JPS58150119A - Alloy having high magnetic permeability for magnetic recording and reproducing head and its production, and magnetic recording and reproducing head - Google Patents

Abstract

PURPOSE:To obtain a magnetic alloy for magnetic heads which is easy to forge, has high magnetic permeability and high resistance to abrasion by adding specific elements to an Ni-Fe-Cu alloy. CONSTITUTION:The alloy contains, by weight, the auxiliary components of the following compsn. in the essential components contg. 37-75% Ni and 35% Cu and consisting of the balance Fe: The auxiliary components are composed of 0.01-30% the auxiliary components in total of 1 or >=2 kinds among <=20% Ta, <=15% each Cr, Mo, W, <=10% each Nb, V, Mn, Co, Ge, <=5% each rare earth elements, Ti, Ga, In, Tl, Al, Si, Zr, Hf, Pt group elements, <=3% each Be, Sn, Sb, and <=1% each B, P, and a small amt. of impurities. The alloy of such compsn. has 4,000G satd. magnetic flux density, have high magnetic permeability and resistance to abrasion, and is usable for magnetic heads, etc.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a magnetic alloy that has high magnetic permeability, excellent wear resistance, and is easy to forge, and is suitable for magnetic recording/reproducing heads.

Magnetic alloys used in the cores and nurses of magnetic heads for magnetic recording, VTRs, etc. are required to have high magnetic permeability, and because magnetic tapes slide in contact with each other, they are expected to have good wear resistance. It's getting worse.

Conventionally, N1 approximately 8 is easy to process as a magnetic alloy for magnetic heads.
N1-Fa based alloys containing 0% have been mainly used. However, since the product is relatively expensive because it contains a large amount of expensive Ni, an inexpensive Ni-lFe alloy with a low N1 content and high magnetic permeability is desired. On the other hand, Ni-Fe
-0u association, its permeability increases with the increase of Ou amount
It is known that alloys with a small amount of i increase in size, but the initial magnetic permeability reaches its maximum value and is at most l! It is small at 100G, and has a Vickers hardness of 110, so its major drawback is that it is easily worn. The present inventor conducted numerous studies by adding various elements to the N1-IF6-Ou gold alloy, and finally [11
We have discovered a magnetic alloy for magnetic heads that is easy to process, has high magnetic permeability, and has excellent wear resistance.

The present invention has a weight ratio of nickel aS to ma 5% and steel 6 to 8.
The main components are 5% and iron balance, and tantalum 20 as a subcomponent.
% or less, each of chromium, molybdenum, and tungsten! 1% or less, niobium, vanadium, manganese, cobalt, germanium cracking 10% or less, rare earth elements,
titanium, gallium.

Ingenium. Thallium, aluminum, nitric acid.

i% of each of zirconium, hafnium, and platinum group elements
Below, beryllium, tin, antimony each with 8 or less, boron, phosphorus with 15 or less each III or 3
The present invention relates to a high magnetic permeability alloy which has a saturation magnetic flux density of 4000 Qt1ir, has a high magnetic permeability and excellent wear resistance, and can be used for magnetic heads etc. Furthermore, the present invention uses the above-mentioned high magnetic permeability alloy for the case and core. This relates to a magnetic recording/reproducing head manufactured by the company.

To produce the alloy of the present invention, first, an appropriate amount of nickel is melted in a non-oxidizing H atmosphere or vacuum using an appropriate melting furnace, and then a small amount of an appropriate deoxidizing agent, deil@ is added. Remove impurities as much as possible, including less than 10% tantalum, chromium, and molybdenum.

16% or less each of tungsten, 10% each of niobium, vanadium, manganese, cobalt, germanium
% or less, rare earth elements, titanium, gallium, indium, thallium, aluminum, silicon, zirconium,
hafnium, platinum group elements) 6% or less each; beryllium, tin, antimony 8% or less each;
A fixed amount of 1 to 0% is added and thoroughly stirred to produce a compositionally uniform molten alloy. Next, this is poured into a mold of an appropriate shape and size to obtain a sound ingot, which is then subjected to forming processes such as forging at high temperatures and hot and cold rolling to obtain the desired shape, e.g. Make a thin plate with a thickness of 0.1. Next, punch out the desired shape and size from the thin plate,
This is carried out in a non-oxidizing zero H atmosphere or in vacuum at a temperature higher than the recrystallization temperature, that is, approximately 600°C or higher, preferably SOO.
℃ or above and below the melting point for 1 minute or more, and then at an appropriate rate depending on the composition, for example, 10 G'C/i ~ 1
Cool at 'C/h. Depending on the composition of the alloy, this can be further heated to a temperature of about 600°C or below (temperature below the ordered lattice-irregular lattice transformation point), sometimes 100 to 600°C for more than 1 minute, and then cooled to achieve a saturation magnetic flux density of 4000G or more. A high permeability magnetic alloy with excellent wear resistance can be obtained.

