JPH03122237A - Ni-fe serite high permeability magnetic alloy - Google Patents

Abstract

PURPOSE:To improve the DC-AC magnetic chracteristics 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, 0.2 to 1.0% Si, <=0.010% P, <=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 is controlled since the hot workability is deteriorated in the case of >0.010%. Si improves the AC characteristics without deteriorating the DC characteristics, but in the case of >=1.0%, the DC characteristics are deteriorated.

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 and also has good hot workability.

(Prior Art) A Ni-Fe based magnetic alloy equivalent to JIS PC is a magnetic material that is currently used in an extremely wide range of applications such as magnetic helad 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 include 80%N+-5%Mo-Fe (supermalloy) and 77%Ni5. %Cu-4%Mo-Fe (M
In terms of DC characteristics, the initial magnetic permeability (hereinafter referred to as μi) is 150,000, and the maximum magnetic permeability (hereinafter referred to as μm) is 300. It is about 000.

Furthermore, in terms of AC characteristics, for example, the inductance permeability μi at a plate thickness of 0.2 mm is about too much.

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 Application Laid-Open No. 62-227053 and Japanese Patent Application Laid-Open No. 62-62 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 above-mentioned alloy to improve hot workability during manufacturing, and the DC magnetic properties were improved by removing B during magnetic annealing. ing.

On the other hand, the above component system contains approximately 80 wt% Ni and is expensive, so we fundamentally reviewed the component system, reduced the Ni content, and added C11% Mn, which is cheaper than Ni, to achieve a high initial permeability. Tokuko Sho 62-13420, which achieved
Japanese Unexamined Patent Publications No. 63247336 and No. 63-2003 disclose that additives are added to reduce oxide inclusions and improve direct current magnetic properties.
247339 technology has also been developed. In particular, these JP-A-63-247336 and JP-A-63-247339
The Ni content of the alloy proposed by J.D. 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 St to ordinary Mo-su-malloy to achieve sufficiently satisfactory magnetic permeability and magnetic shielding properties at a relatively low magnetic annealing temperature of 1030'C or less. It is characterized by obtaining.

(Problem to be solved by the invention) The above-mentioned Japanese Patent Application Laid-open No. 62-227053 and No. 22705
Even with the reduction of impurities and the addition of Cr, which are featured in 4, the DC magnetic properties after the final heat treatment in a hydrogen atmosphere (1100°C x 3 hours) are at most 100,000 for Ni, for example, and even higher magnetic properties are possible. It has no choice but to be unsuitable for the required uses.

In addition, in the proposal of JP-A-62-227054, the normal N
Since Cr is newly added to the i-Fe-Mo or Ni-Fe-Mo-Cu components, the cost is high.

In the proposal of JP-A No. 62-227053, in addition to the high cost due to the addition of Cr, the Mn content was increased (to be higher than the normal level).
1.2 to 10-t%), there is also a manufacturing problem in that hot workability becomes extremely poor.

In both of the above two proposals, B is added, but the B addition in this case is to improve hot workability and punchability, and the B intended in these proposals is
No obvious improvement in magnetic properties is observed with just the addition of , and on the contrary, there are cases in which they deteriorate.

Furthermore, in JP-A-63-149361, the magnetic properties are improved by B removal treatment, but the DC magnetic properties obtained after this treatment are at most 75.000 for Ni, which is a level higher than that of ordinary Ni. -Fe-Mo - This is the level obtained with Cu-based alloys. Therefore, this technique is unsuitable for applications requiring higher magnetic properties.

In addition, the above-mentioned JP-A-62-227053 and JP-A-62-227053
No. 27054 and JP-A No. 63-149361 have not yet achieved improvement in AC magnetic properties in common.

On the other hand, JP 62-13420, JP 63-2473
36 and 247339 can provide permalloy with high DC magnetic properties, but Mn, C
There is a manufacturing problem in that the hot workability during manufacturing essentially decreases because u is increased. Also, the saturation magnetic flux density of the alloy obtained by this proposal is, for example, B. (Magnetic flux density at 10 oersted) is at most 5000 Gauss, which is B in supermalloy and Mo5Cu permalloy. This is low compared to 7000-8000 Gauss.

This means that this alloy is supermalloy, Mo, Cu
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, Mo, and Cu permalloy.

In addition, in the technique of JP-A-1-100232 mentioned above, S
Since a large amount of i is added, processability deteriorates and manufacturability is disadvantageous. Also, with this technology, 50Hz
Although its shielding performance has reached the required level, it has the disadvantage that its shielding performance with direct current is somewhat inferior.

