the cobalt content is greater than the iron content or soot), and the subcomponents are Nickel 50 in atomic %
% or less of 15% or less of at least one of chrome and droplets,
Molybdenum, zirconium, titanium, aluminum, vanadium, niobium, tar, tungsten "Any one or more selected from copper, germanium, beryllium, and bismuth in an amount of 10% or less, and (co) praseodymium, Any one or more selected from neodymium, promethium, samarium, europium, gadolinium, terbium, dysprosium, and holmium in an amount of 5% or less of the above (a) and (b)
, (c) and (d), the alloy containing one or more components selected from the groups of 50% or less in total is melted, and this port hot water is cooled at an ultra-high speed to form a highly transparent material. A method for manufacturing a magnetic head using a high magnetic permeability amorphous alloy, characterized in that an amorphous alloy with high magnetic permeability, low coercive force, high hardness, high specific resistance, and excellent high frequency characteristics is made and this amorphous alloy is molded. is to provide.

Next, the present invention will be explained in detail.

The high magnetic permeability amorphous alloy that can be suitably used in the method of manufacturing the silicon head of the present invention includes 7 to 35 atomic percent of one or more of P, C, and B.
and 25% or less of Si, and the remainder is ferromagnetic at room temperature.
A high magnetic permeability amorphous alloy consisting of a Co-Fe alloy in which o alone or a part of Co is replaced, or the above alloy contains (a) 50% or less Ni, (o) C as a subcomponent in atomic %
and 15% or less of at least one of Mn, (c) Mo
, Zr, Ti, N, V, Nb, Ta, W, Cu, C also,
10% or less of any one or two or more selected from stage and Bi, and (d) Pr, Nb, Pm,
Any one or two or more selected from Sm, Gd, Tb, Dy and Ho in an amount of 5% or less (a),
A metal rotating body that melts an alloy containing 50% or less of any one or more components selected from (b), (c), and (d) in total and rotates the molten alloy at high speed. By depositing it on the surface through the hole of a refractory nozzle, it is rapidly cooled at a rate of 1 to 107°C/sec to solidify into a thin strip, and thus ultra-fast cooling results in high magnetic permeability, low coercive force, and high This is an amorphous alloy with hardness, high specific resistance, and excellent high frequency characteristics, and the magnetic head is made of a high magnetic permeability amorphous alloy made by molding this alloy into a magnetic head.

Each of the above alloys not only has extremely excellent magnetic permeability, but also has high hardness and high resistivity, which are characteristics of amorphous alloys.

Next, an example of a method for manufacturing an amorphous alloy using the magnetic head of the present invention will be explained with reference to the drawings. The figure is a schematic diagram showing an example of an apparatus for manufacturing an alumofous alloy used in the magnetic head of the present invention.

In the figure, reference numeral 1 denotes a quartz tube having a nozzle 2 at its lower end that ejects water in a horizontal direction, into which raw metal 3 is charged and melted. 4 is a heating furnace for heating the raw material metal 3, and 5 is a heating furnace for heating the raw metal 3;
Enemy. p. m. This is a rotating drum that is rotated by a drum.In order to minimize the centrifugal force load caused by the rotation of the drum, it is made of a lightweight metal with good heat conductivity, such as an aluminum alloy, and the inner surface is made of a metal with good heat conductivity. , for example, is lined with a copper plate 7.

8 is a air piston for supporting the quartz tube 1 and moving it up and down.

