JPH02138449A - Manufacture of wear resistant high permeability alloy - Google Patents

Abstract

PURPOSE:To manufacture a wear resistant high permeability alloy by subjecting an alloy composed principally of specific percentages of Ni, Nb, P, S, and Fe and containing specific amounts of Cr, etc., as accessory components to hot working, cold working, heating, and cooling, in succession, under respectively specified conditions. CONSTITUTION:An alloy which has a composition composed principally of, by weight ratio, 60-90% Ni, 0.5-14% 14b, 0.001-1%, in total, of P and S (S is <=0.1% and P and S are >0%, respectively), and the balance Fe and containing, as accessory components, 0.01-30%, in total, of one or >=2 kinds among <=7% each of Cr, Mo, Ge, Au, and other elements and small amounts of impurities is hot-worked at >900-1000 deg.C and cooled. Subsequently, the above alloy is cold-worked at >=50% draft, heated up to a temp. between 900 deg.C and the melting point, and then cooled from a temp. of the superlattice - disordered lattice transformation point or above down to the ordinary temp. at an adequate rate corresponding to the composition, 100 deg.C/sec-1 deg.C/hr. By this method, the alloy in which effective permeability at 1kHz and saturation magnetic flux density are regulated to >=3000 and >=4000G, respectively, and which has a recrystallized texture of {110}<112>+{311}<112> can be obtained.

Description

Detailed Description of the Invention (Industrial Application Field) The present invention contains Ni, Nb, P, S, and Fe as main components, and Cr, Mo, Ge, and Au as subcomponents.

Co, V, W, Cu, Ta, Mn, Al, St.

Ti, Zr, Hf, Sn, Sb, Ga, In.

Te, Zn, Cd, rare earth elements, platinum group elements.

This relates to a method for producing a wear-resistant high permeability alloy containing one or more of Be, Ag, Sr, Ba, and B.
The objectives are to have easy forging, high effective permeability, saturation magnetic flux density of 40,000 or more, and (11
0) <112>+ +311) To obtain a magnetic alloy having a recrystallized texture of <112> and good wear resistance.

(Prior Art) Magnetic recording/reproducing heads such as tape recorders operate in alternating magnetic fields, so the magnetic alloys used therein are required to have high effective magnetic permeability in high-frequency magnetic fields, and the magnetic tape must be in contact with It is desired that the wear resistance is good because it slides on the surface. Currently, as magnetic alloys for magnetic heads with excellent wear resistance, Sendust (Fe-Si-Aρ alloy) and ferrite (M n
0ZnOFezO3), but these are extremely hard and brittle and cannot be forged or rolled. Grinding and grinding methods are used to manufacture head cores, and the products are therefore 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 drawback is that its saturation magnetic flux density is low at approximately 4000 G. On the other hand, permalloy (Ni-Fe alloy) has a high saturation magnetic flux density, but
It has a small effective permeability and is easy to forge, roll and punch, making it suitable for mass production. However, its major drawback is that it is prone to wear, and there is a strong desire to improve this.

(Problems to be Solved by the Invention) The present invention is based on the fact that the Ni-Fe-Nb alloy is easy to forge, has high hardness, and has excellent magnetic permeability. He discovered that it was suitable as a magnetic alloy for industrial use, and filed a patent application for it (Japanese Patent Publication No. 47-2
No. 9690). Afterwards, the present inventors discovered that Ni-Fe-Nb
As a result of systematic research on the wear of Ni-based alloys,
It has become clear that the wear of -Fe-Nb alloys is not uniquely determined by hardness, but is closely related to the recrystallization texture of the alloy.

(Means for solving problems) The features of the present invention are as follows.

First invention weight ratio: Ni 60-90%, Nb 0.5-14%,
Total of P and S 0.001-1% (However, S0.1%
(Hereinafter, P and S do not include 0%) and the balance is Fe as the main components, and the subcomponents are Cr, Mo, and Ge.

Au: 7% or less each, Co, V: 10% each
Below, W is 15% or less, Cu, Ta, and Mn are each 25% or less, Al, St, Ti, Zr, and Hf.

