JPH03122236A - Ni-fe serite high permeability magnetic alloy - Google Patents

Abstract

PURPOSE:To improve the DC-AC magnetic characteristics in the magnetic alloy and to improve its shielding capacity by specifying the amounts of Si, Ni, Mo, Mn, Fe and B to be added under the optimum regulation of inevitable impurities and regulating the componental balance of each amt. into a specified range. CONSTITUTION:The magnetic alloy contains, by weight, 77.5 to 79.5% Ni, 3.8 to 4.6% Mo, 1.8 to 2.5% Cu, 0.1 to 1.10% Mn, 0.010 to 0.080% P, <0.20% or 0.2 to 1.0% Si, <=0.0020% S, <=0.0030% O, <=0.0010% N and <=0.020% C, furthermore contains B in the range of the inequality I and the balance Fe and contains Ni, Mo, Cu, Mn and Fe in the range satisfying the inequality II. In the inequalities, the ones in [ ] are expressed by wt.%. B is essential for improving the magnetic permeability, and when [B] and [N] lie in the above range, high magnetic permeability can be obtd. P and Si improve the AC magnetic characteristics without deteriorating the DC magnetic characteristics; in either case, the DC magnetic characteristics are deteriorated at the time of more than the upper limit, and the amt. of Si is preferably regulated to <0.20% for the application requiring relatively high magnetic flux density.

Description

DETAILED DESCRIPTION OF THE INVENTION Object of the Invention (Industrial Field of Application) The present invention relates to a Ni-Fe based high permeability magnetic alloy, and the present invention relates to a Ni-Fe based high permeability magnetic alloy, which improves the magnetic properties thereof, and achieves especially excellent direct current magnetic properties and outstanding The present invention relates to a magnetic alloy that has excellent AC magnetic properties, minimizes deterioration of magnetic permeability due to distortion, and has good hot workability.

(Prior Art) Nt-Fe based magnetic alloys equivalent to JIS PC are magnetic materials that are currently used in an extremely wide range of applications such as magnetic head cases, various cores, metamorphic cores, and various magnetic shielding materials. In other words, such PC permalloy is characterized by high magnetic permeability and low coercive force, and those in practical use today are 80%Ni-5%Mo-Fe (supermalloy) and 77%Ni5. %Cu-4%Mo-Fe (M
In terms of direct current characteristics, the level of magnetic permeability normally obtained with these alloys is 150,000 for the initial magnetic permeability (hereinafter referred to as μi) and 300 for the maximum magnetic permeability (hereinafter referred to as μm). It is about .000.

In terms of AC characteristics, for example, the inductance permeability μL at a plate thickness of 0.2 mm is about 10,000.

However, with the recent development of electronics, various devices have become smaller and more sophisticated, and there is a desire for further improvements in the properties of magnetic alloys as described above. In other words, in response to such demands, Japanese Patent Laid-Open No. 62-2.27053 and Japanese Patent Laid-Open No. 62-1989 have improved the DC magnetic properties of magnetic alloys with the above-mentioned composition system by reducing impurity elements and adding Cr.
2-227054 has been announced.

Furthermore, in JP-A No. 63-149361, it was announced that B was added to the alloy of the above composition system to improve hot workability during manufacturing, and the DC magnetic properties were improved by removing B during magnetic annealing. There is.

On the other hand, the above component system contains about 80 wt% Ni and is expensive, so we fundamentally reviewed the component system, reduced the Ni content, and added CLIsMn, which is cheaper than Ni, to achieve high initial magnetic permeability. Japanese Patent Publication No. 62-13420, and furthermore, in addition to the technology of this Japanese Patent Publication No. 62-13420, Japanese Patent Application Laid-Open No. 63-247336 and Japanese Patent Application Publication No. 1989-1980 added an appropriate amount of AI to reduce oxide inclusions and improve DC magnetic properties. 63-2
47339 technology has also been developed. In particular, the Ni content of the alloys proposed in JP-A-63-247336 and JP-A-63-247339 is as high as 426,000.