The raw metal is first charged through the inlet la of the quartz tube 1 by fluid conveyance, heated and melted in the heating furnace 4, and then heated by the air piston 8 so that the nozzle 2 faces the inner surface of the rotating drum 5. 1 is lowered to the position shown in the figure,
Gas pressure is then applied to the molten metal 3 almost as soon as it begins to rise, causing the metal to be jetted toward the inner surface of the rotating drum. In order to prevent oxidation of the metal 3, an inert gas such as argon gas 9 is constantly fed into the quartz tube to create an inert atmosphere. The metal jetted onto the inner surface of the rotating drum is brought into strong contact with the inner surface of the rotating drum due to the centrifugal force caused by the high speed rotation, and is cooled at an ultra-high speed to become an amorphous metal. In the research of the present invention, it was newly discovered that Alumofous alloy has particularly excellent mechanical properties as well as excellent magnetic properties, and the results of investigating the magnetic properties by changing various component compositions are shown in Table 1. show. In addition, conventionally known Fe-Si alloy, Fe-
The magnetic properties of AI alloy, Fe-Si-mountain alloy, etc. were measured and compared. As can be seen from the table, the amorphous alloys (M.1 to 12) used in the magnetic head of the present invention have magnetic properties superior to Fe-Si alloys and comparable to Fe-Zn alloys. There are things that have characteristics.

Moreover, the specific resistance of these amorphous alloys is 180
~20040 Ichiga, , Fe-AI alloy and Fe-
It is higher than the 100 and 140 peaks of the Si-mount alloy, and its hardness (Hv) is 800 to 960, which is significantly harder than the Fe-N alloy's 29 and the Fe-Si-AI alloy's 500. Furthermore, despite its high hardness, the amorphous alloy of the present invention is not brittle like e-AI alloys and Fe-Si-N alloys, so it is extremely easy to mold, which is a major feature when used in magnetic heads. . Furthermore, the wear resistance, which is particularly required for magnetic heads, is very high and is almost on the same level as Sendust.

In the present invention, when Fe and/or Co in the Co-based and Co-Fe-based amorphous alloys used in the magnetic head of the present invention are partially replaced with the various metal elements, mechanical properties and corrosion resistance are improved, and
It was newly discovered that Si has excellent magnetic properties, and that Si significantly improves the amorphization and magnetic properties of Co-based amorphous alloys.

Table 2 shows the composition and magnetic properties of these materials of the present invention. By partially substituting other metal elements for Fe and/or Co in the alloys of the present invention exemplified in Table 1, it is possible to obtain alumofous alloys having similarly high magnetic permeability as shown in Table 2. It turns out that it is possible.

In particular, Cr, Ni, and Si are FeSi-Co-Si-B, C
It is a component element that is effective in improving the magnetic permeability of o-B series thermophorous alloys, and addition of the various component elements described above increases the specific resistance and greatly improves the high frequency characteristics. The reason why the content of each component in the above-mentioned amorphous alloy used in the magnetic head of the present invention is set within a predetermined range is as follows.

P, C, and B are elements that help form an amorphous structure, but if the content of at least one of these is less than 7 at% or exceeds 35 at%, the amorphous alloy will not be formed. It is advantageous to keep the content within the range of 7 to 35 atomic %, since manufacturing becomes difficult and the alloy becomes bulky.The larger the content of P, C, and B, the higher the magnetic permeability, but Since the magnetic flux density is reduced, it is best to set the total amount of these elements to about 20 to 25 at %. Fe and Co are elements that exhibit ferromagnetism at room temperature and can completely replace each other, but in the case of the Fe-P-C system, Fe
As Co is substituted with Co, the saturation magnetic flux density decreases linearly, and the coercive force gradually increases, reaching a maximum at about 40 at.% (0.
15), while in the case of Co-B-Si system,
As Co is replaced with Fe, the saturation magnetic flux density increases, the coercive force decreases significantly, and the strain becomes zero at about 5 atomic %.
The coercive force is minimal (0.0080e).

Therefore, it is advantageous to determine the amounts of Fe and Co depending on the required properties. Ni is an element that improves magnetic permeability, but if it exceeds 50 atomic %, the magnetic permeability does not improve much and only decreases the saturation magnetic flux density, so it is advantageous to keep it at 50 atomic % or less.

