JPS60224728A - Wear resistant high magnetic permeability alloy and its manufacture and magnetic recording/reproducing head - Google Patents

Abstract

PURPOSE:To manufacture a high magnetic permeability alloy easy in forging working, having large effective magnetic permeability, saturation flux density and superior in wear resistance, and a magnetic recording and reproducing head made thereof by cold working and heat treating Ni base alloy contg. Nb, P, Fe under specified condition. CONSTITUTION:Ingot contg. alloy composed of 60-90% Ni, 0.5-14% Nb, 0.01- 1% P and the balance Fe, or further many kind elements as auxiliary component is hot forged or hot rolled to rod shape, etc., then annealed at >=600 deg.C temp. Next, said material is cold worked to the aimed shape by >=30% working ratio, heated to temp. of 800 deg.C-m.p., and cooled from temp. of order and disorder lattice transformation point or more by the rate of 100 deg.C/sec-1 deg.C/hr according to compsn. of the alloy. The wear resistant, high magnetic permeability alloy for magnetic recording and reproducing head having >3,000 effective magnetic permeability at 1Hz, >4,000G saturation flux density and recrystallization texture of (110)<112> is manufactured.

Description

[Detailed description of the invention] Abradable high permeability alloy and Ni, Nb, P and li'e as main components, and subcomponents (ir, No.
, Ge3, Au.

Co IV I W, Ou, Ta, Kn
, At, Si, Ti.

, Zr, Hf, Sn, Sb, Ga,
In, Tl, rare earth elements, platinum group elements 115.
Be, A9. Sry lea, B f) 1
This relates to a wear-resistant high magnetic permeability alloy containing a ridge or two or more types, and a method for producing the same, and its purpose is to be easy to forge, have a large effective magnetic permeability, have a saturation magnetic flux density of 4000G or more, The object of the present invention is to obtain a magnetic alloy having a recrystallized texture of (110)<112> and having good wear resistance. Furthermore, the present invention relates to a magnetic recording/reproducing head made of these wear-resistant high permeability alloys.

Since magnetic recording/reproducing heads such as tape recorders operate in alternating magnetic fields, the magnetic alloys used therein must have high effective magnetic permeability in high-frequency magnetic fields, and magnetic tapes must slide in contact with each other. Therefore, it is desired that the wear resistance be good. Currently, as magnetic alloys for magnetic heads with excellent wear resistance, sendust (Fe-3i-Al alloy) and ferrite (M
nO-ZnO-Fe, O,), but these are very hard and brittle and cannot be forged or rolled.6 Grinding and polishing methods are used to manufacture the head core, and therefore the finished product is expensive. Sendust has a high saturation magnetic flux density, but cannot be made into a thin plate, so its effective permeability in a high-frequency magnetic field is relatively low. Further, although ferrite has a high effective magnetic permeability, its disadvantage is that its saturation magnetic flux density is low at about 4000G. On the other hand, permalloy (Ni-Fe alloy) has a high saturation magnetic flux density but a low effective permeability, and is easy to forge, roll, and punch, making it suitable for mass production, but its major drawback is that it wears easily. , it is strongly desired to improve this.

The present inventors have previously discovered that Ni-Fe-Nb alloys are suitable as magnetic alloys for magnetic recording/reproducing heads because they are easy to forge and have excellent high magnetic permeability, and have patented this alloy. Filed (Special Publication No. 47-29690)
issue). Subsequently, the present inventors discovered that the wear phenomenon generally differs depending on the orientation of the alloy crystal, and it is known that crystal anisotropy exists. As a result of research on the relationship between Ni-
In Fe-Nb alloy, (100)<001>
Recrystallized texture is easy to wear, (110)<112
> It was discovered that the recrystallized texture has excellent wear resistance, and this was developed into the patented Jilt (Japanese Patent Publication No. 58-57499
No., Japanese Patent Publication No. 58-26994). .

Based on this knowledge, the present inventors went further and found that it is one of the elements that is said to have the effect of suppressing the formation of (100)<001> recrystallization texture in face-centered cubic metals such as O. P was added to the same face-centered cubic Ni-Fe-Nb alloy, and the formation of recrystallization texture was studied. In other words, when the Ni-Fe binary alloy is cold-rolled, it becomes (1
10) A processing texture of <112> + (112)<111> is produced, but when this is heated at high temperature, it becomes (100)<
001> It is known that a recrystallized texture develops.