Sn, Sb, Ga, In, Tl, Zn, C
d, rare earth elements and platinum group elements each at 5% or less, Be
.

An alloy consisting of 3% or less each of Ag, Sr, and Ba, and 1% or less of B, a total of 0.01 to 30% of one or more types, and a small amount of impurities, at a temperature of more than 900°C and less than 1000°C. After hot working, it is cooled, then cold worked at a processing rate of 50% or more, heated at a temperature of 900°C or more and below the melting point, and then heated to 100°C/100°C from a temperature above the regular-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 at 1 KHz is 3000 or more, the saturation magnetic flux density is 40000 or more, and (001<112>+{311) <112> A method for producing a wear-resistant high permeability alloy characterized by forming a recrystallized texture.

Second invention weight ratio: Ni60-90%, Nb0.5-14%, P
and S total o, oot~1% (however, so, i% or less, P and S do not include 0%) and the remainder Fe as the main components, and Cr, Mo, and Ge as subcomponents.

Au: 7% or less, Co, V: 10% or less, W: 15% or less, Cu, Ta, Mn: 25% or less, Ap, St, Ti, Zr, Hf.

Sn, Sb, Ga, In, Tl, Zn, C
d, rare earth elements and platinum group elements each at 5% or less, Be
.

An alloy consisting of 3% or less each of Ag, Sr, and Ba, and 1% or less of B, a total of 0.01 to 30% of one or more types, and a small amount of impurities, at a temperature of more than 900°C and less than 1000°C. After hot working, it is cooled, then cold worked at a processing rate of 50% or more, heated at a temperature of 900°C or more and below the melting point, and then heated from a temperature below the regular-irregular lattice transformation point to 1
Cool at an appropriate rate corresponding to the composition, from 00°C/sec to 1°C/hour, and further heat at a temperature below the ordered-disorder lattice transformation point for an appropriate time corresponding to the composition, from 1 minute to 100 hours. High wear resistance characterized by forming a recrystallized texture of (1101<112> + (3111<112>) with an effective magnetic permeability of 3000 or more and a saturation magnetic flux density of 40000 or more at 1 KHz by cooling. Manufacturing method of magnetic permeability alloy.

(Function) In general, wear phenomena vary greatly depending on the orientation of alloy crystals, and it is known that crystal anisotropy exists.
In i-Fe-Nb alloys, (100) <001
> Recrystallized texture is easy to wear, +110) <11
2> and rotated somewhat around this <112> direction (3
11) It has become clear that the recrystallized texture of <112> has excellent wear resistance. That is, N i-
F e N b alloy is (110) <112> + {
They have discovered that wear resistance is significantly improved by forming a recrystallized texture of 311+<112>.

Based on this knowledge, the present inventors calculated Hlo) <112>+ (31,1) <11 of the Ni-Fe-Nb alloy.
．． As a result of carrying out numerous studies to form the recrystallized texture of
% (however, 5O 61% or less, P and S not included 0%), the development of (100) <ool> recrystallized texture is suppressed, and (1101 <112> 0 (31N <
112> was found to significantly promote the formation of recrystallized texture. In other words, when the Ni-Fe binary alloy is cold rolled, it becomes [110) <112>+ (1
12) A <111> recrystallized aggregated texture is produced, but it is known that when this is heated at a high temperature, a (100) <001> recrystallized aggregated i11 weave develops. However, 2. When Nb is added to this, the stacking fault energy decreases, but in addition, the total of P and S is o, ooi ~1% (however, 30.1% or less, P and S do not include 0%) When added, phosphides and sulfides precipitate at the grain boundaries, lowering the grain boundary energy, strongly suppressing the development of the (100) <001> recrystallization texture in secondary recrystallization, and (1101<11. 2>+
(31], j The growth of the recrystallized texture of <112> is preferentially promoted, +1it)) <112>+ (3
A recrystallized texture of 111<1.12> is formed, and wear resistance is significantly improved. In addition, when P and S are added to Ni-Fe-Nb alloys, hard phosphides and sulfides are precipitated in the matrix, contributing to improved wear resistance, as well as weakly ferromagnetic and non-ferromagnetic fine particles. We also found that the dispersed precipitation of phosphides and sulfides splits the magnetic domains, reducing eddy current losses in alternating magnetic fields, thereby increasing the effective permeability. In short, Nb
Due to the synergistic effect of P and S, (1,10) <1
As the recrystallized Mn weave of 12>+{311)<112> develops, the effective magnetic permeability increases, and a high magnetic permeability)1(!) alloy with excellent wear resistance is obtained.