Si is an effective element that increases magnetic permeability and decreases coercive force, and has a remarkable effect particularly in the case of Co-based amorphous alloys. However, even if it exceeds 25 atomic %, the magnetic permeability does not improve much and only decreases the saturation magnetic flux density.
It is advantageous to substitute up to 25 atom %. The reason why Cr and Mn are set at 15 atomic % or less is that Cr is an effective element that increases magnetic permeability, reduces coercive force, and further improves hardness and corrosion resistance, and Mn harms magnetic permeability and coercive force. This is because, although these elements harden the amorphous alloy without oxidation, if the content of any of them exceeds 15 at %, the saturation magnetic flux density will be significantly lowered.

Mo, Zr, Ti, V, Nb, Ta, W, C This is because when the amount is 10 atomic % or less, the magnetic properties are not significantly affected and the effect is achieved. Pr,N
The reason why d, Pm, Sm, Eu, Gd, Th, Dy, and Ho are kept at 5 atomic % or less is that if it is 5 atomic % or less, an amorphous alloy can be manufactured without writing the magnetic properties, but if it exceeds 5 atomic % This is because it becomes difficult to manufacture an amorphous alloy. In addition, in the above-mentioned amorphous alloy, (a)
The reason why any one or more components selected from , (o), (c), and (d) is set to be 50% or less in total is that if the total of these components exceeds 50%, the magnetic permeability decreases. Because it does. As described above, it is possible to easily manufacture a novel magnetic head using an amorphous alloy that has excellent magnetic properties, resistivity, hardness, strength, or corrosion resistance.

In order to manufacture a magnetic head using the alloy of the present invention, the manufacturing apparatus shown in FIG. 1 as an example is used. The cooling rate of the molten alloy obtained by this device is approximately 1 pi to 107 °C/
The alloy of the present invention is ultra-quenched to an amorphous phase using this apparatus. Further, the alloy obtained by ultra-quenching is usually obtained in the form of a thin strip having a thickness of 20 to 50 mm, and the surface has a metallic luster. Therefore, it can be used as is to be molded into a head. As shown in Table 1, Table 2, and Figure 2, the amorphous alloy obtained as described above is highly elastic and not brittle as produced, and exhibits the characteristics of high electrical resistance and high hardness. In addition, it has excellent magnetic properties, particularly high magnetic permeability, low coercive force, and excellent high frequency properties, and is therefore characterized in that it can provide a novel magnetic head that cannot be obtained with conventional head materials.

Conventional magnetic head materials include well-known Alperm alloy (Fe-mountain) and Sendust alloy (Fe-Si-
AI-based alloys are brittle and have poor moldability, while permalloy alloys (Fe-Ni-based) are too soft and difficult to mold, and their performance deteriorates significantly during processing. On the other hand, amorphous alloys have the advantage of being easy to process (punching, polishing, etc.) as head materials because of their high elasticity, so that heads can be easily constructed. The amorphous alloy of the present invention essentially crystallizes upon heating. This crystallization temperature is approximately 40°C for this alloy.
It is in the range of 0 to 500 qo, and if it is heated above this crystallization temperature, various properties peculiar to alumophous alloy will be lost, so it cannot be used as a head. That is, when heated above the crystallization temperature, it loses its elasticity and forms arms, resulting in no workability, and its electrical resistance decreases to about 1:3, making its magnetic permeability and coercive force much worse than conventional materials. Therefore, heating the alloy of the present invention above its crystallization temperature must be avoided. Furthermore, even if the amorphous alloy is heated to a temperature below the crystallization temperature, the characteristics of the amorphous alloy described above may be deteriorated depending on the alloy composition, so it is preferable to use the amorphous alloy in an ultra-quenched state.
However, if the material is not sufficiently ultra-quenched during manufacture, the required magnetic properties may not be obtained, so heat treatment improves the magnetic properties again. For example, if necessary, water cooling after desensitization at 50 qo below the crystallization temperature, 500
Magnetic properties can be improved by applying hammering in a magnetic field of Ørsted level and scorching anchor under stress. The alloy of the present invention is ultra-quenched and then molded to form a head, and the magnetic core for the head can be constructed in exactly the same manner as in the conventional method.