Furthermore, in addition to the above-mentioned demand for improved magnetic properties, there is also a recent demand for manufacturing with the required properties at a lower cost, and from this point of view, Japanese Patent Application Laid-Open No. 1-100232
techniques have also been proposed. In other words, this technology adds 1 to 4 wt% of Si to ordinary Mo-su-malloy and sets the magnetic annealing temperature to a relatively low temperature of 1030°C or less.
It is characterized by obtaining sufficiently satisfactory magnetic permeability and magnetic shielding properties at 50 Hz.

(Problem to be solved by the invention) The above-mentioned Japanese Patent Application Laid-open No. 62-227053 and No. 22705
Even with impurity reduction and Cr addition, which are featured in 4, the DC magnetic properties after the final heat treatment in a hydrogen atmosphere (1100'CX for 3 hours) are at most 100,000 for Ni, for example, and higher magnetic properties are required. It cannot help but be unsuitable for such uses.

In addition, in the proposal of JP-A-62-227054, ordinary Ni
- Since Cr is newly added to the Fe-Mo or Ni-Fe-Mo-Cu components, the cost is high. On the other hand, in the proposal of JP-A-62-227053, in addition to the high cost due to the addition of Cr, the Mn content is increased above the normal level (1
．． 2 to 10 wt%), there is also a manufacturing problem in that hot workability becomes extremely poor.

In both of the above two proposals, B is added, but in this case the B addition is to improve hot workability and punching properties, and the addition of B is the only addition intended in these proposals. No clear improvement in magnetic properties was observed, and on the contrary, some cases of deterioration were observed.

Furthermore, in JP-A-62-149361, magnetic properties were removed from B.
Although it can be improved by treatment, the DC magnetic properties obtained after this treatment are at most 75.000 μi, which is the same level as that obtained with ordinary Ni-Fe-Mo-Cu alloys. Therefore, this technique is unsuitable for applications requiring higher magnetic properties.

In addition, the above-mentioned Japanese Patent Application Laid-open No. 62-227053 and No. 227053
7054 and JP-A No. 63-149361, improvements in AC magnetic properties have not yet been achieved in common.

On the other hand, JP 62-13420, JP 63-24733
6 and 247339 can provide permalloy with high direct current magnetic properties, but they have a manufacturing problem in that hot workability during manufacturing is inherently low due to increased Mn and Cu content. There is. Also, the saturation magnetic flux density of the alloy obtained by this proposal is, for example, B+o (magnetic flux density at '10 Oersteds) at most 500 Gauss, which is B in supermalloy and Has Cu permalloy. This is low compared to the 7,000-8,000 gas.

This means that this alloy is supermalloy or MO% C1
This means that the magnetic flux within the material is saturated with an external magnetic field that is lower than that of permalloy, and when used as a shielding material, it is unsuitable for use in places where the external magnetic field is relatively high. Furthermore, the AC magnetic properties of this alloy are lower than those of supermalloy and MO%Cu permalloy.

In the technique disclosed in Japanese Patent Application Laid-Open No. 1-100232, the shielding performance at 50 Hz is at the required level, but the shielding performance at direct current is rather poor.

"Structure of the Invention" (Means for Solving the Problems) The present invention was created after repeated studies to solve the problems in the conventional technology as described above, and has good hot workability. It has both particularly excellent AC magnetic properties and excellent DC magnetic properties, and minimizes deterioration due to distortion of magnetic permeability.Furthermore, in order to obtain the required magnetic properties at the same level as conventional methods, it is possible to reduce the magnetic annealing temperature. 100 more than before
This made it possible to lower the temperature by as much as ℃.The influence of major components such as Ni and MO%C11%Fe on magnetic properties was further investigated, and the relationship between the properties and components obtained was investigated for the B-added system. As a result of extensive experiments and research, the present invention was completed. That is, the present invention is as follows.