However, when Nb is added to this, the stacking fault energy decreases and a (110) <112> recrystallization texture is generated, but by further adding fine P to this, the (100) <001 >The growth of the recrystallized texture is suppressed, the growth of the (110) <112> recrystallized texture is promoted preferentially, and the (iio) <112> recrystallized texture is formed, resulting in significantly improved wear resistance. I found that it can be improved. Furthermore, when P is added to Ni-Fe3-Nb alloy, N1-p, F19-P and Nb-
The hard phosphides of the P yarn are precipitated in the matrix, increasing the hardness and contributing to the improvement of wear resistance. At the same time, the magnetic domains are divided by the dispersed precipitation of these weakly ferromagnetic and non-ferromagnetic fine phosphides. We also found that the eddy current loss in an alternating magnetic field is reduced, which increases the effective magnetic permeability. In short, due to the synergistic effect of decoy and P, (110) <
112> As the recrystallization texture develops, the effective magnetic permeability increases, resulting in a high magnetic permeability alloy with excellent wear resistance.

To make the alloy of the present invention, 60-90% Ni, NbO
, 5-14%, Po, 001-1% and the balance FB were melted in air, preferably in a non-oxidizing atmosphere (hydrogen, argon, nitrogen, etc.) or in vacuum using a suitable melting furnace. After that, a small amount of deoxidizing and desulfurizing agents such as manganese, silicon, aluminum, titanium, calcium alloy, magnesium alloy, beryllium alloy, etc. is added to remove as much impurity as possible. Alternatively, Qr may be added to the above alloy as an axial component.

7% or less of Mo, Ce, All, 10% or less of Co, V, 15% or less of W, 25% of Ou, Ta, Mn
% or less, Sr, Ba, 8% or less, 31% or less, or 2M or more in a predetermined amount of a total of 0.01 to 80%. The mixture thus obtained is 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 forged or hot-worked at high temperatures to form an appropriate shape, such as a bar or a plate, and is then shaped into a metal ingot as required. If so, annealing is performed at a temperature of 600°C or higher.

This is then subjected to a processing rate of 80% by methods such as cold rolling.
The above cold working is performed to produce a thin plate of the desired shape, for example, a thin plate with a thickness of 0.1 #II. Next, an annular plate with an outer diameter of 45 mm and an inner diameter of 88 mm is punched out from the thin plate, and this is heated at 800°C or higher in hydrogen or other suitable non-oxidizing atmosphere (hydrogen, argon, nitrogen, etc.) or in vacuum. Heating at a temperature below the melting point for an appropriate time, then heating at a temperature above the regular-irregular lattice transformation point (approximately 600°C) at 100"C/sec to 1°C
cooling at an appropriate rate corresponding to the composition of
Reheat at the following temperature for an appropriate time and cool. In this way, the effective magnetic permeability is 8000 or more and the saturation magnetic flux density is 4000G.
A wear-resistant high permeability alloy having the above properties and a recrystallization texture of (110)<112> can be obtained.

The invention will now be explained with reference to the drawings.

Figure 1 shows the recrystallization aggregation of an 80%Ni-Fe-5%Nb-P alloy when it is cold rolled at a processing rate of 85%, heated at 1050°C, and then cooled at a rate of 1000°C/hour. This figure shows the relationship between tissue and bone characteristics and P content. When Ni-ye-Nb alloy is cold rolled (
A processing texture of 110)<112>+ (112)<111> is produced, but when this is heated at high temperature, (110)<
A recrystallized texture of 112>+(100)<001> is generated. However, when P is added to this, (100)<0
01>Recrystallization, generation of crystal texture is suppressed, (110)
<11! ＞ recrystallization texture develops, and the amount of purchase decreases accordingly. Moreover, the effective magnetic permeability increases by adding P. Figure 2 shows 80%mi-ye -5%Nb-0
,05%P alloy, the relationship between the recrystallization texture and texture properties and cold working rate when heated at 1050°C, and the increase in cold working rate is (110)<112>
leads to the development of recrystallized texture, improves wear resistance, and increases effective magnetic permeability. Figure 8 shows 80%Ni-Fe
-5%Nb -0.05%P alloy cold working rate 85%
This figure shows the relationship between the heating temperature after rolling with the recrystallized texture and the original properties.
112) <111> component decreases, (llo) <112
> develops, wear resistance improves, and effective magnetic permeability increases. Figure 4 shows alloy number 8 (80%Ni-Fe-5
%Nb-0,05%P alloy), alloy number 41 (79,
5%xi-ye -s%Nb -0,086%P-2%
MO alloy), alloy number 89 (82%Ni-ye-z%
The relationship between the effective magnetic permeability and the cooling rate for the Nb-0,085%P-8%Si alloy) and the effective magnetic permeability (marked with X) when this is further subjected to reheating treatment are shown. It can be seen that there is an optimal cooling rate, optimal reheating temperature, and optimal reheating time that correspond to the composition of the alloy.

