JPH0699766B2 - Ni-Fe system high permeability magnetic alloy - Google Patents

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, which has improved magnetic characteristics, and has particularly excellent direct-current magnetic characteristics and excellent magnetic properties. The present invention relates to a magnetic alloy which has the above-mentioned AC magnetic characteristics, has small deterioration due to distortion of magnetic permeability, and has good hot workability.

(Prior Art) Ni-Fe magnetic alloys equivalent to JIS PC are magnetic materials that have a very wide range of applications, such as magnetic head cases, various cores, metamorphic magnetic cores, and various magnetic shield materials. In other words, such PC permalloy is characterized by high magnetic permeability and low coercive force.
% Ni-5% Mo-Fe (Supermalloy), 77% Ni-5%
Cu-4% Mo-Fe (Mo, Cu permalloy) and the like, and the level of the magnetic permeability normally obtained with these alloys is 150,000 in the initial magnetic permeability (hereinafter referred to as μi) and the maximum magnetic permeability (hereinafter (Hereinafter referred to as μm) is about 300,000.

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

However, due to recent advances in electronics, miniaturization and high performance of various devices have progressed, and further improvement in the characteristics of magnetic alloys as described above is desired. That is, JP-A-62-127053 and JP-A-62-127054, in which the DC magnetic characteristics of the magnetic alloys of the above-mentioned components are improved by reducing the impurity elements and adding Cr in response to such requirements, have been announced.

Further, in Japanese Patent Laid-Open No. 63-149361, it was announced that a material containing B added to the alloy of the above component system in order to improve the hot workability at the time of production is subjected to B removal during magnetic annealing to improve the DC magnetic characteristics. There is.

On the other hand, in the above component system, Ni is contained at about 80 wt% and is expensive, so the component system was fundamentally reviewed, Ni was reduced, and instead, Cu and Mn, which are cheaper than Ni, were added to increase the initial permeability. In addition to the technology of Japanese Patent Publication No. 62-13420, the Japanese Patent Publication No. 63-247336 and Japanese Patent Laid-Open Publication No. 63-247336, in which an appropriate amount of Al is added to reduce oxide inclusions and enhance DC magnetic properties, The technology of Kaisho 63-247339 has also been developed. In particular, the μi of the alloys proposed by JP-A-63-247336 and JP-A-63-247339 is as high as 426,000 at maximum.

Further, in addition to the above-mentioned demands for improving the magnetic properties, it has recently been required to manufacture the required properties at a lower cost. From this point of view, the technique of JP-A-1-100232 is also proposed. . In other words, this technique is sufficiently satisfactory even when the magnetic annealing temperature is 1030 ° C. or lower, which is a relatively low temperature, by adding 1 to 4 wt% of Si to ordinary Mo supermalloy.
It is characterized by obtaining permeability and magnetic shielding property at Hz.

(Problems to be Solved by the Invention) DC magnetic characteristics after the final heat treatment (1100 ° C. × 3 hours) in a hydrogen atmosphere by reducing impurities and adding Cr, which are the features of JP-A-62-127053 and 227054. Is, for example, at most 100,000 in μi, and it is unavoidable that it is not suitable for applications requiring magnetic characteristics higher than that.

Further, in the proposal of Japanese Patent Laid-Open No. 62-227054, since Cr is newly added to a usual Ni-Fe-Mo-based or Ni-Fe-Mo-Cu-based component, the cost becomes high. On the other hand, in the proposal of Japanese Patent Laid-Open No. 62-227053, in addition to the high cost due to the addition of Cr, there is a manufacturing problem that the hot workability is extremely deteriorated because Mn is made higher than the normal level (1.2 to 10 wt%). Have

In both of the above two proposals, B is added, but the addition of B in this case is to improve hot workability and punchability. Only the addition of B intended in these proposals is performed. In, no clear improvement in magnetic properties was observed, and conversely, deterioration was also observed.

Further, in JP-A-62-149361, the magnetic characteristics are improved by de-B treatment, but the DC magnetic characteristics obtained after this treatment are at most 75,000 μi, and this level is normal Ni-Fe. -This is the level obtained with Mo-Cu based alloys. Therefore, this technique is inevitably unsuitable for applications requiring higher magnetic properties.

Incidentally, in the above-mentioned JP-A-62-127053, JP-A-227054, and JP-A-63-149361, improvement in AC magnetic characteristics has not been achieved in common.

