JPH0375327A - Ni-fe series high permeability magnetic alloy - Google Patents

Abstract

PURPOSE:To improve the magnetic characteristics such as magnetic permeability and shielding capacity in a direct current and low frequency area by appropriately controlling impurity elements and controlling the amounts of Ni, Mo, Cu, Mn, Fe and B to be added and the componential balance of each amt. into specified range. CONSTITUTION:The compsn. of the Ni-Fe series high permeability magnetic alloy is formed from the one constituted of, 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% P, <=0.0020% S, <=0.0030% O, <=0.0010% N, <=0.020% C and B in the range satisfying inequality I and the balance essential Fe. Furthermore, Ni, Mo, Cu, Mn and Fe are respectively incorporated thereto in the range satisfying inequality II. In the alloy having the compsn., the amt. of B in austenite grain boundaries and in the neighborhood of them is preferably regulated to 10 to 50atm%.

Description

Detailed Description of the Invention Object of the Invention (Field of Industrial 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 its magnetic properties, and particularly improves its initial permeability under direct current. This invention relates to this excellent magnetic alloy.

(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 hend cases, various cores, metamorphic cores, and various magnetic shielding materials. In other words, such PC permalloy has high magnetic permeability,
It is characterized by a low coercive force, and the ones in practical use today are 80%Ni-5%Mo-Fe (supermalloy) and 77%Ni-5%Cu-4%Mo-Fe (
N0% CLI permalloy), etc., and the level of i3 magnetic permeability normally obtained with these alloys is the initial magnetic permeability (hereinafter μi
The maximum magnetic permeability (hereinafter referred to as μm) is approximately 300,000.

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, JP-A-62227053 and JP-A-62-22 improve the magnetic properties of magnetic alloys with the above-mentioned component system by reducing impurity elements and adding Cr.
7054 has been developed.

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

On the other hand, the above component system contains approximately 80 wt% of Ni and is expensive, so we fundamentally reviewed the component system, reduced the amount of Ni, and added Cu and Mn, which are cheaper than Ni, to achieve a high initial penetration. Japanese Patent Publication No. 62-13420, which achieved magnetic properties, and Japanese Patent Publication No. 63-247336 and Japanese Patent Publication No. 63-247336, which added an appropriate amount of Al to reduce oxide inclusions and improve magnetic properties in addition to the technology of Japanese Patent Publication No. 62-13420. Kaisho 63-247
339 technology has also been developed. Especially these JP-A-63
The μi of the alloys proposed in JP-A-247336 and JP-A-63-247339 is as high as 426,000.

In addition to the above-mentioned demand for improved magnetic properties, there has recently been a demand for manufacturing with the required properties at a lower cost, and from this point of view, the technique of JP-A-1100232 has also been proposed. In other words, this technology
1 to 4 wt of Si to Malloy! It is characterized in that sufficiently satisfactory magnetic permeability can be obtained even when the magnetic annealing temperature is relatively low, such as approximately 1030° C. or lower.

(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 direct JL magnetic properties after the final heat treatment in a hydrogen atmosphere (1100°C x 3 hours) are at most ioo, ooo in μi, for example.
Therefore, it is unsuitable for applications requiring higher magnetic properties.

In addition, in the proposal of JP-A-62-227054, ordinary Ni
Since Cr is newly added to the Fe-Mo-based or Ni-Fe-Mo-Cu-based components, the cost becomes high. On the other hand, in the proposal of JP-A No. 6,222,7053, the addition of Cr not only increases the cost but also increases Mn to a higher level than the normal level (1.2~
10-1%), 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. However, no clear improvement in magnetic properties was observed, and on the contrary, some cases of deterioration were observed.

Furthermore, in JP-A-63-149361, the magnetic properties are improved by B removal treatment, but the magnetic properties obtained after this treatment are at most 75,000 μi, which is a level higher than that of ordinary Ni-Fe. - This is the level obtained with a Mo-Cu alloy. Therefore, this technique is unsuitable for applications requiring higher magnetic properties.

On the other hand, JP 62-13420, JP 63-24733
6 and 247339 can provide permalloy with a high μi, but they have a manufacturing problem in that hot workability during manufacturing is inherently low due to the increased Mns Cu content. Also, the saturation magnetic flux density of the alloy obtained by this proposal is, for example, 5000 Gauss at most when viewed as B+o (magnetic flux density at 10 Oerstes), which is similar to B in supermalloy, Mo, and Cu permalloy. 7000
It is low compared to ~8000 Gauss. This means that the magnetic flux in this alloy is saturated in a lower external magnetic field than supermalloy or MO% Cu permalloy, and when used as a shielding material, it is difficult to use it in places where the external magnetic field is relatively high. Its use must be inappropriate.