(11Ni: 77.5-79.5wt%, Mo
: 0.0020 wt%, Cu: 1.8-2.
5 wt%, Mn: 0.1”1.10evt
%P: 0.010"0.080 wt%, Si
: Less than 0.20wt%, S: 0.0020wt%
Below, O: 0.0030prt% or less, N:
0.0010wt% or less, and B 0.020
wt% or less, B is contained within a range of 4, the remainder is basically Fe, and Nis MO% Cus Mn5Fe is contained within a range that satisfies (however, t% is in brackets). N characterized by being
i-Fe based high permeability magnetic alloy.

(21Ni: T'r, 5-79.5ht%, M
o: 0.0020 wt%, Cu: 1.8-2
．． 5 wL%, lLn: 0.0030wt%,
P: 0.010 = 0.080 ut%, St:
0.2-1.0 wt%, S: 0.0020wt
% or less, O: 0.0030wt% or less, N:
0.0010wt% or less, and B 0.020
wt% or less, B is contained within a range of 4, the remainder is basically Fe, and Nis MO% CLI, MIDXFe are within a range that satisfies (however, the values in brackets are wt%). A Ni-Fe based high permeability magnetic alloy characterized by containing:

(3) Having the component composition described in the previous item (item 11), and having BI at the austenite grain boundary and its vicinity after magnetic annealing.
is 10 to 5 Qatm%.
Fe-based high permeability magnetic alloy.

(4) Ni-F having the component composition described in the preceding item (2), and characterized in that the amount of B at the austenite grain boundary and its vicinity after magnetic annealing is 10 to 50 atm%.
E-based high permeability magnetic alloy.

(Function) The device according to the present invention, under proper control of impurity elements,
As a level that makes hot workability good, Sis N
is MO% Cus Mns By optimizing the amounts of Fe and B added and controlling the component balance of capacity within a specific range, we have achieved excellent direct current that has not been seen in conventional MO%Co permalloys and supermalloys of the same type. It has both magnetic properties and excellent alternating current magnetic properties, and furthermore, it is possible to lower the magnetic annealing temperature by about 100° C. compared to the conventional method while obtaining the same level of required magnetic properties as the conventional method.

That is, first, the improvement in magnetic properties intended in the present invention is achieved by controlling the level of impurities in the alloy.
The reason for the limit on N and C is as follows in wt% (hereinafter simply referred to as %).

S is harmful to hot workability, inhibits grain growth during final hydrogen annealing through the formation of sulfides, and has a negative effect on magnetic properties because the grain size after annealing becomes small and magnetic permeability does not improve. It is an extremely harmful element. If this amount of B exceeds 0.0020%, the following N
is Mo,, even if we tried to optimize Cus Fe5Bii, we could not improve the magnetic properties as aimed at in the present invention,
Further, since hot workability is significantly deteriorated, it is necessary to set the upper limit to 0.0020%. Note that in order to further improve the magnetic permeability in direct current and alternating current, it is more desirable that the content be 0.0005% or less.

0 exists as oxide-based inclusions in the alloy targeted by the present invention, and if the amount is large, it will inhibit grain growth during the final hydrogen annealing, and the grain size after annealing will be small, resulting in a decrease in magnetic permeability. Since it does not improve magnetic properties, it is an extremely harmful element to magnetic properties. That is, if this amount of O exceeds 0.0030%, even if the amount of Nis MO% Cus Fe5B is optimized as described above, the magnetic properties cannot be improved as intended by the present invention.
．． The upper limit was set at 0.0030%. Note that in order to further improve the magnetic permeability in direct current and alternating current, the content is more preferably 0.0005% or less.

In an alloy based on B addition, N easily combines with B to form BN, resulting in a decrease in the effective amount of B. Furthermore, since the magnetic properties are significantly deteriorated by the formed BN, if it is contained in a large amount in the alloy, it will have an adverse effect. In other words, if this N exceeds 0.0010%, the deterioration of magnetic properties will be significant for the reasons mentioned above.
The upper limit was %.

In addition, in order to further improve the magnetic permeability in AC, o, oo
More preferably, it is os% or less.