To make the alloy of the present invention, 60-90% Ni, Nho,
5 to 14%, a total of P and S, o, oot to 1% (however, 50.1% or less, P and S do not include 0%) and the balance Fe in an appropriate amount in air, preferably a non-oxidizing Melt in an atmosphere (hydrogen, argon, nitrogen, etc.) or in vacuum using a suitable melting furnace. The above alloy contains Cr, Mo, and Ge as subcomponents.

7% or less of Au, 10% or less of Co, V, 15% or less of W, 25% or less of Cu, Ta, Mn, A1. Si.

Ti, Zr, Hf, Sn, sb, Ga, In.

5% or less of Ti, Zn, Cd, rare earth elements, platinum group elements, 3% or less of Be, Ag, Sr, Ba, 1% or less of B, a total of 0.01 to 30% of one or more types. Further add a predetermined amount. Furthermore, in order to improve forgeability and workability, a small amount (0.5% or less of each) of C, Ca, Mg, etc. is added as a deoxidizing agent if necessary. The mixture thus obtained is sufficiently 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 plate. , annealed if necessary. Next, this is subjected to cold working at a processing rate of 50% or more by a method such as cold rolling to obtain the desired shape, for example, a thickness of 0. Make a thin plate of I n+m. Next, an annular plate having an outer diameter of 45 mm and an inner diameter of 33 mm, for example, is punched out from the thin plate, and this is held in hydrogen or other suitable non-oxidizing atmosphere (hydrogen, argon, nitrogen, etc.) or in vacuum at a temperature of 900°C or higher and lower than the melting point. Heating for an appropriate time at
From the above temperature, cool at an appropriate rate corresponding to the composition of 100°C/sec to 1°C/hour, or further regulate this.
The mixture is reheated at a temperature below the irregular lattice transformation point (approximately 600° C.) for a suitable period of time, and then cooled. In this way, the effective permeability is 300
0 or more, has a saturation magnetic flux density of 40,000 or more, and (1
10) A wear-resistant high permeability alloy having a recrystallized texture of <112>+ (311) <112> is obtained.

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

Figure 1 shows an 80%Ni-Fe3%Nb-P-3 alloy (P:5=10:1) cold-rolled at a processing rate of 90%, heated at 1100°C, and then heated at 1000°C/hour. This figure shows the relationship between the recrystallized texture and crystal properties and P and sl when cooling at a high speed.

When Ni-Fe-Nb alloy is cold rolled (110
) <112>+ (112) A recrystallized texture of <111> occurs, but when this is heated at high temperature, it becomes (100)
<001> and HIO) <112>+ (311) <
112> recrystallized texture is generated. However, when P and S are added to this, the formation of (100) <001> recrystallized aggregate fibers is suppressed, and 1tlo) <112>+
(311) <112> recrystallization texture develops,
At the same time, the amount of wear decreases. Further, the effective magnetic permeability increases by adding P and S, but if P and S exceed 1%, forging becomes difficult, which is not preferable. Figure 2 is 8
0%Ni-Fe-5%Nb-0,05%P-0,01%
This figure shows the relationship between the recrystallized texture and core properties and cold working rate when S alloy is heated at 1100°C, and the increase in cold working rate is (110) <112>+ (
3111<112> resulting in the development of recrystallized texture, improving wear resistance and increasing effective magnetic permeability.