Magnetic heads have various uses.

For example, those for audio, VTR, and computer are well known. Since the characteristics required for these magnetic heads differ depending on the use, it is necessary to select the composition of the alloy of the present invention depending on the use. Amorphous alloys with low Co content can be used for the magnetic heads of inexpensive audio decks, and amorphous alloys with high Co content are suitable for high-end decks. Especially in Table 3, Co7
An alloy containing Fe5 as the main component is optimal.

The present invention will be described with reference to examples.

Example 1 Several representative amorphous alloys shown in Table 2 were produced by the method described above. As a result, they had a thickness of about 30 mm and a width of about 0 mm.
．． 5 Ribbon with uniform dimensions (thin strip sample), approximately 30 mm long
was obtained, and it was confirmed by X-ray diffraction that it was a completely amorphous phase, and the properties shown in Table 3 were obtained.

Table 3 As shown in Table 3, the alloy of the present invention has a hardness of 75
It can be seen that it has extremely high mechanical properties with a cape V of 0 to 86 and a fracture strength of 285 to 305 k9/side 2, and has wear resistance comparable to Sendust alloy.

-On the other hand, it is an amorphous alloy with high electrical resistance, which is advantageous in terms of high frequency characteristics and iron loss. Furthermore, as can be seen from this table, the alloy of the present invention has high magnetic permeability and low coercive force. In particular, Co78B, Bi, 5Fe5 alloys have low magnetostriction, and have lower wear and excellent magnetic properties than Sendust alloys (maximum permeability of 400,000, coercive force of 0.008).
It turns out that he has a plan).

Figure 2 shows the measurement results of the high frequency characteristics of this alloy. As is clear from this figure, the effective magnetic permeability is as high as about 10,000, and it hardly changes up to about 10 frequencies, clearly indicating that a magnetic head with excellent characteristics within the audible frequency range can be obtained. Regarding various compositions of the amorphous alloy of the present invention, Curie temperature (°C), crystallization temperature (0
0), saturation magnetic flux density (KG), effective magnetic permeability, coercive force (m
The results of measuring 0e) are as follows. Table 4 Example 2 Width 2 with various thicknesses by the liquid quenching device shown in Figure 1
A ribbed Fe5Co7oSi,5Bo amorphous alloy was prepared and its magnetic properties were measured.

The results are shown in Table 5. The thickness of the sample was obtained by changing the rotation speed of the rotating drum from 1000 to 800 pm. Table 5 *1KHZ, 3m.

As shown in Table 5, the coercive force and effective magnetic permeability of the sample did not decrease significantly when the thickness of the sample ranged from 15 to 100 mm, but significantly decreased when the thickness increased to 200 mm.

As a result of X-ray analysis of the samples, samples 21 to 24 were all amorphous, but sample 25 contained about 20% crystals. Therefore, the properties of the head material need to be amorphous single phase, and the ultra-quenching rate needs to be 1 picosecond or more. Example
3 The moldability of the sample shown in Example 2 as a head material was investigated.

The results are shown in Table 6. This alloy Fe5Co75Si,
In the case of 5B, o, when the thickness exceeds 100 m, the surface loses its metallic luster and tends to sulfurize, resulting in poor punchability and bendability. Table 6 Therefore, if crystals precipitate in the sample, the moldability as a head material will be lost, so the sample must be in an amorphous phase.

Example 4 Fe5C Takumi.