Furthermore, the technique of JP-A-1-100232 has a problem in that workability deteriorates and manufacturability deteriorates because a large amount of St is added. Further, in this technology, although the shielding performance of 5011z was at the required level, it had the drawback that the shielding performance in direct current was 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 products as described above. This essentially improves the magnetic properties such as magnetic permeability and shielding performance, and furthermore, it requires magnetic annealing at 100°C more than before to obtain the same level of required properties as before.
With the aim of making it possible to lower the temperature to a certain degree, we further investigated the influence of the main components such as Ni, Mo, Cu, and Fe on the magnetic properties, and applied the relationship between the properties and components obtained there to 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.

(1) Ni: 77.5-79.5wt%, Mo
: 0.1-1.10wt%, Cu: 1.8-2
．． 5 wt%, Mn: 0.010 wt%, P:
0.010 wt% or less, S: 0.0020 wt%
Below, 0: 0.0030wt% or less, N: 0.
0.010 wt% or less, C: 0.020 wt% or less, B is contained within the range of 4, the balance basically consists of Pe, and Ni, Mo, Cu, Mn, Fe are ,(however〔
] indicates -t%)
i-Fe based high permeability magnetic alloy.

(2) It has the component composition described in the previous section, and after magnetic annealing, the amount of B at the austenite grain boundary and its vicinity is 10 to 5.
A Ni-Fe based high permeability magnetic alloy characterized by having a magnetic permeability of 0 atm%.

(Function) The device according to the present invention, under proper control of impurity elements,
By optimizing the amounts of Ni, Mo, Cu, Mn, Fe, and B added, and controlling the component balance of the base amount within a specific range, we have achieved a high The magnetic annealing temperature can be lowered by about 100° C. compared to the conventional method while making magnetic permeability and shielding properties distantly related and obtaining the same level of required characteristics as the conventional method.

That is, first, the improvement of magnetic properties intended in the present invention can be achieved by controlling the level of impurities in the alloy.

The reason for the limit for S, O, N, and C is -t% (hereinafter simply referred to as %) and is as follows.

P is an element that is harmful to the hot workability of the high Ni-Fe alloy that is the subject of the present invention, and weakens the tendency to form a cubic texture during final bisque annealing.
If it exceeds 0.010X, magnetic permeability deteriorates and hot workability deteriorates, so the upper limit was set at 0.010%. Note that the lower limit is preferably 0.0010% from the economical point of view of melting.

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
Even if the amounts of i, Mo, Cu, Fe, and B are optimized, it is not possible to improve the magnetic properties as aimed at in the present invention, and the hot workability deteriorates significantly, so the upper limit is set at 0.0020%. It is necessary to. Note that in order to improve magnetic properties, the content is more preferably 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 magnetic permeability. Since it does not improve magnetic properties, it is an extremely harmful element to magnetic properties. That is, if this zero amount exceeds 0.0030%, Ni, Mo, Cu, and Pe as above.

Even if the Bi content is optimized, the magnetic properties intended by the present invention cannot be improved, so 0.0030% is set as the upper limit.

Note that in order to improve magnetic properties, the content 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 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 %.

Note that in order to improve magnetic properties, the content is more preferably 0.0005% 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 can be achieved only 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 balance of large amounts of components within a specific 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 0.1 to 1.10%, 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 exceeds 4.6%, magnetic permeability cannot be improved;
It is necessary to do so.

In alloys within the specifications of the present invention, Cu dramatically improves DC magnetic properties in the coexistence of B, which will be described later, and also improves the effective magnetic permeability of AC.
) also has the effect of improving the squareness (Br/B+w). This effect of Cu is 77.5% to 79.5% of Ni.
, Mo: Hail occurs when it is 0.1 to 1.10%, and the optimum amount of Cu is 1.8 to 2.5%. Note that Cu is 1.
If the content is less than 8%, such improvement in properties due to Cu cannot be observed,
On the other hand, if Cu exceeds 2.5%, the properties 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 of the present invention, similar to MO% Cu mentioned above, and when Mn is 1.10
% or less can achieve the high magnetic permeability targeted by the present invention, but if it exceeds 1.10%, such improvement in magnetic permeability cannot be achieved, so 1.10% is set as the upper limit. On the other hand, Mn is 0.10
If it is less than 0.0%, hot workability deteriorates and is not preferable.
The lower limit was set at 10%.