Figure 3 shows 80%Ni-Fe-5%Nb-0.05%P-
This figure shows the relationship between the heating temperature after rolling a 0.01% S alloy at a cold working rate of 85%, the recrystallized Mi texture, and the properties of the metal. As the heating temperature increases, (112) < 11
1> component decreases, (110) <112>+ (31
1) <112> develops, improving wear resistance and increasing effective magnetic permeability. Figure 4 shows alloy number 7 (81.5%
Ni-Fe-2%Nb-0,155%P-0,022%
S alloy), alloy number 45 (79,3%Ni-Fe-7
%Nb-0,04%P-0.008%S-2%Mo alloy), alloy number 37 (82%Ni-Fe-3,5%Nb
-0,062%P-0.01%S-5%V alloy), the relationship between effective magnetic permeability and cooling rate and the effective magnetic permeability (x mark) when this is further subjected to reheating treatment are shown. It is something. 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 5 is a characteristic diagram of the wear amount of the magnetic head when Cr, Mo, Ge, Au or Co is added to the 80%Ni-Fe3%Nb-0.05%P-〇,01%S alloy. When Cr, Mo, Ge, Au, or CO is added, the effective magnetic permeability increases and the amount of wear decreases, but when Cr, Mo, Ge, or Au exceeds 7%, the saturation magnetic flux density becomes less than 4000 G, which is not preferable. .

Further, if the Co content exceeds 10%, residual magnetism becomes large and magnetization noise increases, which is not preferable.

Figure 6 is the same <80%Ni-Fe-5%Nb-0,05
This is a characteristic diagram of the amount of wear and effective magnetic permeability of the magnetic head when V, W, Cu, Ta or Mn is added to the %P-0,01%S alloy. , the effective magnetic permeability increases and the amount of wear decreases in both cases, but ■ is 10% or more, W is 15% or more,
If Cu, Ta or Mn is added in an amount of 25% or more, the saturation magnetic flux density becomes 4000 C or less, which is not preferable.

Figure 7 shows the same <80%Nt-Fe-5%Nb-0,05
%P-0,01%S alloy with Al, Si, Ti, Zr
.

This is a characteristic diagram when Hf, Sn, Sb, Ga, In, or Tl is added. Af, Si, Ti, and Zr.

When Hf, Sn, Sb, Ga, In, or Tffi is added, the effective magnetic permeability increases and the amount of wear decreases, but Si, Ti, Zr, Hf, and Ga.

When In or Tffi is 5% or more, the saturation magnetic flux density is 40
00 G or less, Aj! , Sn or sb is 5%
If this is the case, forging becomes difficult, which is not preferable.

Zn, Cd, La, Pt, Be in 0.01% S alloy.

In the characteristic diagram when Ag, Sr, Ba or B is added, when Zn, Cd, La, Pt, Be, A4゜Sr, Ba or B is added, the effective magnetic permeability increases,
Although the amount of wear decreases, Zn.

Cd, La, PL 5% or more, Be, Sr, Ba 3%
If more than 3% is added, the saturation magnetic flux density becomes 4000 C or less, and if 3% or more of Ag or 1% or more of B is added, forging becomes difficult, which is not preferable.

Figure 8 is the same <80%Ni-Fe3%Nb-0.05%
F-0,01%S alloy with Zn, Cd, La, and PL.

Characteristic diagram when Be, Ag, Sr, Ba or B is added, Zn, Cd, L, a, PL, Be.

Adding Ag, Sr, Ba or B increases the effective magnetic permeability and reduces the amount of wear, but Zn, Cd,
If 5% or more of La or Pt or 3% or more of Be or 5rBa is added, the saturation magnetic flux density becomes 4000 G or less, and if 3% or more of Ag or 1% or more of B is added, forging becomes difficult, which is not preferable.

Figure 9 shows 80%Ni-Fe3%Nb-0.05%P-0
, 01% S alloy manufactured according to Example 1 is a diagram showing the relationship between hot rolling temperature, recrystallization texture, and wear amount. 80%Nt-Fe-5%Nb-0,0
A 5% po, oi% S alloy was forged at approximately 1000'cT to form a plate with a thickness of 7 mm. Furthermore, it was hot rolled to a thickness of 1.0 mm at various heating temperatures, and then cold rolled at room temperature to form a 0.1 mm thin plate (cold working rate 90%).
). Figure 9 shows the relationship between hot rolling temperature, recrystallization texture, and wear amount when this thin plate was heated in hydrogen at 1100°C for 2 hours and then cooled to room temperature at a rate of 800°C/hr. . When the hot rolling temperature is below 900°C, severe wear occurs due to residual (112) <111>, but at temperatures between 900°C and 1000°C, (111)
The recrystallized texture of 101<112> and (311/)<112> develops, and the amount of wear becomes particularly small.