From the above solution temperature to the regular-disordered lattice transformation point (approximately s
When cooling to a temperature above o o'c , there is no significant difference in the magnetism obtained whether the material is rapidly cooled or slowly cooled, but the cooling rate below this transformation point has a large effect on the magnetism. In other words, by cooling from a temperature above this transformation point to room temperature at an appropriate rate of 100°C/sec to 1" corresponding to the composition at C7, the degree of order can be appropriately adjusted and excellent magnetism can be obtained. When rapidly cooled at a rate close to 100°C/sec among the above cooling rates, the degree of order decreases, and if the cooling rate is faster than this, the degree of order does not progress, the degree of order decreases further, and the magnetism deteriorates.However, the degree of order decreases. When an alloy with a small degree of magnetization is heated to 300° C. to 600° C., which is below its inflection point, and then cooled, ordering progresses to a moderate degree of ordering, and the magnetism improves.

On the other hand, from the temperature above the above transformation point, for example 1'C7
If it is slowly cooled at a speed lower than 100 hr, the ordering will progress too much and the magnetism will decrease.

Next, embodiments of the present invention will be described.

・Example alloy number @s8 (composition Ni-61, Ii 0u-11,
011.

Nbs, 0%, 8 parts F6) To make a sample, put the entire amount into a 5-foot alumina crucible,
After melting in vacuum in a high-frequency induction electric furnace, 10.8% Mn was added as a deoxidizing agent, and the mixture was thoroughly stirred to obtain a homogeneous molten alloy. Next, this [direct lime■, height 17Qsm
The ingot is poured into a lid with holes, and the resulting ingot is heated to approximately 1100°.
C forged into a plate with a thickness of about 〒-. Further about soo'
It was hot-rolled at a temperature between c and 900°C to a thickness of 1, and then cold-rolled at room temperature to form a thin plate with a thickness of 0.1. An annular plate with an inner diameter of 8.delta. and the core of a magnetic head were punched out. Next, this is 10 days in a hydrogen atmosphere.
After heat treatment at 10°C for 8 hours, the annular plate was used to measure the magnetic properties and hardness, and the core was used to manufacture a magnetic head, and a surface roughness needle was used to measure the amount of wear on the magnetic tape after 100 hours. It was shown to.

Table 8 also shows the properties of representative alloys produced in ceramic form.

As seen in aSS, the Ni-Fe-0u alloy has an initial magnetic permeability of 111,000, a maximum magnetic permeability of 80,000, and a Vickers hardness of 11G, which are poor in magnetic properties and wear resistance, but alloy number 88 has an initial magnetic permeability of 1500, maximum magnetic permeability of 117ooo, and Vickers hardness of 171, it has excellent magnetic properties and wear resistance, and is suitable as a magnetic alloy for magnetic heads.

In short, the alloy of the present invention is easy to forge and process, has excellent magnetic properties and wear resistance, and is not only suitable as a magnetic alloy for magnetic heads, but also very suitable as a magnetic material for ordinary electrical equipment. It is.

Next, the reasons for limiting the alloy of the present invention will be described.

Nickel I! i~? ! i%, copper! i~81%, remainder 1e
tantalum, chromium, molybdenum, and tungsten.

Niobium, vanadium, manganese, germanium.

Adding rare earth elements, titanium, aluminum, silicon, platinum group elements, etc. has a particularly large effect on increasing magnetic permeability.
Tantalum, niobium, batium, gel! Ni, Titanium, Gallium, Indium, Thallium, Aluminum, Ni, Zirconium, Hafnium, Beryllium, Tin,
Unchicken. Adding materials such as Pone and phosphorus has a particularly large effect on increasing hardness, adding cobalt has a large effect on increasing saturation magnetic flux density, and adding manganese, titanium, etc. has a large effect on improving forging workability, but tantalum has a large effect on improving forging workability. 10% or more, tarom, molybdenum.

When 11% or more of each of tungsten and 10% or more of each of niobium, vanadium, and germanium are added, the saturation magnetic flux density becomes 4000G or less□.

So it's not desirable. Also, 1 each of X Ngan and Cobalt.
04 or higher, rare earth elements, titanium, gallium.

Adding more than 6% of indium, thallium, and platinum group elements is not preferable because the magnetic permeability decreases. Aluminum, nitric acid, zirconium, hafnium, beryllium, tin.

Each of antimony aS and above, porin. If phosphorus is added in an amount of 1 or more, forging becomes impossible, so each additive element is limited as described above. Furthermore, the sum of these s1g bulk elements is 0.
If it is less than 0.01%, there is no effect of addition, and if it is more than 8011%, the saturation magnetic flux density will be less than 4000G, which is not preferable because it cannot be used in a magnetic head.

Furthermore, Part 1 II! And as is clear from Table 2, 1j
If any of the i-Fe-Ou gold alloy additive elements is added, the magnetic permeability will increase, the hardness will also increase, and the wear resistance will be improved, so these additive elements have the same effect and are the same effective components. It can be regarded as. Rare earth elements include scandium,
Although it is composed of yttrium and lanthanum-based elements, its effects are exactly the same. Platinum group elements are composed of platinum, iridium, ruthenium, rhodium, palladium, and osmium, and their effects are exactly the same.