C exists as an interstitial element in the target alloy of the present invention, and if its amount is large, the magnetic permeability decreases, so it is a harmful element to magnetic properties, and if it exceeds 0.020%, this element For some reason, the deterioration of magnetic properties becomes significant, so 0.0
The upper limit was set at 20%.

Now, in the present invention, the purpose of the present invention is achieved by optimizing the amounts of Nis Mo, Cu, Fe, and B added under the control of impurity elements as described above, and by keeping the component balance of capacity within a specific range. The details are as follows.

When Ni is in the range of 77.5 to 79.5%, high magnetic properties and high shielding properties as intended by the present invention can be obtained. If this Ni content is less than 77.5% or more than 79.5%, magnetic permeability will decrease in either case.
The lower limit was 5% and the upper limit was 79.5%.

When Mo is within the range of 0.0020%, the high magnetic properties and high shielding properties targeted by the present invention can be achieved. That is, if Mo is less than 3.8% or more than 4.6%, magnetic permeability cannot be improved, so it is necessary to set it to 0.0020%.

In alloys in which Ni, Mo, and other components are within the specified ranges of the present invention, Cu, in the coexistence of B (described later), dramatically improves the DC magnetic properties and increases the effective magnetic permeability of AC. It also has the effect of improving the squareness (Br/8m) at AC (5' OHz).

This effect of Cu is 77.5 to 79.5% of Ni.
, Mo: Appears when the content is 0.0020%, and the optimum amount of Cu is 1.8 to 2.5%. Note that Cu is 1.8%
If the content of Cu is less than 2.5%, the properties cannot be improved, and if the content exceeds 2.5%, the properties deteriorate, so the range of Cu is set at 1.8 to 2.5%.

Like MOXCu mentioned above, Mn is an element that affects the magnetism of the alloy subject to the present invention, and when this Mn is 1.10%
Although the high magnetic permeability targeted by the present invention can be achieved with the following,
If it exceeds 1.10%, such improvement in magnetic permeability will not be achieved, so 1.10% is set as the upper limit. On the other hand, Mn is 0.10%
If it is less than 0.1, hot workability deteriorates and is not preferable.
The lower limit was 0%.

([B] and (N) are the amounts of B and N added in the alloy, respectively, %
) is in the range of o,oos to 0.0070%, the object of the present invention can be effectively achieved, but if it is less than 0.0005%, the magnetic permeability will not improve, while if it exceeds 0.0070%, the magnetic permeability will be low. Therefore, the values were set to 0.0005% and 0.0070%.

P is an element that can improve alternating current magnetic properties, that is, effective magnetic permeability in alternating current and squareness in a low frequency range, without deteriorating direct current magnetic properties within the specified range of the present invention. . P is also an element that, when added in an appropriate amount, makes it possible to reduce the deterioration of direct current and alternating current magnetic permeability due to distortion.

The amount of P that improves the AC magnetic properties as described above without deteriorating the DC magnetic properties is 0.010 to 0.080%.
is within the range of If P is less than o, oio%, the AC magnetic properties intended in the present invention cannot be improved;
If it exceeds 0.010%, the DC magnetic properties will deteriorate.
% and 0.080% were the lower and upper limits, respectively. The amount of P added is preferably 0.020% or more in order to reduce the deterioration of magnetic permeability due to distortion, which is the objective of the present invention.

St is an element that further improves alternating current magnetic properties, that is, effective magnetic permeability in alternating current, without deteriorating direct current magnetic properties in the alloy of the present invention whose components are within the specified range. Furthermore, St is an element that makes it possible to further reduce deterioration of direct current and alternating current magnetic permeability due to distortion under a specific addition amount. However, since the saturation magnetic flux density of this St decreases with the amount added, it is preferable to keep it at 0.20 wt % or less in applications where a relatively high magnetic flux density is required. That is, when St is 0.20wt% or less, 100OA/m
The magnetic flux density within the material (hereinafter abbreviated as B+ooo) when external magnetization is applied has a value of 7700 Gauss or more. The amount of Si that further improves the AC magnetic properties as described above without deteriorating the DC magnetic properties is 0.2.
It is in the range of 0 to 1.0 θ%. In other words, Si is 0.20%
If it is less than 1.00%, it will not be possible to improve the alternating current magnetic properties, which is the objective of the present invention, and if it exceeds 1.00%, the direct current magnetic properties will deteriorate, so it is set at 0.20 to 1.00%. The amount of Si added to reduce the deterioration of magnetic permeability due to distortion as intended in the present invention is preferably 0.30% or more.