"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 furthermore, in order to obtain the same level of required magnetic properties as conventional ones, the magnetic annealing temperature has been lowered by about 100°C than conventional ones. Ni, Mo, Cu,
The present invention was completed by further examining the influence of major components such as Fe, and by expanding the relationship between the characteristics and components obtained thereto to include B-added systems and conducting experiments and research. That is, the present invention is as follows.

(1) Ni: 77.5-79°5wt%, Mo
: 3.8-4.6 wt%, Cu: 1.8-2
．． 5 wt%, Mn: 0.0020 wt%, Si
: 0.2-1.0 wt%, P: 0.010 w
t% or less, S: 0.0020wt% or less, O: 0
．． 0.0030wt% or less, N: 0.0010wt% or less, C: 0.020wt% or less, and contains 4 B, the balance basically consisting of Fe, and Ni,
Mo, Cu, Mn5Fe (however, the values in brackets are wt%)
) N characterized by being contained within a range that satisfies the following.
i-Fe-based high permeability magnetic alloy.

(2) It has the component composition described in the previous section, and after magnetic annealing, Bi at the austenite grain boundary and its vicinity is 10-10.
A Ni-Fe based high permeability magnetic alloy characterized by having a magnetic content of 50 atm%.

(Function) The device according to the present invention, under proper control of impurity elements,
As a level that makes hot workability good, Si, N
By optimizing the amounts of i, Mo, Cu, Mn, Fe, and B added, and controlling the component balance of capacity within a specific range, we were able to achieve improvements that could not be seen in conventional Mo, Cu permalloys or supermalloys made from the same system. It has both excellent direct current 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.
, C is limited by wt% (hereinafter simply referred to as %) and is as follows.

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. When this sl exceeds 0.0020%, N
Even if we try to optimize the amounts of Mo, Cu, Fe, and B, we cannot 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.

O exists as an oxide inclusion in the alloy targeted by the present invention, and if its amount is large, it inhibits grain growth during the final hydrogen annealing, and the grain size after annealing is small, resulting in a decrease in i3 magnetic property. Since it does not improve magnetic properties, it is an extremely harmful element to magnetic properties. That is, if this ON exceeds 0.0030%, the magnetic properties cannot be improved as intended by the present invention even if the amounts of N1% Mo, 'Cu, Fe, and B are optimized as described above, so 0.0030% is the upper limit. And so. Note that in order to improve magnetic permeability in direct current, it is more preferably 0.0010% or less.

In an alloy based on B addition, N easily combines with B to form BN, resulting in a decrease in effective Bl. 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 is achieved by optimizing the amounts of Ni, Mo, Cu, Fe, and B added under the control of impurity elements as described above, and by keeping the component balance of capacity within the characteristic range. These 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 in the range of 3.8 to 4.6%, the high magnetic properties and high shielding properties that are the object of 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 3.8 to 4.6%.

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 also increases the effective magnetic permeability of AC. Furthermore, the squareness (B
r/8m) also has the effect of improving.

This effect of Cu is 77.5 to 79.5% of Ni.
, MO: 3.8-4.6%, the optimum C
ul is 1.8-2.5%. Note that Cu is 1.8%
If Cu is less than 2.5%, the characteristics cannot be improved, and if Cu exceeds 2.5%, the characteristics deteriorate, so the range of Cu was set at 1.8 to 2.5%.

Mn is an element that affects the magnetism of the alloy subject to the present invention, similar to the above-mentioned MO% CLI, and when Mn is 1.1
Although it is possible to achieve the high magnetic permeability targeted by the present invention even if the content is less than 0%, if it exceeds 1.10%, such an improvement in magnetic permeability cannot be achieved, so 1.10% is set as the upper limit. On the other hand, Mn is 0.1
If it is less than 0%, hot workability deteriorates and is not preferable.
．． The lower limit was set at 10%.

B is an essential element in order to achieve the high magnetic permeability intended in the present invention.

4 ([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. With Nanoru, the lower and upper limits of 4 are 0.0005% and 0.00, respectively.
It was set at 70%.

P is an element harmful to the hot workability of the high Ni-Fe alloy that is the object of the present invention. If P exceeds 0.010%, hot workability deteriorates, so the upper limit was set at 0.010%. Note that the lower limit is preferably 0.0 from the economical point of view of melting.
010%.

Si is an element that achieves improvement in alternating current magnetic properties, that is, effective magnetic permeability in alternating current, without deteriorating direct current magnetic properties, within the specified range of the present invention. Also, this Si
It is also an element that, when added in an appropriate amount, can reduce the permeability of direct current and alternating current due to distortion.