In addition, impurities include carbon, oxygen, nitrogen, and sulfur, which generally impair workability when mixed in large amounts, but increase hardness and improve wear resistance. Furthermore, they precipitate as intermetallic compounds and increase effective magnetic permeability. Since the effect is also embroidered, there is no problem in containing up to 0.1% of each.

Claims (1)

[Claims] L 86-76% nickel by weight, #16-aS-
The main component is residual iron, and the secondary components are less than 1G of tantalum, chromium, and molybdenum. Less than 16% of tungsten and niobium, respectively. 10% or less of each of vanadium, manganese, cobalt, germanium, 5% or less of each of rare earth elements, titanium, gallium, indium, thallium, aluminum, nickel, zirconium, ha7nium, platinum group elements, beryllium, tin, Less than 8% of each of antimony, boron,
One or eight or more subcomponents each containing 1% or less of phosphorus, totaling 0. A high permeability alloy for a magnetic recording/reproducing head, comprising O1 to O80 and a small amount of impurities, and having a saturation magnetic flux density of 4000G or more. l The main components are nickel 8i to ma SS, steel 10 to 8i, niobium 0.6 to 10% iron alS, and the subcomponents are tantalum less than 1G, phosphorus, molybdenum, and tungsten.16 % or less, each of vanadium, manganese, cobalt, germanium 1051 or less, rare earth elements, titanium, gallium, indium. Thallium, aluminum, silicon, zirconium, hafnium, platinum group elements, beryllium,
It consists of 8% or less each of tin and antimony, 111 or less of boron and phosphorus, a total of 0.01 to 80% of lI components of 8 or more types, and a small amount of impurities, and has a saturation magnetic flux density of 4004)G A high magnetic permeability alloy for a magnetic recording head, characterized by having the above characteristics. The main components are nickel 8i to 1%, steel ink to 85% iron, and tantalum 1G or less as a secondary component, based on the weight ratio.
Chromium, molybdenum, tungsten, each below the li sac, and niobium. Vanadium, manganese, cobalt, gel! Rare earth elements, titanium, gallium, indium, thallium, aluminum, silicon, zirconium, hydrogen, platinum group elements each have an Is% of 101 or less, beryllium, tin, antimony each have 8% or less, boron , an alloy consisting of 1% or less of phosphorus, a total of 0.01 to 80 of one or more subcomponents, and a small amount of impurities, in a non-oxidizing atmosphere or in vacuum at a temperature of 600°C or more and less than the melting point. , after heating for an appropriate time corresponding to the composition for at least 1 minute to 100 hours, from a temperature above the ordered-disorder lattice transformation point at an appropriate rate corresponding to the composition from 100 ° C / sec to 1 ° C / hour. A method for manufacturing a high permeability alloy for magnetic recording/reproducing heads that is cooled to room temperature. The main components are 85 to 16% nickel and the remainder of copperware to 81S iron by weight, with subcomponents of up to 10% tantalum, up to 15% each of chromium and molybdenum/tungsten, and niobium. 10% or less of each of vanadium, manganese, cobalt, germanium, rare earth bonds, titanium, gallium, indium, thallium, aluminum, silicon, zirconium, hafnium, that of platinum group elements, beryllium, tin, each of antimony & duck, boron,
An alloy consisting of 1% or less of phosphorus each or a total of 0.0L-801G of 8 or more subcomponents and a small amount of impurities is prepared in a non-oxidizing atmosphere or in a vacuum at a temperature above AOO'C and below the melting point. After heating for an appropriate time corresponding to the composition from 1 minute to 100 hours, heat from a temperature above the regular-irregular lattice deformation point at an appropriate rate corresponding to the composition of 10'C, 4 to 1'C7. Magnetic recording and reproducing characterized by cooling to room temperature, further heating at a temperature below the regular-disorder lattice transformation point in a non-oxidizing atmosphere or in vacuum for an appropriate time corresponding to the composition for 1 minute or more, and cooling. Manufacturing method of high magnetic permeability alloy for heads. 1 The main components are nickel S ~ 1 ink, the balance of steel wire ~ 85 duck iron, and the subcomponents are tantalum 20 kg, chromium, molybdenum, and tungsten each 16% or less,
Less than 10% each of niobium, vanadium, manganese, cobalt, and germanium, rare earth elements, and titanium. Gallium, indium, thallium, aluminum, silicon, zirconium, hafnium. Less than 5% of each of the platinum group elements, beryllium. Less than 8% of each of tin and antimony. A magnetic recording/reproducing head comprising an alloy comprising one or more subcomponents of 1% or less of phosphorus, a total of 0.01 to 80% of each subcomponent, and a small amount of impurities, and having a saturation magnetic flux density of 4000G or more. .