In order to improve the magnetic properties aimed at in the present invention, the above-mentioned S
, OlN, CXN15M0. CLI% Mn, B
By adjusting the amount and adding appropriate amounts of St and P, N1%
MO% CIJ% Parameter 1 that defines the component balance of B and Fe is within the range of 0.0005 to 0.0070%, the initial permeability of direct current after magnetic annealing, the degree of magnetic shielding against a direct current magnetic field of 500 milligauss, Effective permeability at IKHz, 50H
Direct current and alternating current magnetic properties such as squareness in z can be dramatically improved.

That is, according to the above-mentioned component regulations and component balance regulations, as shown in the example work described later, the initial magnetic permeability μi is 300.000 or more, the magnetic shielding degree against a 500 milligauss DC magnetic field is 250 or more, and the plate thickness is 0. Effective magnetic permeability at IKHz at .20 tm is 15.000 or more, 50
The squareness at Hz can be 0.90 or more.

In order to further improve the magnetic properties of the alloy of the present invention, it is necessary to increase the initial magnetic permeability by increasing the amount of B in the austenite grain boundaries and their vicinity after heat treatment to increase final magnetism within the range of 10 to 50 atm%. It can have high magnetic shielding, relatively high effective magnetic permeability, and relatively high squareness.

That is, by using the alloy of the present invention, if Bq at the austenite grain boundary and its vicinity after magnetic annealing is within the above range, it is possible to provide magnetic properties that are even more excellent than those of Example 1, which will be described later. In other words, as shown in Example 2, which will be described later, the initial magnetic permeability μi is 400.000 or more, the magnetic shielding degree against a 500 milligauss DC magnetic field is 350 or more, and the plate thickness is 0.2.
The effective permeability at IKHz at 0■■ is 17,000
As described above, the squareness at 5011z can be set to 0.93 or more.

Note that the Ni-Fe alloy targeted by the present invention has poor hot workability. As a method of improving this processability, a combination of adding a small amount of B and a small amount of Ca is often used, but even if such addition of 1lca is performed, as long as the above-mentioned requirements of the present invention are satisfied. The improvement in initial magnetic permeability that is the objective of the present invention is achieved. Further, in the present invention, in addition to the above-mentioned composition, 8L, which is inevitably included in iron alloys, will not be mentioned in detail, but for example, 8β: within a range of 0.03% or less. Containment is allowed.

The cause of this improvement in magnetic properties is not clear, but the presence of an appropriate amount of B at and near grain boundaries changes the properties of the grain boundary area, and this change improves magnetic properties, especially the movement of domain walls such as initial permeability. It is inferred that the ease of rotational magnetization or the ease of rotational magnetization has a positive influence on the required characteristic values.

Specific embodiments according to the present invention will be described below.

Example 1 High Ni-Fe having chemical components as shown in Table 1 below
The alloys of the present invention and comparative alloys were melted by vacuum melting, and then hot worked and descaled to prepare cold rolled materials. These materials are then cold rolled and annealed to a 0.
5 A thin plate sample of a crane was used, and a JIS ring with an outer diameter of 45 mm and an inner diameter of 33 mm was punched out from these samples.