The amount of Si that improves the AC magnetic properties as described above without deteriorating the DC magnetic properties is in the range of 0.20 to 1.00%. That is, if the Si content is less than 0.20%, the AC magnetic properties intended by the present invention cannot be improved, while if it exceeds 1.00%, the DC magnetic properties deteriorate, so the above range was set.

Note that the amount of Si added to reduce the deterioration of magnetic permeability due to distortion as intended in the present invention needs to be 0.30% or more.

In order to improve the magnetic properties as the object of the present invention, the component balance of Ni, Mo, Cu, and Fe must be maintained by optimizing the above-mentioned S, O1C%Ni, Mo, CuSMn, and Bq and adding an appropriate amount of Si. It is necessary to optimize the

That is, the parameter Magnetic shielding degree against DC magnetic field, effective magnetic permeability at I KHz, 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 specifications and component balance specifications, the initial magnetic permeability μi is 3, as shown in the examples described later.
00,000 or more, magnetic shielding degree against a DC magnetic field of 500 milligauss is 250 or more, and I at a plate thickness of 0.20 m.
Effective magnetic permeability at KHz is 15.000 or more, 5011z
The squareness can be improved to 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 amount of B at the austenite grain boundaries and their vicinity after heat treatment to increase the final magnetism to IO ~ 50 atm%.
It can have higher initial magnetic permeability, higher degree of magnetic shielding, relatively high effective magnetic permeability, and relatively high squareness.

That is, when the alloy of the present invention is used and the amount of B at the austenite grain boundary and its vicinity after magnetic annealing is within the above range, magnetic properties superior to those of Example 1 described later can be imparted. In other words, as shown in Example 2 described later, the initial magnetic permeability μ
i is 400,000 or more, the degree of magnetic shielding against a DC magnetic field of 500 milligauss is 350 or more, the effective magnetic permeability at IK)Iz at plate thickness 0.20 mm is 16,000 or more, and the squareness at 50Hz is 0. Each can be increased to 92 or higher. The cause of this improvement in magnetic properties is not necessarily 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 causes magnetic properties, especially the movement of domain walls such as initial magnetic permeability. It is presumed that the ease of handling or the ease of rotational magnetization has a positive effect on the required characteristic values.

Note that the Ni-Fe alloy targeted by the present invention has poor hot workability. As a method for 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 m1ca addition is performed, as long as the constituent requirements of the present invention as described above are met, the present invention can be achieved. The improvement in initial magnetic permeability, which is the objective of the invention, is achieved. Further, in the present invention, in addition to the above-mentioned component composition, A1, which is inevitably included when making an iron alloy, will not be mentioned in detail.
For example, /lji! : Content of 0.03% or less is allowed.

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

Example ■.

High Ni-Fe with chemical composition 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.

Each of the materials listed in Table 1 as described above was then cold rolled and annealed to obtain 0.5 mm thin plate samples, and from these samples J! The S ring was used as a punched sample. In addition, the magnetic properties of these samples were heat treated at 1100°C for 3 hours in an atmosphere of purified high-purity hydrogen permeated through a palladium membrane, and at 400°C/hr between 1100'C and 650°C. After that, it was cooled in a furnace and measured, and μi was set to 0.00.
The results obtained as magnetic permeability at 5 oersted, shielding degree, effective magnetic permeability, squareness at 50 Hz, coercive force, magnetic flux density, and initial magnetic permeability when surface pressure is applied are shown in Table 2 below. be.

In other words, the degree of shielding is determined by processing a 0.5 mm thick material with the same manufacturing history as above into a cylinder with a diameter of 50 mm and a length of 200III11, and heat-treating it under the same magnetic annealing conditions as above. External magnetic field (no
), was determined by measuring the internal magnetic field (H6) at the center inside the cylinder when 500 milligauss was applied in a direction perpendicular to the axial direction of the cylinder.

The degree of shielding was measured using a box that was magnetically shielded to a level where the effects of geomagnetism were sufficiently negligible.

The effective magnetic permeability at 1 Hz was determined by measuring the inductance permeability at 5 millier steps using a ring sample with a thickness of 0.2 mm that had undergone magnetic annealing in the same manner as above, and the squareness at 50 Hz was Residual magnetic flux density (Br) and magnetic flux density (BO, +) at a magnetic field of 0.1 oersted using the same ring sample as when measuring the effective magnetic permeability.
It was calculated from the ratio of

Note that the magnetic flux density and coercive force were measured using the same ring sample as used to determine the initial magnetic permeability. That is, magnetic flux density B11
1°. 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 determined by applying a uniform load (surface pressure 4 kgf/mm") in the direction perpendicular to the plate surface of the ring sample using the sample whose initial magnetic permeability was measured above. It was determined by measuring.