This is the must-song 7c chord. [[J --[N)([
B] and (N) are the amounts of B and N added in the alloy, respectively (%), which can effectively achieve the object of the present invention in the range of o,ooos to 0.0070%, but less than o,ooos%. If the magnetic permeability exceeds 0.0070%, the magnetic permeability is determined to be 0.0005% and 0.0070%, respectively.

Next, by optimizing the amount of each component added above, Ni,
It is necessary to optimize the component balance of Mo, Cu, Fe, and B in order to improve the characteristics intended by the present invention, and FIGS. 1 to 4 respectively show the parameters (this Initial magnetic permeability, shielding degree, effective magnetic permeability at 1 kHz, squareness at 50 Hz obtained for each sample material when the horizontal axis is the parameter X and the vertical axis is the amount of B added However, the test materials in Figure 1 are all Ni, Mo, Cu, Mn,
B.

The amounts of P, S, O, N, and C are within the range of the present invention,
Plate thickness 0.5 made by repeating cold rolling and annealing after hot working
JI with an outer diameter of 45 tm and an inner diameter of 33 mm from a thin plate sample of N.
Punch out S-rings to use as samples, and cover them with palladium film i.
Under an atmosphere of a stream of purified high-purity hydrogen, ■10
Heat treatment for 0℃ x 3 hours, from 1ioo℃ to 650℃
It was cooled at a rate of 100° C./hr until then, and then cooled in a furnace. The degree of shielding was obtained by applying an external magnetic field (Ho) of 500 using a Helmholtz coil to a cylinder with a plate thickness of 0.5 s + m, a diameter of 50 + 1 m, and a length of 200 mm, which had the same manufacturing history as above.
It was determined by measuring the internal magnetic field Hl at the center inside the cylinder when ξ Li Gauss is applied in a direction perpendicular to the axial direction of the cylinder. The numbers (shielding degree) in the figure are the values of Ha/H+. Note that the measurements were performed in a box that was magnetically shielded to a level where the influence of geomagnetism was sufficiently negligible.

The effective magnetic permeability of (K'')z is determined by measuring the inductance permeability at 5 millier steps using a ring sample with a thickness of 0.35 mm that has undergone the same magnetic annealing as above, and the squareness at 50H2 is determined by the effective magnetic permeability. The magnetic permeability was determined from the ratio of Br and Bm at a magnetic field of 0.1 oersted using the same ring sample used to measure the magnetic permeability.

In contrast, when X is less than 3.3 or more than 3.8, Ni is at a low level of less than 200,000. μj is decreasing. Further, as shown in FIG. 2, the shielding degree also shows a high value of 300 or more within the range of the present invention, which is higher than the shielding degree of materials outside the range of the present invention.

FIG. 3 shows the effective magnetic permeability, which shows a high value of 6500 or more within the range of the present invention, which is higher than materials other than those of the present invention. Furthermore, in FIG. 4, the squareness at 50 Hz also shows a high value of 0.90 or more within the range of the present invention, which is higher than that of materials other than the materials of the present invention. Based on these facts, the present invention uses N as a component balance that provides high Ni, high shielding degree, high effective magnetic permeability, and high squareness.
i, Mo, Cu, Mn.

B is the range of the present invention as described above, and the parameter
was defined as within the range of 3.3 to 3.8.

By the way, as a result of repeated studies on further improving the magnetic properties using the alloy of the present invention as described above, the present inventors found that after the final heat treatment to increase the magnetism, the austenite grain boundaries and the vicinity of the austenite grain boundaries of the alloy It was confirmed that the initial magnetic permeability Ni and the degree of shielding were further improved when the amount of B was within a specific range. That is, FIG. 5 (al to +d) shows the relationship between Ni and the amount of B at the austenite grain boundary and its vicinity in an alloy having the composition range of the present invention (invention alloy 3 of Example 1 described later).
is a thin plate sample with a thickness of 0.5 n+ produced by repeatedly cold rolling and annealing after hot working with the above alloy, with an outer diameter of 45 tm,
A JIS ring with an inner diameter of 33 m was punched out, and this sample was heat-treated at 1100°C for 3 hours in an atmosphere of purified high-purity hydrogen that was permeated through a palladium membrane.
to 650° C. at a constant cooling rate within the range of 50 to 650° C. and then furnace-cooled. That is, the amount of B at the austenite grain boundaries and their vicinity was determined by cutting out a notched test piece that could be mounted on an Auger observation stage from a sample that had undergone the same thermal processing history as the thin plate sample in which Ni was measured. The grain boundary fracture surface was analyzed in 10 different points using Auger spectroscopy.
The average value is calculated, and the unit is atm%.