Each sample in Table 1 above was heat-treated at 1100°C for 3 hours in an atmosphere of purified high-purity hydrogen by permeating it through a palladium membrane.
It was measured by cooling at 400'C/hr between ℃ and 650℃, then furnace cooling, and the results of μi being determined as permeability 4ff at 0.005 oersted, degree of shielding, effective magnetic permeability, and 50Hz. The results of squareness, coercive force, magnetic flux density, and initial magnetic permeability when surface pressure is applied are as shown in Table 2 below.

The degree of shielding is obtained by processing a material with a thickness of 0.5 am that has gone through the same manufacturing history as above into a cylinder with a diameter of 50mm and a length of 200mm.
Using a sample heat-treated under the same magnetic annealing conditions as above, an external magnetic field (Ho) of 500
It was determined by measuring the internal magnetic field H1 at the center inside the cylinder when a milliGauss force is applied in a direction perpendicular to the axial direction of the cylinder. The degree of shielding (=HO/H1) was measured in a box that was magnetically shielded to a level where the influence of geomagnetism could be sufficiently ignored.

The effective magnetic permeability at IKHz was determined by measuring the inductance permeability at 5 millier steps using a ring sample with a thickness of 0.20 W that underwent the same magnetic annealing as above, and the squareness at 50 Hz was determined by the effective The residual magnetic flux density (Br) and the magnetic flux density (Bo, 1) at a magnetic field of 0.1 oersted using the same ring sample in which the magnetic permeability was measured.
It was calculated from the ratio of

Note that the magnetic flux density and coercive force were measured using the same ring sample as the one used to determine the initial magnetic permeability. Magnetic flux density 13to. . is the magnetic flux density when an external magnetic field of 100 OA/m is applied, and the coercive force is the strength of the magnetic field when an external magnetic field of 100 OA/m is applied, then reversed, and the magnetic flux density becomes 0.

The initial magnetic permeability when surface pressure is applied is measured by applying a uniform load (surface pressure 4 kg 171.z) perpendicular to the plate surface of the ring sample using the sample whose initial magnetic permeability was measured above It was determined by

That is, each village of alloy floor 1 and floor 2 according to the present invention has C%
3% 0% N% BXP, Nis Mo, Cu and M
The amount of n is within the range of the components of the present invention, especially Nll, Na2
These alloys correspond to the first and second inventions of the present invention, respectively, but Ni has a Ni content of 300.000 or more, a shielding degree of about 250 or more, and an effective magnetic permeability (hereinafter abbreviated as μe).
is also 15,000 or more, 501 (squareness at z (hereinafter Br
/am) is also 0.90 or more, showing superior magnetic properties compared to comparative alloys. Furthermore, in case No. 2, St was added within the range specified by the present invention, and μe shows an even higher value than No. 1.

Also, Alloy Hikari 3 has CSS, 0. N, B, Nis M
O% CLI and Mn1l are within the range of the components of the present invention, and this is an alloy that falls under the claims of the present invention, and in which a trace amount of Ca has been added with the intention of improving hot workability. Also, the magnetic properties are at approximately the same level as the alloy PkLl and the second alloy mentioned above. That is, it was confirmed that the effects of the present invention can be sufficiently exhibited even in alloys to which a trace amount of Ca has been added in this manner.

Furthermore, in Alloy Optical 4 material, C, S, and OlN are reduced to more preferable levels, and μm1 shielding degree, μe, Br
/Bm is even higher than each village of No. 1 to No. 3. In addition, in these invention alloys of 1IkL1 to 4, the deterioration in initial magnetic permeability when a surface pressure of 4 kgf/■Tomi2 is applied is smaller than that of the comparative alloys 5 to N1121, which will be described later, and the deterioration of characteristics against strain is also small. is understood.

On the other hand, in each village of alloy floors 5 and 6, the Ni content exceeds the upper limit or is less than the lower limit, and
Each village of Alloy No. 7 and Ream 8 has Mol exceeding the upper limit or less than the lower limit, and Alloy No. 9 and No. 1
1 and 1.10 are those in which the amount of Cu exceeds the upper limit or is less than the lower limit, respectively. Further, the alloy layer 11 has a Mn content exceeding the upper limit, and the alloy layer 12 has a St content exceeding the upper limit, and the alloy layer 13 and! In the case of 1h14, the amount of B exceeds the upper limit or is less than the lower limit, and furthermore, each village of alloy blocks 15 to 19 has either C, P, S, O, or H as the original. For those exceeding the invention component range, and for alloys No. 20 and No. 21, the parameter X exceeds the upper limit specified by the present invention and is less than the lower limit, respectively. Both are at a lower level compared to the examples of the present invention.