On the other hand, Japanese Examined Patent Publication No. 61-13420, Japanese Unexamined Patent Publication Nos. 63-247336 and 24733.
Although the technique of 9 can provide permalloy having high direct current magnetic characteristics, it has a problem in manufacturing that hot workability during manufacturing is essentially lowered because Mn and Cu are increased. In addition, the saturation magnetic flux density of the alloy obtained by this proposal is 5000 Gauss at the highest when viewed in B ₁₀ (magnetic flux density at 10 Oersted), and it is 7,000 to 8,000 gau of B ₁₀ in supermalloy, Mo, Cu permalloy. Low when compared.
This means that this alloy saturates the magnetic flux in the material with an external magnetic field lower than Supermalloy, Mo, and Cu Permalloy, and when used as a shield material, the external magnetic field is relatively high. Inevitably the use is unsuitable. Further, this alloy has a drawback that the AC magnetic properties are lower than those of supermalloy, Mo, and Cu permalloy. It should be noted that in the above-mentioned technique of Japanese Patent Laid-Open No. 1-100232, the shielding performance at 50 Hz has a required level, but the shielding performance at DC is inferior to that extent.

“Structure of the Invention” (Means for Solving the Problems) The present invention was devised through repeated studies to solve the problems in the above-described conventional techniques.
It has both good hot workability and excellent AC magnetic characteristics as well as excellent DC magnetic characteristics, and the deterioration due to the distortion of permeability is small, and the required magnetic characteristics at the same level as before can be obtained. In addition, the magnetic annealing temperature was set to 100
It was also made possible to lower the temperature by about ℃. By further examining the effect of the main components such as Ni, Mo, Cu, and Fe on the magnetic properties, the relationship between the obtained properties and the components was
The present invention has been completed as a result of repeated experiments and studies by expanding to an addition system. That is, the present invention is as follows.

(1) Ni: 77.5 to 79.5 wt%, Mo: 3.8 to 4.6 wt%, Cu: 1.8 to 2.5 wt%, Mn: 0.1 to 1.10 wt% P: 0.010 to 0.080 wt%, Si: less than 0.20 wt%, S : 0.0020 wt% or less, O: 0.0030 wt% or less, N: 0.0010 wt% or less, C: 0.020 wt% or less, and B Contained within the range of, and the balance basically consists of Fe, and Ni, Mo, Cu, Mn, Fe (However, the content in [] is wt%).
-Fe-based high-permeability magnetic alloy.

(2) Ni: 77.5-79.5wt%, Mo: 3.8-4.6wt%, Cu: 1.8-2.5wt%, Mn: 0.1-1.10wt%, P: 0.010-0.080wt%, Si: 0.2-1.0wt% , S: 0.0020 wt% or less, O: 0.0030 wt% or less, N: 0.0010 wt% or less, C: 0.020 wt% or less, and Contained within the range of, and the balance basically consists of Fe, and Ni, Mo, Cu, Mn, Fe (However, the content in [] is wt%).
Ni-Fe based high permeability magnetic alloy.

(3) Ni-Fe high permeability having the composition as described in the above item (1), and having a B content of 10 to 50 atm% at and near the austenite grain boundaries after magnetic annealing. Magnetic susceptibility magnetic alloy.

(4) The amount of B in the austenite grain boundary and its vicinity after the magnetic annealing has the component composition described in the above item (2).
Ni-Fe high permeability magnetic alloy characterized by 10 to 50 atm%.

(Operation) According to the present invention, under proper control of impurity elements,
P, Si, and N are the levels that give good hot workability.
Not found in conventional Mo, Cu permalloy and supermalloy by the same system by optimizing the addition amount of i, Mo, Cu, Mn, Fe and B and controlling the component balance of each amount within a specific range. It has excellent direct current magnetic characteristics and excellent alternating current magnetic characteristics. Furthermore, in order to obtain the required magnetic characteristics at the same level as before, the magnetic annealing temperature was set to 100
It is possible to lower the temperature by about ℃.

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

S is detrimental to hot workability, and it inhibits grain growth during final hydrogen annealing through the formation of sulfides, and the grain size after annealing is small, so magnetic permeability does not improve. On the other hand, it is an extremely harmful element. If the S content exceeds 0.0020%, Ni, Mo,
Even if the Cu, Fe and B contents are optimized, the magnetic properties intended in the present invention cannot be improved, and the hot workability is significantly deteriorated, so 0.0020% is required as the upper limit. is there.
In order to further improve the magnetic permeability of direct current and alternating current,
0.0005% or less is more desirable.