In the present invention, cold working is (110) <112>-
+-+112) <111> is formed, and based on this, (110) <112>+ (31L) <
112> is necessary to develop a recrystallized Mn texture, and as shown in Figs. 1 and 2, cold working at a processing rate of 50% or more is necessary when the total amount of P and S is 0.001% or more. fllo) <112>++3
11) The development of recrystallized texture of <112> is remarkable,
Its wear resistance is significantly improved and its effective magnetic permeability is also high. Furthermore, the heating performed after the above-mentioned cold working not only homogenizes the structure but also removes processing distortion.

It is necessary to develop a recrystallized texture of (110) <112> + (311) <112> and obtain high effective permeability and excellent wear resistance, but as shown in Figure 3, Effective magnetic permeability and wear resistance are significantly improved by heating to 900° C. or higher.

Incidentally, repeating the above-mentioned hot rolling at a temperature of 900°C or higher and 1000°C or lower, cold working, and subsequent heating at a temperature of 900°C or higher and lower than the melting point is (110) <112>+ (3H) It is effective for increasing the degree of accumulation of recrystallized texture of <112> and improving wear resistance.Even if it is less than 50%, it is +110) <112
〉+{311) A recrystallized texture of <112> is obtained, which is included in the technical idea of the present invention. Therefore, the cold working rate of the present invention means the total working rate of cold working in all manufacturing processes, and does not mean only the final cold working rate.

When cooling from a temperature above 900°C below the melting point to a temperature above the regular-irregular lattice transformation point (approximately 600°C), there is not much difference in the magnetic properties obtained whether the cooling is rapid or gradual. As seen in FIG. 4, the cooling rate below this transformation point has a large effect on magnetism.

In other words, from the temperature above this transformation point to 100℃/sec ~ BiC
By cooling to room temperature at an appropriate rate corresponding to the composition of 1/2 hour, the degree of regularity of the ground can be appropriately adjusted and excellent magnetism can be obtained. When cooling at a rate close to 100°C/sec among the above cooling rates, the degree of order decreases; if the cooling rate is any faster, order does not progress, and the degree of order decreases even further (and the magnetism deteriorates. However, the degree of order decreases. When an alloy with a low degree of order is reheated and cooled for 1 minute or more and 100 hours or less depending on the composition at 200° C. to 600° C. below its transformation point, the ordering progresses to a suitable degree of order and the magnetism improves.

On the other hand, if the material is slowly cooled from a temperature above the above-mentioned transformation point at a rate of 1° C./hour, for example, ordering will proceed too much and the magnetism will decrease.

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.

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

Implementation burning Alloy number 45 (composition N1 = 79.3%, Nb = 7%.

P = 0.04%, S = 0.008%, Mo = 2%
, 99.8% pure electrolytic nickel, 99.9%
An iron-phosphorus master alloy containing pure electrolytic iron, 99.8% pure niobium, 99.5% pure sulfur, molybdenum, and 10% phosphorus was used. To prepare the sample, 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, this was poured into a mold with holes of 25 mm in diameter and 1,701 mm in height, and the resulting ingot was approximately io.

It was forged at ℃ to form a plate with a thickness of about 7 mm. Approximately 900 more
It was hot rolled to a suitable thickness between ℃ and 1ooo'c, and then cold rolled at room temperature at various processing rates to a thickness of 0.1 m.
A circular plate having an outer diameter of 45 mm and an inner diameter of 33 mm was punched out from the thin plate.

Next, various heat treatments are applied to this material to improve its magnetic properties and when used as the core of a magnetic head, the humidity is 80% and the temperature is 40%.
The amount of abrasion after 200 hours using Cry and magnetic tape at ℃ was measured using a Talysurf surface roughness meter, and the characteristics shown in Table 1 were obtained.

The characteristics of typical alloys are shown in Table 2.