That is, in the present invention, Nis MO% Cus Mn, B, with the reduction of impurity elements of C%P, S, O, and N.
By controlling the amount and balance of Fe within strictly defined ranges, excellent initial magnetic permeability, shielding degree, effective magnetic permeability, and squareness at 501 rz can be achieved for the first time. In order to obtain the required characteristics in the present invention, the gas used for heat treatment can be a high-purity H2 gas as shown in this example, but similar characteristics can be obtained using JIS
It can also be obtained by heat treatment in a normal H2 atmosphere as defined in 2006, that is, in a H2 gas stream with a dew point of -40°C or less.

Example 2゜The alloy of the present invention of Example 1 described above! Cold rolled about 1h4,
Outer diameter 4 from annealed thin plate sample of 0, 51111
A JIS ring with 5 cranes and an inner diameter of 33 cranes was produced by punching and used as a sample. A notched test piece that could be attached to an Auger observation stage was also cut from the same sample.

The samples obtained as described above were heat treated at 1100°C for 3 hours under various atmospheres as shown in Table 3 below, and cooled at different cooling rates between 1100°C and 650°C. The magnetic properties and degree of shielding were measured using the sample that was cooled in a furnace. In addition, the amount of B at austenite grain boundaries and their vicinity can be determined by adding electrolytic hydrogen by cathodic electrolysis to perform grain boundary embrittlement treatment after the above heat treatment, and performing grain boundary fracture in a vacuum. Component analysis of the surface was performed at 10 different points using Auger spectroscopy, and the results were averaged. These results are also shown in Table 4.

That is, in the case of using material 4 not specified in the present invention, sample material 11
In hl~4, the amount of B at the austenite grain boundary and its vicinity is within the specification of the present invention, μi, tW degree of shielding, μe, B
r/Bm is higher than that of sample material No. 6, in which the amount of B at and near the austenite grain boundaries is not specified by the present invention. Furthermore, in these test materials, the deterioration of the initial magnetic permeability when a surface pressure of 4 kgf/cnl is applied is smaller than that of the comparative alloy of Example 1, and it can be seen that the deterioration of characteristics due to strain is small.

In addition, in Table 3.4, the test material resistance 4 is 1100℃×
This is a case where the dew point of N2 is higher than 140° C. during the atmosphere maintenance for 3 hours, and the μi, degree of shielding, μe −, and Br78m of the sample heat-treated under such conditions are lower than those of other invention examples. That is, the effects of the present invention can be properly exhibited by performing heat treatment with N2 at a dew point of -40° C. or lower as defined by JIS.

Further, the effects of the present invention can also be exhibited by heat treatment under a high vacuum such as I x 10-'Torr.

Example 3゜4 outside the scope of the present invention in Example 1 and the following 5th example
Samples of comparative alloy No. 22 having the components shown in the table were prepared under the same manufacturing conditions as in Example 2, and each sample was heat-treated under the magnetic annealing conditions shown in Table 6 to improve magnetic properties and shielding. The measurement was carried out in the same manner as in Example 2. The results are shown in Table 7.

Note that in this comparative alloy 22, N1% CLI% P is outside the scope of the present invention, and the other components are within the scope of the present invention.

The properties obtained after magnetic annealing at 1000°C for 1 hour using the invention alloy No. 4 are as follows: using the comparative alloy N [N22,
The magnetic properties obtained after magnetic annealing at 100° C. for 1 hour, ie, μi, degree of shielding, μe, Br/Bm, μm, and Hc, are approximately the same level or slightly higher. That is, according to the present invention, it is possible to lower the magnetic annealing temperature by about 100° C. to obtain the same properties as the comparative alloy.