Figure 6 is a characteristic diagram of the wear resistance of a magnetic head when Orr MOr Ge e Au or co is added to an 80% ai-ha-5% Nb-0, Q5% P alloy.
When IMOIGe, Au or CO is added,
In both cases, the effective permeability increases and the amount of wear decreases, but O
r.

If MO, Ge, or Au is 7% or more, the saturation magnetic flux density becomes 4000G or less, which is not preferable. Moreover, if CO is 10% or more, the effective magnetic permeability becomes 8000 or less, which is not preferable.

Figure 6 shows the same 80%Ni -Fe -5%Nb -0
, 05% P alloy vr W + Cu, Ta or Mn is added to the magnetic head wear amount and effective magnetic permeability characteristic diagram. The magnetic rate increases,
The amount of wear decreases, but when ■ is 10% or more, W is 15% or more, and Qu.

If 25% or more of Ta or 4n is added, the saturation magnetic flux density becomes 4000 G or less, which is not preferable.

Figure 7 also shows 80% Ni-F1a -5% Hb-o,
o5%P.

-At, Si, Ti, Zr, Hf, Sn, Sb alloy is a characteristic diagram when Ga is added to the alloy, and jU, Si, T
i.

5 Zr, Hf, Sn, Sb or Ga
% or more, the effective magnetic permeability increases and the amount of wear decreases, but Si, Ti, Zr, Hf
Alui has a saturation magnetic flux density of 4000G when Ga is 5% or more.
If i, Sn or sb is 5% or more, forging becomes difficult, which is not preferable.

Figure 8 shows the same 80% Ni-re -5%) Jb -0
,05%P alloy with In, Tl, La l Ru
l Be l This is a characteristic diagram when Ag, Sr, Ba or B is added, and In, Tl.

La, Ru, Bel Ag, Sr, B
When a or B is added, the effective permeability increases and the amount of wear decreases, but: [n, Tl, La
, Ru at 5% or more, Be.

When 8% or more of Sr or Ba is added, the saturation magnetic flux density increases to 4
000G or less, A is 8% or more or B is 1%
Adding more than this amount makes forging difficult, which is not preferable.

In the present invention, cold working is (110)<112)
It is necessary to form a + (112) <111> texture and, based on this, to develop a (110) <112> recrystallization texture, as shown in Figures 1 and 2. At P O,001% or more, especially when the processing rate is 80
(110) <112> when subjected to cold working of % or more
The development of the recrystallized texture is remarkable, the wear resistance is significantly improved, and the effective magnetic permeability is also high. In addition, the heating performed after the cold working described above not only homogenizes the structure and removes processing strain, but also develops a (110)<112> recrystallized texture, resulting in high effective magnetic permeability and excellent wear resistance. 800°C as shown in Figure 8.
The effective magnetic permeability and wear resistance are significantly improved by the above heating.

Note that repeating the above cold working and the subsequent heating above 800°C and below the melting point is (110)<1.
12> is effective for increasing the degree of accumulation of the recrystallized texture and improving wear resistance. In this case, the (110)<i12> recrystallized texture can be obtained even if the final cold working rate is 30% or less, but this is included in the technical idea of the present invention.

When cooling from the temperature above 800°C or higher (m) below the melting point to a temperature above the regular-irregular lattice transformation point (approximately 600°C), there is no significant difference in the magnetic properties obtained whether the cooling is rapid or gradual. However, as shown in Figure 4, a cooling rate below this transformation point has a large effect on magnetism. In other words, by cooling from a temperature above this transformation point to room temperature at an appropriate rate corresponding to the composition of 100°C/sec to 1"C/hour, the regularity of the ground can be adjusted appropriately 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, if the alloy with low order is 2 below its transformation point,
00°C to 600°C for 1 minute or more depending on the composition.
When reheated for 0 hours or less and then cooled, ordering progresses to a suitable degree of order and improves magnetism. On the other hand, if the material is slowly cooled from a temperature above the above-mentioned transformation point at a rate of, for example, 1"C/hour or less, ordering progresses too much and the magnetism decreases.