As mentioned above, the alloy of the present invention is easy to process, has excellent wear resistance, and has a saturation magnetic flux density of 40,000 or more, a high effective magnetic permeability of 3,000 or more, and a low coercive force. It is suitable not only as a magnetic alloy for cases, but also 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 60 to 90% Ni, N
b 0.5-14%, total of P and S 0.001-1
% (30.1% or less, P and S do not include 0%) and the balance is Fe, and the elements added as subcomponents are Cr, Mo, Ge, Au 7% or less, Co, V
10% or less, W 15% or less, Cu.

Ta, Mn 25% or less, Af, Si, Ti, Zr
.

Hf, Sn, Sb, Ga, In, Tl, Zn.

Cd, rare earth elements, platinum group elements at 5% or less, Be.

The reason why Ag, Sr, Ba was limited to 3% or less, and B was limited to 1% or less, the total of 0.01 to 30% of one or more types, is clear from each example, Table 2, and the drawings. , the effective magnetic permeability in this composition range is 3000 or more, and the saturation magnetic flux density is 40
000 or more and has a recrystallized texture of (110) <112> + (311) <112>, and has excellent wear resistance. However, if the composition falls outside this composition range, magnetic properties or wear resistance deteriorate. Because it does.

That is, when Nb is 0.5% or less and the total of P and S is 0.001% or less, (110) <112>+ (3
11) The recrystallized texture of <112> is not sufficiently developed, resulting in poor wear resistance.
If the total of 1% or more and 30.1% or more, forging becomes difficult, and the effective magnetic permeability becomes 3000 or less and the saturation magnetic flux density becomes 4000G or less.

And the composition range of Ni 60-90%, Nb 0.5-14%, P and S total 0.001-1% (however, so, i% or less, P and S do not include 0%), and the balance Fe The alloy has an effective magnetic permeability of 3000 or more and a saturation magnetic flux density of 4.
0000 or more, it has excellent wear resistance and good workability, but generally it is further supplemented with Cr.

Mo, Ge, Au, W, V, Cu, Ta, Mn.

Al, Zr, Si, Tt, Hf, Ga, In.

Tl, Zn, Cd, rare earth elements, platinum group elements.

Adding Be, Ag, Sr, Ba, B, etc. has the effect of particularly increasing the effective magnetic permeability, adding Co has the effect of particularly increasing the saturation magnetic flux density, and adding Co has the effect of particularly increasing the saturation magnetic flux density.

Mn, Ti, Co, rare earth elements, Be, Sr.

Adding Ba and B has the effect of improving forging and processing, and AI! ,,Sn,Sb,Au,Ag,Ti.

The addition of Zn, Cd, Be, Ta, and V and the phosphide and sulfide of each element as a subcomponent are (110) <112>+
+311) It has the effect of developing a <112> recrystallized texture and improving wear resistance.

(Effect of the invention) In short, the alloy of the present invention can be easily forged, and (1101<
112>+ +311) By forming a recrystallized texture of <112>, it has excellent wear resistance, has a saturation magnetic flux density of 40,000 or more, and has a high effective permeability, so it is suitable as a magnetic alloy for magnetic recording/reproducing heads. In addition, it is suitable as a magnetic material for general electromagnetic equipment that requires wear resistance and high magnetic permeability.

[Brief explanation of the drawing]