The present invention is not limited to the manufacturing method of the above-described embodiments, but also includes melting and refining, casting into a thin cast plate, as-cast or after hot working and/or descaling, cold rolling, annealing. It's okay.

Warm working may be performed instead of hot working or to improve the efficiency of cold rolling.

However, if surface quality, plate thickness shape, and dimensional accuracy are required, it is preferable to perform cold rolling before final melting.

Furthermore, instead of one cold rolling process, cold rolling process and recrystallization annealing (
For example, at 800° C. or higher), cold rolling may be repeated.

Even with the above manufacturing method, substantially equivalent products can be obtained as long as they are within the scope of the present invention.

"Effects of the Invention" According to the present invention as explained above, Ni-Fe
Appropriately improves the magnetic properties of the system's high permeability magnetic alloy, particularly magnetic properties such as magnetic permeability in the DC and low frequency range, shielding performance, and even AC permeability compared to conventional PC.
We provide high permeability magnetic alloys that are dramatically superior to permalloy, and are used in various magnetic shielding materials, magnetic head cases, cores, and even magnetic amplifiers and pulse transformers that require even higher shielding properties than conventional ones. It can be widely used in materials used in nonlinear applications such as, and it also makes it possible to lower the magnetic annealing temperature by about 100 degrees Celsius than before to obtain the same level of required characteristics as before, and the characteristics deteriorate due to strain. This is because it is small in size and can exhibit the required magnetic properties even when used as a structural member such as a shielded room, and can respond quickly and appropriately to the recent demands of the electronics industry. This invention has great industrial effects.

Procedural amendment (spontaneous) October 31, 1989

Claims (1)

[Claims] (1) Ni: 77.5 to 79.5 wt%, Mo: 3.8
~4.6wt%, Cu:1.8~2.5wt%, Mn:
0.1-1.10wt%P: 0.010-0.080w
t%, Si: less than 0.20wt%, S: 0.0020w
t% or less, O: 0.0030wt% or less, N: 0.00
Contains 10 wt% or less, C: 0.020 wt% or less,
and B is 0.0005wt%≦[B]−10.8/14[N]≦
The content is within the range of 0.0070 wt%, the balance basically consists of Fe, and Ni, Mo, Cu, Mn, and Fe are 3.2≦2.02×[Ni]−11.13×[Mo] −
1.25×[Cu]-5.03×[Mn]/2.13×
[Fe]≦3.8 (however, the values in brackets are wt%).
i-Fe based high permeability magnetic alloy. (2) Ni: 77.5 to 79.5 wt%, Mo: 3.8
~4.6wt%, Cu:1.8~2.5wt%, Mn:
0.1-1.10wt%, P: 0.010-0.080
wt%, Si: 0.2-1.0wt%, S: 0.002
0wt% or less, O: 0.0030wt% or less, N: 0.
0010wt% or less, C: 0.020wt% or less, and B: 0.0005wt%≦[B]-10.8/14[N]≦
The content is within the range of 0.0070 wt%, the remainder basically consists of Fe, and Ni, Mo, Cu, Mn, and Fe are 3.2≦2.02×[Ni]−11.13×[Mo] −
1.25×[Cu]-5.03×[Mn]/2.13[
A Ni-Fe based high permeability magnetic alloy, characterized in that each content is within a range that satisfies the following: Fe]≦3.82.13×[Fe] (wherein the values in brackets are wt%). (3) It has the component composition according to claim 1, and the amount of B at the austenite grain boundary and its vicinity after magnetic annealing is 1.
A Ni-Fe based high permeability magnetic alloy characterized by having a magnetic permeability of 0 to 50 atm%. (4) It has the component composition according to claim 2, and after magnetic annealing, the amount of B at the austenite grain boundary and its vicinity is 10
A Ni-Fe based high permeability magnetic alloy characterized by having a magnetic permeability of 50 atm%.