Note that it is preferable to perform the above heat treatment in an atmosphere where hydrogen is present, since this is particularly effective in increasing the effective magnetic permeability.

Next, the invention will be explained with reference to examples.

Example 1 Alloy number 8 (composition N1-5O%, Nb-5%, P-0.
05%.

99.8% pure electrolytic nickel as raw material, 99.9%
Purity electrolytic iron, 99.8% purity niobium and phosphorus 20
% nickel-phosphorous master alloy was used. To make a sample,
The raw materials were placed in an alumina crucible with a total weight of 800 g, melted in a high frequency induction electric furnace in a vacuum, and then thoroughly stirred to obtain a homogeneous molten alloy. Next, make this with a diameter of 25 mm and a height of 17 mm.
01sfi holes were injected into the mold, and the obtained ingot was forged at about 1000"C to form a plate with a thickness of about 7 mm. Further, it was forged at an appropriate thickness between about 900"C and 1000C. The sheet was hot-rolled at room temperature and then cold-rolled at various processing rates at room temperature to form a thin sheet with a diameter of 0.111131.
I. An annular plate with an inner diameter of 88#ll11 was punched out.

Next, this was subjected to various heat treatments to improve its magnetic properties and when used as the core of a magnetic head, m1V80%, 40%.
The wear of Orb and magnetic tape after 200 hours at °C was measured using a Taliser 7 surface roughness meter.
We obtained the characteristics shown in the table.

Example 2 Alloy number 41 (composition Mi-79.5%, Wb-8%,
The raw materials for producing the alloy (P - 0,085%, No - 2%, Fe - balance) are nickel and iron of the same purity as in Example 1, niobium of 99.8% purity, molybdenum and iron-phosphorus of 10% phosphorus. A mother alloy was used. The method of manufacturing the sample was the same as in Example 1. When the sample is subjected to various heat treatments to improve its magnetic properties and is used as the core of a magnetic head, the humidity is 80% and the temperature is +
The amount of wear after 200 hours was measured using crocodile and magnetic tape at 40°C, and the characteristics shown in Table 2 were obtained.

The characteristics of typical alloys are shown in Table 8.

The alloys listed in each of the above Examples, Table 8 and the drawings include relatively pure metals Nb, Or, Mo, and W.
.

Mn, V, Ti, Al, Si, and rare earth elements have been used in the past, but even if economically advantageous commercially available 17)7 alloys, master alloys, and misch metals are used in their place, desorption occurs during melting. If acid and desulfurization are performed sufficiently, the magnetic properties are almost the same as when these metals are used alone.
Provides wear resistance and processability.

As mentioned above, the alloy of the present invention is easy to process, has excellent wear resistance, has a saturation magnetic flux density of 4000 G or more, high magnetic permeability, and low coercive force, so it can be used as a magnetic material for cores and cases of magnetic recording/reproducing heads. Not only is it suitable as an alloy, but
It is also suitable as a magnetic material for general electromagnetic equipment that requires wear resistance and high magnetic permeability.

Next, in the present invention, the composition of the alloy is N16o~90%, N
b0.5-14%, Po, 001-1% and balance Fe
3, and the element added as a subcomponent to this is Or
+MO+Ge, Au 7% or less, CO, V 1
0% or less, W 15% or less, Ou, Ta, Mn
25% or less, ht, si, Ti, Zr
, Hf, Sn, Sb, Ga.

5% or less of In, Tt, rare earth elements, platinum group elements,
Be, Ag, Sr l Ba 8% or less, B 1
Total of one or more types below % to 0.01・30
%, as is clear from each example, Table 8, and drawings, the effective magnetic permeability in this composition range is 8000 or more, the saturation magnetic flux density is 4000G or more, and (110)41
This is because although it has a recrystallized texture of 2> and has excellent wear resistance, if it deviates from this composition range, the magnetic properties or wear resistance will deteriorate.

i.e. Nb O, 5% or less and PO, 001%
Below, the recrystallized texture of (110)<112> is not sufficiently developed, resulting in poor wear resistance (Nb of 14% or more and 21% or more makes forging difficult, and the effective magnetic permeability is less than 8000 and the saturation magnetic flux density is 4000G). This is because the following is true.

and Ni 60-90%, Wb O, 5-14%, P
It has excellent wear resistance and good workability, but it is generally made of Or, MO, Ge, Au, W, V, etc.