The degree of shielding is a plate thickness of 0.5 n+ that has gone through the same manufacturing history as above,
It was determined by measuring the internal magnetic field HI at the center inside the cylinder when an external magnetic field (Ho) of 500 milligauss was applied in the axial direction of the cylinder using a Helmholtz coil with a diameter of 50 questions and a length of 200 mm. The degree of shielding (=H, /H1) was measured in a box that was magnetically shielded to a level where the influence of geomagnetism could be sufficiently ignored. The effective permeability of I KHz is 0.35W, which has undergone the same magnetic annealing as above.
It was determined by measuring the inductance permeability at 5 millier steps using a ring sample of 50 Hz.
The squareness was determined from the ratio of Br and Bm at a magnetic field of 0.1 oersted using the same ring sample used to measure the effective magnetic permeability.

It is clear that the amount of B at the austenite grain boundaries and the vicinity of the Ni shown in FIG. 000 or more. Ni like this
Although the reason for the improvement is not clear, the presence of an appropriate amount of B at and near the grain boundaries changes the properties of the grain boundaries, and this change improves magnetic properties, especially the ease of movement of domain walls such as initial magnetic permeability, or It is presumed that the ease of rotational magnetization has a positive effect on the required characteristic values. From these results, we found that the conditions for achieving both higher Ni and higher shielding degree, relatively high effective magnetic permeability, and relatively high squareness in an alloy within the composition range of the present invention are as follows: It was determined that the Bt of 10 to 50 atmX.

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 adding Lit Ca is often used, but even if such a small amount of Ca is added, the above-mentioned requirements of the present invention cannot be satisfied. In this case, the objective of the present invention, which is to improve the initial magnetic permeability, can be achieved. Further, in the present invention, in addition to the above-mentioned composition, Si and ^i, which are inevitably included in iron alloys, will not be mentioned in detail, but for example, Si: 0.3% or less, A/: 0 Content within the range of .03% or less is allowed.

(Example) Specific examples of the present invention will be described below.

Example】.

The present invention alloy and comparative alloy, which are high NiFe alloys having chemical components as shown in Table 1 below, were produced by vacuum melting,
This was subjected to hot working and descaling to prepare a cold rolled material. The Si content is 0.05 to 0.1 in all sample materials.
It is within the 5% range. In addition, these materials are then subjected to cold rolling processing,
The thin plate samples of 0.5 am were annealed, and JIS rings with an outer diameter of 45 mm and an inner diameter of 33 nm were punched from these samples. 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.
The measurement was performed by cooling at 400"C/hr between ~650℃ and then furnace cooling, and μi was determined as magnetic permeability at 0.005 oerstesod, shielding degree, effective magnetic permeability, 5
The results of squareness, coercive force, and magnetic flux density at 0 Hz are also shown in Table 1.

The shielding degree is a cylinder with a plate thickness of 0.5 mm, diameter som, and length 200 w* that has gone through the same manufacturing history as above, and is applied with an external magnetic field (Ho) of 500 milligauss in a direction perpendicular to the axis of the cylinder using a Helmholtz coil. It was determined by measuring the internal magnetic field H8 at the center inside the cylinder when applied to the cylinder. Shielding degree (-
HO/Hl) 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 1 kHz is determined by measuring the inductance permeability at 5 millier steps using a ring sample with a thickness of 0.35 mm that has been subjected to the same magnetic annealing as above, and the squareness at 5 Hz is determined by the effective magnetic permeability. B at a magnetic field of 0.1 eStesod using the same sample ring as measured.
It was determined from the ratio of r and Bm.

The magnetic flux density and coercive force were measured using the same sample ring used to determine the initial magnetic permeability. The magnetic flux density is BIOo. 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 1000 A#+ is applied and then reversed to make the magnetic flux density O.

In other words, each village on the 1st floor and the 2nd floor is c, p, s, ○.