O exists as an oxide inclusion in the alloy targeted by the present invention, and if the amount thereof is large, it inhibits grain growth during the final hydrogen annealing, and since the grain size after annealing is small, the magnetic permeability is high. Since it does not improve, it is an extremely harmful element for magnetic properties. That is, if this O amount exceeds 0.0030%, N
Even if the amounts of i, Mo, Cu, Fe and B are optimized, the magnetic properties intended in the present invention cannot be improved, so 0.0030% was made the upper limit. Note that 0.0005% or less is more preferable in order to further improve the magnetic permeability with direct current and alternating current.

In an alloy based on addition of B, N easily combines with B to form BN, so that the amount of effective B decreases. In addition, the large amount of BN that is formed adversely affects the magnetic properties, so that it adversely affects the alloy. That is, if this N exceeds 0.0010%, the magnetic characteristics deteriorate remarkably for the above reasons, so 0.0010% was made the upper limit. In order to further improve the magnetic permeability with alternating current, 0.00
05% or less is more preferable.

C exists as an interstitial element in the target alloy of the present invention, and if it is present in a large amount, the magnetic permeability decreases, so it is an element harmful to the magnetic properties. If it exceeds 0.020%, C is for this reason. Since the deterioration of magnetic properties becomes remarkable, 0.020% was set as the upper limit.

Now, in the present invention, under the control of the above-described impurity elements, the respective amounts of P, Ni, Mo, Cu, Fe and B added are optimized, and the purpose is to make the component balance of each amount within a specific range. Achieved and these are as follows:

Ni can obtain high magnetic properties and high shielding properties as intended in the present invention in the range of 77.5 to 79.5%. This Ni
Is less than 77.5% or exceeds 79.5%, the magnetic permeability decreases in any case, so 77.5% is the lower limit and 79.5% is the upper limit.

Mo can achieve the high magnetic properties and high shielding properties aimed at by the present invention when in the range of 3.8 to 4.6%. That is, if Mo is less than 3.8% or exceeds 4.6%, the improvement in magnetic permeability cannot be achieved, so it is necessary to set it to 3.8 to 4.6%.

Cu, in an alloy in which Ni, Mo and other components are within the specified range of the present invention, dramatically improves the direct current magnetic characteristics under the coexistence of B described later and also improves the effective magnetic permeability of alternating current. It has the effect of improving the squareness (Br / Bm) at AC (50Hz). The effect of Cu is that Ni is 77.5
Appears when ~ 79.5% Mo: 3.8-4.6%, optimal Cu
The amount is 1.8-2.5%. If Cu is less than 1.8%, such improvement in properties cannot be achieved by Cu. On the other hand, if Cu exceeds 2.5%, these properties are deteriorated, so the Cu range is 1.8.
~ 2.5%.

Mn is an element that affects the magnetism of the alloy of the present invention like Mo and Cu described above, and even if this Mn is 1.10% or less, it is possible to achieve the target high magnetic permeability in the present invention. If it exceeds the above, such improvement in magnetic permeability cannot be achieved, so the upper limit is 1.10%. On the other hand, if Mn is less than 0.10%, the hot workability deteriorates, which is not preferable, so 0.10% was made the lower limit.

B is an essential element for achieving the high magnetic permeability intended in the present invention.

([B] and [N] are the addition amounts of B and N in the alloy,
%) Is 0.0005 to 0.0007%, the object of the present invention can be effectively achieved, but if less than 0.0005%, the magnetic permeability is not improved,
On the other hand, if it exceeds 0.0070%, the magnetic permeability will decrease, The lower and upper limits of 0.0005% and 0.0070%, respectively.

P is an element that can improve the AC magnetic characteristics, that is, the effective magnetic permeability in the AC and the squareness in the low frequency region without degrading the DC magnetic characteristics in the components within the specified range of the present invention. Further, P is also an element capable of reducing deterioration due to distortion of direct current and alternating current magnetic permeability under an appropriate amount of addition.

The amount of P that improves the AC magnetic characteristics as described above without degrading the DC magnetic characteristics is in the range of 0.010 to 0.080%. If P is less than 0.010%, the AC magnetic properties intended in the present invention cannot be improved, while if it exceeds 0.080%, the DC magnetic properties deteriorate, so 0.010% and 0.080% were made the lower and upper limits, respectively. It should be noted that the addition amount of P, which is intended to reduce the deterioration of the magnetic permeability due to strain, is 0.020%.
The above is preferable.