Ou, Ta, Mn, kl, Zr, Si,
Ti, Hf, Ga.

Adding rare earth elements, Be, Ag, B, etc. has the effect of particularly increasing the effective magnetic permeability, and adding CO has the effect of particularly increasing the saturation magnetic flux density.
, Ta, W, Ti, Zr, Hf
, At, Si, Sn.

sb, Ga, In, Tl, rare earth elements, platinum group elements.

Adding Be, kg, Sr l Bar B, etc. has the effect of particularly improving wear resistance, and adding Au,
Mn, Ti, Co.

Addition of rare earth elements, Be, Sr, Ba, and B has the effect of improving forging and processing.

In addition, if it is desired to improve the machinability of the alloy of the present invention depending on the application, it may be necessary to
Small amounts of tellurium, sulfur, calcium, bismuth and selenium may be added.

Furthermore, since carbon, oxygen, and nitrogen improve wear resistance, they may be contained in small amounts as long as they do not impair workability.

[Brief explanation of the drawing]

Figure 1 is a characteristic diagram showing the relationship between the initial properties and the amount of P for the 80%Ni-Fe-5%Nb-P alloy. Figure 2 is 80%Xi-Fe-5%Nb-0.05%P.
Characteristic diagram showing the relationship between alloy properties and cold working rate, No. 8
The figure shows 80%Ni -Fe -5%Nb -0.05%P
A characteristic diagram showing the relationship between alloy properties and heating temperature, Figure 4 shows 80%N1-Fe-6%Nb-0.05%P alloy (alloy number 8), 79.5%Ni-ye-s %Nb −
0, Oa5%P-2%MO alloy (41), and 82%
Ni-ye -2%)ib -0,085%P-13%
Characteristic diagram showing the relationship between effective magnetic permeability, cooling rate, reheating temperature and reheating time of Si alloy (89), Figure 6 is 80%Ni -Fe -5%Nb -0,05
%P alloy with Qr, MO, Qe, Au or G
A characteristic diagram showing the relationship between the characteristics when O is added and the amount of each element added, Figure 6 is 80%Ni-Fe-5%Nb-0
, 05%P alloy, when V, W, Ou, Ta or Mn is added, the characteristic diagram showing the relationship between the characteristics and the amount of addition of each element, Figure 7 is 80%xi-ye-5%
Nb-0,05%P alloy with kl, Si, Ti
, Zr, Hf, Sn, Sb or Button is added. Figure 8 is a characteristic diagram showing the relationship between the initial characteristics and the amount of each element added.
Be + kg y Sr. FIG. 2 is a characteristic diagram showing the relationship between the characteristics when Ba or B is added and the amount of each element added. Patent Applicant: Institute of Electric and Magnetic Materials Foundation Karaskon Inaq Motion Range Figure 5 Cr, Morζre, Aa or Co (%) Figure 6 Vr Wz C11rT12 07 /'Ph (%)
Figure 7 Me υ 54″71orZr (X) Hf,,f;n,
Sbor8a (gji figure 8

Claims (1)