The amounts of N, B, Ni, Cu, and Mn are all within the range of the components of the present invention, and μi is 350,000.
It shows a high magnetic permeability, and the degree of shielding also shows a high value of about 300 or more. In addition, the effective magnetic permeability, squareness at 50 Hz, and coercive force are also at an excellent level compared to the comparative example.

Also, alloys Nn3 and 4 are C, P, S, O, N,
B.

Ni, Mo, Cu, and Mn1l are alloys within the scope of the present invention, and are alloys in which a trace amount of Ca is added with the intention of improving hot workability, but even in this case, each characteristic value is as described above. It is at approximately the same level as Alloy 1 and 2. In other words, it was confirmed that the effects of the present invention are sufficiently exhibited even in alloys to which 1iica is added.

In addition, in the alloy Nn5 material, C, S, O, and N are reduced to more preferable levels, and each characteristic value is aimed at 1-414.
It is even higher than each village.

On the other hand, each village of Alloy IVk16 and Alloy 7 has a Ni content exceeding the upper limit or less than the lower limit, and each village of Alloy No 8 and Ai9 has an M4 exceeding the upper limit or the lower limit. Alloy ll & 11
Nos. 0 and 11 have a Cu amount exceeding the upper limit or less than the lower limit, respectively. Furthermore, Alloy 1m12 has a Mn content exceeding the upper limit, Alloy 13 has a Mn content below the lower limit, and Alloys IVkl14 and Ih15 each have a Bi content exceeding the upper limit or below the lower limit, Furthermore, each village of alloys 11h16 to m20 is C
, P, S, O, N exceeds the composition range of the present invention, and alloy 11h2L l1h22 has parameter Test magnets 6 to 11 & 121 are all at a lower level than the present invention except for 1t13. As mentioned above, the Mnl of alloy cell 13 is less than the lower limit specified in the present invention, and each characteristic value level is the same as that of the present invention and shows high values, but the hot workability during sample preparation was extremely bad.

That is, in the present invention, Ni, Mo, Cu, Mn, and Ni, Mo, Cu, Mn, and C, P, S, O, and N impurity elements are reduced.
B.

By controlling the amount and balance of Fe within strictly defined ranges, excellent initial magnetic permeability, shielding degree, effective magnetic permeability, squareness at 50 Hz, and coercive force can be achieved for the first time. In order to obtain the required characteristics in the present invention, the gas used for the heat treatment can be a high-purity H2 gas as shown in this example, but the same characteristics can be obtained by using a high-purity H2 gas as specified in JIS. It can also be obtained by heat treatment in a normal H2 atmosphere, that is, in a 11□ gas stream with a dew point of 40°C or less.

Example 2 The outer diameter of the 0.5 mm thin plate sample of the present invention alloy ml-11h4 of Example 1, which was cold rolled and annealed, was 4 mm.
A JIS ring with 5 meshes and an inner diameter of 33 mm 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 2 below, and then cooled at different temperatures between 1100°C and 650°C. The magnetic properties and degree of shielding were measured using samples that were cooled at high speed and then furnace cooled.

In addition, after the above heat treatment, Bi in the austenite grain boundaries and their vicinity is treated by adding electrolytic hydrogen by cathodic electrolysis to perform grain boundary embrittlement treatment, and grain boundary fracture is performed 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 the second
As shown in the table.

That is, in the case of using 1 kl of the alloy of 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, and the μi and shielding degree are those of sample material 11h6, in which the amount of B at the austenite grain boundary and the vicinity thereof is outside the specification of the invention. It's higher than that. In addition, in the case of using the present invention alloy No. 2, the amount of B at the austenite grain boundary and its vicinity in each village of 11 m24 of the sample material was within the specification of the present invention, and the μi and the degree of shielding were at the austenite grain boundary and its vicinity. The amount of B in the vicinity is higher than that in each village of sample materials N7 and Asahi 12, which are outside the scope of the present invention.

In the case of using the alloy Il&13 of the present invention, the sample material Na1
The amount of B at the austenite grain boundary and its vicinity in each village of 4 to 11h16 is within the specification of the present invention, and its μi
and the shielding degree is Bl at the austenite grain boundary and its vicinity.
is higher than that of sample material 11h13 and fish 18, which are not specified in the present invention.