Figure 1 is a characteristic diagram showing the relationship between the properties of the 80%Ni-Fe-5%Nb-P-3 alloy and P and Sl (where P:5=lO:l). %Nt-Fe-5%Nb 0.05%P
=Characteristic diagram showing the relationship between the properties of the 0.01% S alloy and the cold working rate, Figure 3: 80%Ni-Fe-5%Nb-0.05%P-
Figure 4 is a characteristic diagram showing the relationship between the initial properties and heating temperature of the o,oi%S alloy.
%P-0,022%S alloy (alloy number 7'), 79
゜3%Ni-Fe-7%Nb-0.04%P-0.00
8%S-2%M. Alloy (45), and 82%Ni-Fe 3.5%
Nb-0,062%P-0.01%S-5% ■Alloy (3
7) Characteristic diagram showing the relationship between effective magnetic permeability, cooling rate, reheating temperature and reheating time, Figure 5 is 80%Ni-Fe-5%Nb-0,05%P-
0.01% S alloy with Cr, Mo, Ge, Au or C
Figure 6 is a characteristic diagram showing the relationship between the initial characteristics and the amount of each element added when O is added. , a characteristic diagram showing the relationship between the characteristics and the amount of each element added when Cu, Ta or Mn is added.
〇, 01% S alloy with AI, Si, Ti, Zr, Hf
. A characteristic diagram showing the relationship between the characteristics and the amount of each element added when Sn, Sb, Ga, In or Ti is added.
〇, 01% S alloy with Zn, Cd, La, Pt, Be. FIG. 2 is a characteristic diagram showing the relationship between the initial characteristics and the amount of each element added when Ag, Sr, Ba, or B is added. Figure 9 shows 80%Ni-Fe3%Nb-0.05%P0.
FIG. 2 is a characteristic diagram showing the relationship between hot rolling temperature, recrystallization texture, and wear amount of 01% S alloy. Figure 2; Rei9 Qf, Roe Pei'p t5) Figure 1 P15 (%n(1'+52f(J) Figure 3 nO section Uryu (℃) Figure 4; A (℃/direction) Fig. 5 Cr, No, θe, Co or Au (%) Fig. 7 jA ffLt force Loe temperature (°C) Fig. 8 zn, Cd, La, Pt, Be (%) Al, 5r , Ba, B (%) Report December 1989

Claims (1)

[Claims] 1. Ni 60-90%, Nb 0.5-14% by weight
, P and S total 0.001-1% (however, 50.1
% or less, P and S do not include 0%) and the balance is Fe as the main component, Cr, Mo, Ge, Au as subcomponents are each 7% or less, Co, V
10% or less each, W 15% or less, Cu, Ta,
Mn is 25% or less, Al, Si, Ti, Zr,
Hf, Sn, Sb, Ga, In, Ti, Zn, Cd, rare earth elements, platinum group elements each at 5% or less, Be, Ag
, an alloy consisting of 3% or less each of Sr and Ba, and 1% or less of B, a total of 0.01 to 30% of one or more types, and a small amount of impurities, is heated at a temperature of more than 900°C and less than 1000°C. After being cold worked, it is cooled, and then cold worked at a working rate of 50% or more, and then heated at a temperature of 900°C or more and below the melting point,
Then, from the temperature above the regular-irregular lattice transformation point to 100°C
By cooling to room temperature at an appropriate rate corresponding to the composition of
00 or more, saturation magnetic flux density 4000G or more, and {11
A method for producing a wear-resistant high magnetic permeability alloy, characterized by forming a recrystallized texture of 0}<112>+{311}<112>. 2.Ni60-90%, Nb0.5-14% by weight
, P and S total 0.001-1% (however, 50.1
% or less, P and S do not include 0%) and the balance is Fe as the main component, Cr, Mo, Ge, Au as subcomponents are each 7% or less, Co, V
10% or less each, W 15% or less, Cu, Ta,
Mn is 25% or less, Al, Si, Ti, Zr,
Hf, Sn, Sb, Ca, In, Tl, Zn, Cd, rare earth elements, platinum group elements each at 5% or less, Be, Ag
, an alloy consisting of 3% or less each of Sr and Ba, and 1% or less of B, a total of 0.01 to 30% of one or more types, and a small amount of impurities, is heated at a temperature of more than 900°C and less than 1000°C. After being worked, it is cooled, and then cold worked at a working rate of 50% or more, and then heated at a temperature of 900°C or more and below the melting point,
Then, from the temperature above the regular-irregular lattice transformation point to 100°C
Cool at an appropriate rate corresponding to the composition/second to 1°C/hour,
By further heating this at a temperature below the regular-disorder lattice transformation point for an appropriate time corresponding to the composition for 1 minute to 100 hours and cooling, the effective magnetic permeability at 1 KHz is 30.
00 or more, saturation magnetic flux density 4000G or more, and {11
A method for producing a wear-resistant high magnetic permeability alloy, characterized by forming a recrystallized texture of 0}<112>+{311}<112>.