[Claims] 1. N160-90%, Nb O, 5-14% by weight
%, P O,001~1% and the balance is Fe and a small amount of impurities, and the effective permeability at I KHz is 8000.
above, the saturation magnetic flux density is 4000G or above, and (110)
A wear-resistant high permeability alloy characterized by having a <112> recrystallization texture. ? , Ni60-90%, Nb 0.5-1 by weight ratio
The main components are 4%, Po, 001-1% and the balance Fe, and the secondary components are Qr * MOr Ger Au 7% or less, Co and V 10% or less each, W
15% or less, Ou, Ta, Mn each 25% or less, A4, Si, Ti, Zr. Hf, Sn, Sb, Ga, In,
Tl l Rare earth element. 5% or less of each of platinum group elements, Be, A, and . Sr and Ba are each 8% or less, and B is 1% or less.
The effective magnetic permeability at IKH2 is 80
00 or more, saturation magnetic flux density 4000G or more, and (11
0) A wear-resistant high permeability alloy characterized by having a <112> recrystallization texture. & Weight ratio: Ni 60-90%, Nb O, 5-14
%, PO,001~1% and the balance F6 and a small amount of impurities is subjected to cold working at a processing rate of 80% or more, then heated at a temperature of 800"C or more and below the melting point, and then processed according to the rule - 100”C/from temperature above irregular lattice transformation point
By cooling to room temperature at an appropriate rate corresponding to the composition of seconds to 1'C/hour, the effective magnetic permeability in lKH2 is 80.
00 or more, saturation magnetic flux density 4000G or more, and (11
0) A method for producing a wear-resistant high permeability alloy characterized by a <112> recrystallization texture. 4 N160-90% by weight, Nb O, 5-14
%, PO,001~1%, the balance Fe and a small amount of impurities are subjected to cold working at a processing rate of 80% or more, then heated at a temperature of soo'c or more and less than the melting point, and then processed according to the rule - Cool from a temperature above the disordered lattice transformation point at an appropriate rate corresponding to the composition of 100"C/sec to 1°C/hour, and then cool for 1 minute or more at a temperature below the ordered-disordered lattice transformation point. By heating and cooling for an appropriate time corresponding to the composition of
0 or more, the saturation magnetic flux density is 4000G or more, and (110
) A method for producing a wear-resistant high permeability alloy, which is characterized by forming a recrystallized texture of <112>. Lively N160-90% by weight, Nb O, 5-14
%, PO, 001~1% and the balance Fe as the main components, Or, MO, Ge, Au as subcomponents of 7% or less, CO1■ of 10% or less each, W as 1
5% or less, Qu, Ta, Mn each 2b% or less, A! , Si, Ti, Zr, Hf +
sn, sb, Ga, InrTl + rare earth elements, platinum group elements each at 5% or less, Be,
A9y Sr*Ba each 3 su, v, B 1% or less or 21a or more total 0.01 to 80
%, and a small amount of impurities, is subjected to cold working at a processing rate of 30% or more, heated at a temperature of 800°C to below the E melting point, and then heated from a temperature above the regular-disorder lattice transformation point to 1
By cooling to room temperature at an appropriate rate corresponding to the composition of 00°C7/sec to 1°C/hour, the effective magnetic permeability at I KHz is 8000 or more, the saturation magnetic flux density is 4000G or more, and (110)<112> A method for producing a wear-resistant high permeability alloy characterized by forming a recrystallized texture. a weight ratio n1ao ~90%, l'lb O,6
~14%, PO, 001~1% and the remainder F6 as the main component and subcomponents as Or, MO, Ge, Au
7% or less each, CO and V 10% or less each,
W 16% or less, Qu, Ta, Mn each 25% or less, L, Si, Ti, Zr,
Hf. Sn, Sb, Ga, In, Tl, rare earth elements, platinum group elements each at 6% or less, Be e
After cold working at a processing rate of 80% or more on an alloy consisting of 8% or less of A9 v 5ryB&, 1% or less of B, or a total of 0.01 to 80% of two or more, and a small amount of impurities. , heated at a temperature of 800°C or higher and lower than the melting point, and then heated at a temperature of 100°C or higher than the regular-irregular lattice transformation point.
Cool at an appropriate rate corresponding to the composition from °C/sec to 1 °C/hour, and then heat at a temperature below the ordered-disorder lattice transformation point for an appropriate time corresponding to the composition for 1 minute to 100 hours. A wear-resistant high permeability alloy characterized by having an effective magnetic permeability in IKH2 of 8000 or more, a saturation magnetic flux density of 4000G or more, and forming a recrystallized texture of (110) < 112 > by cooling. Manufacturing method. 7 In terms of weight ratio, nio~90%, NbO, 6~1
4%, P 0.001-1%, balance Fe and a small amount of impurities, effective permeability at I KHz 800
0 or more, the saturation magnetic flux density is 4000G or more, and (110
) A magnetic recording/reproducing head made of a wear-resistant high permeability alloy having a <112> recrystallization texture. & ・Ni 60-90%, Nb O, 5-90% by weight
14%, p 0.001-1% and the balance Fe as the main components, Or, Mo, Ge as minor components.
Au 7% or less each, Co and V 10% each
Below, W is 15% or less, Cu, Ta, Mn are each 2I11% or less, kl, Si, Ti
, Zr. Hf, Sn, Sb, Ga, In,
Tj, rare earth element; 5% or less of platinum group elements, Be, A, each. Consists of 8% or less of each of Sr and Ba, 0.01 to 80% in total of one or more types of Bt-1% or less, and a small amount of impurities, and has an effective magnetic permeability of 800 at lKH2.
0 or more, the saturation magnetic flux density is 4000G or more, and (110
) A magnetic recording/reproducing head made of a wear-resistant high permeability alloy having a <112> recrystallization texture.