Furthermore, when the present invention alloy 11h4 is used, the Bi at the austenite grain boundary and its vicinity in each village of sample materials m19.20.22 and 23 is within the present invention specification, and their μi and shielding The degree is higher than that of sample material 11m24, which is out of specification. In addition, the Bi of the austenite grain boundary and its vicinity is within the specification of the present invention in the test material Ko1-N14. N18~hase11. N114
~N116. Hiro 19. 20. Hiro 22. Na2
No. 3 has excellent initial magnetic permeability and shielding degree, and also has relatively high effective magnetic permeability and squareness at 50 Hz.

In addition, the sample material was 1m2. Magnetic 14. N115. Disease 18.
Na19 has a higher initial permeability and these materials have closer coercivity.

In addition, the sample materials 11m5.17 and 21 in Table 2
Each village is H during the atmosphere maintained at 1100℃
This is the case where the dew point of No. 8 is higher than 140° C., and the μi of the sample heat-treated under such conditions is clearly low at about 200,000, and the degree of shielding is also about 100, which is lower than other invention examples. That is, the effects of the present invention can be properly exhibited by performing 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 I x 10-'Torr.

(Example 3) Samples were made under the same manufacturing conditions as in Example 2 for the above-mentioned Example 1 outside the scope of the present invention 4 and Comparative Alloy Hiro 23 having the components shown in Table 3. Heat treatment was performed under the magnetic annealing conditions as shown in Figure 4, and the magnetic properties and shielding degree were determined in the same manner as in Example 2. The results are shown in Table 4.

In this comparative alloy No. 23, Ni and Cu are outside the scope of the present invention, and other components are within the scope of the present invention.

The magnetic properties are approximately the same level or slightly higher than those obtained after magnetic annealing at 1000° C. for 1 hour using the invention alloy 4. That is, it can be seen 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.

The present invention is not limited to the manufacturing method of the embodiments, but may also be carried out by melting and refining, casting into a thin cast plate, as-cast or after hot working and/or descaling, cold rolling, and annealing.

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 better 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 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
The system has appropriately improved the magnetic properties of the high permeability magnetic alloy, and has dramatically superior magnetic properties such as magnetic permeability, especially in the DC and low frequency range, and shielding performance compared to conventional PC permalloy. We provide magnetic permeability magnetic alloys for various types of magnetic shielding materials, magnetic head cases, cores, and even magnetic amplifiers that require higher shielding properties than conventional ones.
It can be widely used in materials used in nonlinear applications such as pulse transformers, and it also makes it possible to reduce the magnetic annealing temperature by about 100 degrees Celsius compared to conventional methods to obtain the same level of required characteristics as conventional ones. It has little characteristic deterioration due to distortion, and can exhibit the required magnetic properties even when used as a structural component such as a shielded room.It is suitable for industrial use because it can respond appropriately and quickly to the recent demands of the electronics industry. This is a highly effective invention.

[Brief explanation of drawings]

The drawings show the technical contents of the present invention, and Fig. 1 shows the initial magnetic permeability μi and the parameter X, Fig. 3 shows the effective magnetic permeability of AC and the parameter 2 is a chart showing the relationship between magnetic permeability μ and Bt at and near austenite grain boundaries. Parameter
70 80 90 Ostenite grain boundary and ζ〈Bl in its vicinity (a mountain υ Fig. 4 flat bottom) December 15, 1999, Director General of the Japanese Bureau of Art, Mr. Yoshida Bunki 1, Incident Indication 1999 Patent Application No. 256383 No. 3゜4゜Person making the amendment Name of address related to Hanyu Name of agent

Claims (1)

[Claims] 1. Ni: 77.5 to 79.5 wt%, Mo: 3.8 to 79.5 wt%
4.6 wt% Cu: 1.8 to 2.5 wt%, Mn: 0.
1 to 1.10 wt%, P: 0.010 wt% or less, S:
0.0020wt% or less, O: 0.0030wt% or less, N: 0.0010wt% or less, C: 0.020wt%
Contains the following and B, 0.0005wt%≦[B]-10.8/14[N]≦
The content is within the range of 0.0070 wt%, and the remainder basically consists of Fe, and Ni, Mo, Cu, Mn, and Fe are contained within the range of 3.3≦(2.02×[Ni]−11.13×[ Mo〕
−1.25×[Cu]−5.03×[Mn])/2.1
3×[Fe]≦3.8 (however, values in brackets are wt%).
i-Fe based high permeability magnetic alloy. 2. 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 10 to 10.
A Ni-Fe based high permeability magnetic alloy characterized by having a magnetic flux of 50 atm%.