Ni phantom Si, oB5 amorphous alloy (30-skin thickness,
The magnetic properties of the sample, which had been water-cooled after being hammered, were measured. Figure 3 shows the results. The magnetic flux density is B2. (
Although the residual magnetic flux density of Br is almost constant under a magnetic field of 20° C., it increases slightly at 450° C., and the squareness ratio improves. on the other hand,
Coercive force Hc and effective magnetic permeability Mue are 200qC to 300
It gets worse around qo, but it gets significantly better above that, especially around 450°C. However, when crystallization occurs at 500 qo, the condition deteriorates rapidly and the superiority of the alumofous alloy is completely lost. For this reason, when performing heat treatment, it is not preferable to use a coagulation hammer at least at a temperature higher than the crystallization temperature. Example 5 The amorphous alloy tape (thickness: 30 Am, width: 12 side) shown in Table 7 was produced using the ultra-quenching apparatus shown in Fig. 1, and the effect of heat treatment on its effective magnetic permeability (e) is shown in Fig. 4. show.

Table 7 1 Table 7 2 As shown in the figure, re is a steepness of 1000 when the liquid is rapidly cooled, which is sufficient for the characteristics of a magnetic head, but the characteristics change slightly due to subsequent heat treatment.

In sample 26, the crystallization temperature is higher than the Curie temperature, and the peak e reaches its maximum value by the post-dawn water cooling treatment above Tc. On the other hand, the furnace cooling after moth dulling is lower than that of quenched materials. Also,
When the Curie temperature is higher than the crystallization temperature as in sample 27, the Akatsuki hammering process worsens the peak e. On the other hand, treatment in a magnetic field is effective for both alloys. As mentioned above, the effect of heat treatment is recognized depending on the composition of the alloy. From the above, it can be seen that the alumofous alloy of the present invention has excellent magnetic properties essential for a magnetic head material.

[Brief explanation of the drawing]

FIG. 1 is a schematic diagram showing an example of an apparatus for manufacturing the firmophus alloy for magnetic heads of the present invention, and FIG.
．． A magnetic characteristic diagram showing the relationship between frequency and effective magnetic permeability of an amorphous alloy made of 5Fe5 in comparison with the characteristics of conventional 78Mo permalloy and Alperm. FIG. 4 is a characteristic diagram showing the effect of the dawn anchor treatment on the effective magnetic permeability of the Co-based amorphous alloy. 1... Quartz tube, 2... Nozzle, 3... Raw metal, 4...
... Heating furnace, 5... Rotating drum, 6... Motor, 7...
・Steel plate, 8...air piston, 9...argon gas. Figure 1 Figure 2 Figure 3 Figure 4

Claims (1)

[Scope of Claims] 1. 7 to 35 at% of any one or more of phosphorus, carbon, and boron, and 25% or less of silicon (however, 0%
) and the balance is cobalt only or cobalt and iron (
However, the cobalt content shall be greater than the iron content)
melt an alloy containing and cool this molten metal at an ultra-high speed,
A magnetic head made of a high magnetic permeability amorphous alloy, characterized in that an amorphous amorphous alloy with high magnetic permeability, low coercive force, high hardness, high specific resistance, and excellent high frequency characteristics is made and this amorphous alloy is molded. Manufacturing method. 2. 7 to 35 atomic% of one or more of phosphorus, carbon, and boron, and 25% or less of silicon (but 0%
) and the remainder cobalt only or cobalt and iron (
However, the cobalt content shall be greater than the iron content)
Contains as a main component and as a subcomponent in atomic % (a)
50% or less of nickel, (b) 15% or less of at least one of chromium and metal, (c) selected from molybdenum, zirconium, titanium, aluminum, vanadium, niobium, tantalum, tungsten, copper, germanium, beryllium, and bismuth. and (d) any one or two or more selected from praseodymium, neodymium, promethium, samarium, europium, gadolinium, terbium, dysprosium, and holmium. 5% or less of the above (a),
Any one selected from the group of (b), (c) and (d)
An alloy containing a total of 50% or less of a species or two or more components is melted, and this molten metal is cooled at an ultra-high speed to achieve high magnetic permeability, low coercive force, high hardness, high specific resistance, and excellent high frequency characteristics. 1. A method for manufacturing a magnetic head using a high magnetic permeability amorphous amorphous alloy, which is characterized by making an amorphous amorphous alloy and molding the amorphous amorphous alloy.