In addition, for hot workability, the alloy steel ingot (thickness 70 mm) shown in Table 1 is
The hot-rolled sheet was heated to 150"C, hot-rolled to a final thickness of 5mm, and the occurrence of cracks at the edge of the hot-rolled sheet was observed.Generally, when hot workability is poor, the edge portion is It is known from experience that cracks are more likely to occur. However, regarding the results shown in Table 1.2 above, each village of alloys Nα1 and Nα2 has C, S,
O,N.

BSP, 'Si, Ni, Mo, Cu and Mn
The amounts are all within the range of the components of the present invention, μi is 350,
000 or more, the shielding degree is about 250 or more, the effective magnetic permeability (hereinafter referred to as μe) is more than 15,000, and the squareness at 50Hz (hereinafter abbreviated as Br/B+++) is also more than 0.90, compared to the comparative alloy Nα4. It shows superior magnetic properties compared to each village of ~Nα19. Also, there is no edge cracking of hot rolled sheets.
Good hot workability. In addition, for Nα2 material, C1S, O
, N are reduced to more desirable levels, and Ni,
The degree of shielding, )te, Br78m is even higher than that of the Nα1 material. In addition, in these invention alloys of No. 1 to Nα2 materials, the initial magnetic permeability deterioration when a surface pressure of 4 kgf 7 mm is applied is smaller than that of comparative alloys No. 4 to 19, which will be described later, and the deterioration of characteristics against strain is also small. .

The Nα3 alloy material contains 0.25% Si, and all other components are within the scope of the present invention, including Ni, shielding degree, μe, and B.
r/B11 shows approximately the same level as the above-mentioned Nα1 and Nα2 alloy materials. However, the surface pressure is 4kif/mm
The magnitude of the initial permeability deterioration when 2 is added is approximately 75,000,
This is larger than approximately 50,000 for Nα1 and Nα2 alloy materials. In this way, in order to reduce the deterioration of initial permeability due to strain, the amount of Si should be reduced to 0.30% even within the specified range of the present invention.
It is understood that the value must be higher than that.

In the comparative alloy Nα4 material, only P exceeds the specification of the present invention, and in this case, μm1 shielding degree, μe1Br/Bm
, Ni at the time of strain application is the present invention alloy N (L 1, No, 2
However, there are edge cracks in the hot rolled sheet and the hot workability is inferior. Note that in the Nα21 material, only P exceeds the specified range of the present invention, but P is 0.0
If it exceeds 90% and 0.080%, Ni, shielding degree,
μe, Br/Bm, and Ni when strain is applied are at lower levels than in the alloy of the present invention. Also in this case, edge cracking of the hot rolled sheet occurs and hot workability is poor. As described above, in order to ensure the magnetic properties intended in the present invention, P must be 0.080% or less.

On the other hand, in each village of alloys Nα5 and Nα6, the Ni amount exceeds the upper limit or less than the lower limit, and in each village of alloys Nα7 and Nα8, the Moi exceeds the upper limit or is less than the lower limit. of alloy N
In α9 and Nα19, the amount of Cu exceeds the upper limit or is less than the lower limit, respectively. Furthermore, alloy Nα11 is
The amount of Mn exceeds the upper limit, and the alloy 12 has an amount of Si that exceeds the upper limit, and the alloys Na13 and N1
In No. 14, the amount of B exceeds the upper limit or is less than the lower limit. Furthermore, each village of alloy levels 15 to 18 has C, S, 0, or N exceeding the composition range of the present invention, and alloys 71h19 and Nα20 each have a parameter X exceeding the lower limit defined by the present invention. However, these test materials are below the lower limit.
0 is at a lower level than the examples of the present invention.

In addition, in the comparative alloys, N116, magnetic 7, and 9 to 1
6. Each village of 11h18 to 11h20 is a case where P exceeds the specification of the present invention, and edge cracking of the hot rolled sheet has occurred in each case, and the hot workability is poor. On the other hand, Alloy Arashi 8 and Alloy Arashi 17 have P within the specification of the present invention, have no edge cracks in the hot rolled sheets, and have good hot workability. In addition, alloy N1122 has an Mn content below the lower limit, and N
i, shielding degree, μe, Br78m, and Ni at the time of strain application are approximately at the same level as the present invention alloy, but there is edge cracking of the hot rolled sheet and hot workability is poor.

That is, in the present invention, N1% N0% CLI, Mns
By controlling the individual amounts and balance of B, Si, and Fe within strictly defined ranges, it has good hot workability, as well as excellent initial magnetic permeability, shielding degree, effective magnetic permeability,
Any squareness at 50 Hz can be appropriately obtained. In order to obtain the required characteristics in the present invention, the gas used for heat treatment may be a high-purity H2 gas as shown in this example; (1) It can also be obtained by heat treatment in a 2 atmosphere, that is, in a 11□ gas stream with a melting point of -40°C or lower.

Example 2 A thin plate sample of 0 and 5 fins cold-rolled and annealed in accordance with the invention specification 2 of Example 1 described above has an outer diameter of 45 mm and an inner diameter of 3.
A 3 m JIS ring 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 out from the same sample.

The samples obtained as above are shown in Table 3 (A
), heat treatment was carried out at 1100"c x 3 hours under various atmospheres as shown in Figure 3. Cooling was performed at different cooling rates between 1100°C and 650°C. After that, the magnetic properties and shielding degree were determined by the furnace-cooled samples. was measured.

In addition, the amount of B at the austenite grain boundaries and their vicinity is 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 exposed grain boundary fracture surface was performed at 10 different points using Auger spectroscopy, and the results were averaged. These results are shown in Table 3 (A) and (B).

That is, in those using the above-mentioned alloys No. 2 of the present invention, the amount of B in the austenite grain boundaries and the vicinity thereof is within the range specified by the present invention in sample materials No. 011 to 4, and μ
The m1 shielding degree, μe, and Br/Bm are for the sample No.
It is higher than that of 16.

Furthermore, in these test materials, the initial magnetic permeability deterioration when a surface pressure of 4 kgf 7 cm'' was applied was smaller than that of the comparative alloy of Example 1, indicating that the deterioration of characteristics due to strain was small.

In addition, sample material 5 in Table 3 is a case where the dew point of H2 is higher than 140°C while the atmosphere is maintained at 1100°C for 3 hours, and the Ni, shielding degree, μe, Br of the sample heat-treated under such conditions are /BRI is low compared to other invention examples. That is, the effects of the present invention can be properly exhibited by performing the heat treatment at H2 with 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 IX 10-' Torr.

Example 3 Samples of the present invention alloy Nα2 of Example 1 and the comparative alloy Nα23 having the components shown in Table 4 below were prepared under the same manufacturing conditions as Example 2, and samples were prepared using the same conditions as Example 2. Heat treatment was performed under the magnetic annealing conditions shown in the table, and the magnetic properties and degree of shielding were measured in the same manner as in Example 2. The results are shown in Table 6 below.

Note that this comparative alloy Nα23 contains Ni, Cu, P,
Si 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 Nα2 are the same as those obtained using the comparative alloy Nα23,
Magnetic properties obtained after magnetic annealing at 1100°C for 1 hour, namely Ni, shielding degree, μe, Br/am, μm and H
Compared to c, it shows approximately the same level or a slightly higher value.

In other words, it can be understood that according to the present invention, the magnetic annealing temperature can be lowered by about 100°C to obtain the same properties as the comparative alloy.

In addition to the manufacturing method of the above-described embodiments, the present invention is also applicable to melting, casting, casting into a thin cast plate, as-cast or after hot working and/or descaling, cold rolling, and 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), the cold rolling process may be repeated.

Even with the manufacturing method described above, substantially the same product can be obtained by using the present invention.

"Effects of the Invention" According to the present invention as described above, the magnetic properties of a NiFe-based high permeability magnetic alloy can be appropriately improved, and the magnetic properties such as magnetic permeability and shielding performance can be improved especially in the direct current and low frequency range. In addition, we have provided a high permeability magnetic alloy whose AC permeability is dramatically superior to that of conventional PC permalloy, and is used in various magnetic shielding materials, magnetic head cases, and cores that require even higher shielding properties than conventional ones. It can be widely used in materials used in nonlinear applications such as ceramic amplifiers, pulse transformers, etc., and furthermore, it makes it possible to considerably lower the magnetic annealing temperature to obtain the same level of required characteristics as conventional methods. In addition, the property deterioration due to distortion is small, and it exhibits the required magnetic properties even when used as a structural member such as a shield room, and in addition, it has good hot workability, so it can increase the yield during manufacturing. This invention has a great industrial effect because it can respond quickly and appropriately to the recent demands of the electronics industry.

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%, Si: 0.2-1.0wt%
, P: 0.010wt% or less, S: 0.0020wt%
Below, O: 0.0030wt% or less, N: 0.0010
wt% 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 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) It has the component composition according to claim 1, 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%.