Si is an element that further improves the alternating-current magnetic characteristics, that is, the effective magnetic permeability under alternating current, without degrading the direct-current magnetic characteristics in the alloy having the components within the specified range of the present invention. Again this
Si is also an element that makes it possible to further reduce deterioration due to distortion of DC and AC magnetic permeability under a specific addition amount. However, since the saturation magnetic flux density decreases with the addition amount of Si, it is preferable that the Si content be 0.20 wt% or less in applications requiring a relatively high magnetic flux density. That is, Si
At 0.20 wt% or less, the magnetic flux density (hereinafter referred to as B ₁₀₀₀ ) in the material when external magnetization of 1000 A / m is applied is 7700.
Has a value greater than or equal to Gauss. Improve the above AC magnetic characteristics without degrading the DC magnetic characteristics.
The Si content is in the range of 0.20 to 1.00%. That is, if the Si content is less than 0.20%, the intended AC magnetic characteristics cannot be improved in the present invention, while the DC magnetic characteristics exceeding 1.00% deteriorate, so the content was made 0.20 to 1.00%. Note that the addition amount of Si that reduces deterioration due to strain of magnetic permeability intended in the present invention is 0.30.
% Or more is preferable.

In order to improve the magnetic properties aimed at by the present invention, the appropriate amounts of S, O, N, C, Ni, Mo, Cu, Mn and B described above, Si,
With the addition of an appropriate amount of P, a parameter X that defines the component balance of Ni, Mo, Cu, B and Fe, Is between 3.2 and 3.8, and Is in the range of 0.0005 to 0.0070%, the initial magnetic permeability of DC after magnetic annealing, the magnetic shielding against a DC magnetic field of 500 milligauss, the effective magnetic permeability at 1 KHz, and the squareness at 50 Hz. The characteristics can be dramatically improved.

That is, according to the above-described component regulation and component balance regulation, as shown in Example 1 described later, the initial magnetic permeability μi is
It is possible to obtain a magnetic shielding degree of 250 or more for a DC magnetic field of 300,000 or more and 500 milligauss, an effective magnetic permeability of 15,000 or more at a plate thickness of 0.20 mm, and a squareness of 0.90 or more at 50 Hz.

In order to further enhance the magnetic properties in the alloy of the present invention, the B content in the austenite grain boundaries after heat treatment for enhancing the final magnetism and in the vicinity thereof is higher than the initial permeability in the range of 10 to 50 atm%. It can have a high degree of magnetic shielding, a relatively high effective magnetic permeability, and a relatively high squareness.

That is, by using the alloy of the present invention, if the B content in the austenite grain boundaries after magnetic annealing and in the vicinity thereof is within the above range, it is possible to impart more excellent magnetic characteristics to those of Example 1 described later. That is, 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 DC magnetic field of 500 milligauss is 350 or more, the effective magnetic permeability at 1 KHz at a plate thickness of 0.20 mm is 17,000 or more, and the square at 50 Hz. The moldability can be 0.93 or more.

The Ni-Fe alloy targeted by the present invention is inferior in hot workability. As a method of improving the workability, a combination of a small amount of B and a small amount of Ca is often combined, but even if such a small amount of Ca is added, the constituent requirements of the present invention as described above can be satisfied. For example, the improvement of the initial magnetic permeability which is the object of the present invention is achieved. Further, in the present invention, in addition to the component composition as described above, Al inevitably contained in the case of making an iron alloy will not be described in detail, for example, Al: 0.0
Content within the range of 3% or less is allowed.

Although the cause of such improvement in magnetic properties is not clear, the presence of an appropriate amount of B at the grain boundaries and in the vicinity thereof changes the properties of the grain boundary parts, and this change causes the magnetic properties, especially the movement of the magnetic domain wall such as initial permeability. It is presumed that the ease of rotation or the ease of rotational magnetization has a good influence on the required characteristic value.

A specific embodiment of the present invention will be described below.

Example 1 Inventive alloys and comparative alloys of the high Ni-Fe alloys having the chemical components shown in Table 1 below were melted by vacuum melting, hot-worked, descaled, and cooled. Prepared rolled material. These materials are then cold rolled and annealed to 0.5 mm.
Or 0.2mm thin plate sample, outer diameter is 45mm than these
A JIS ring with an inner diameter of 33 mm was punched out as a sample.

The magnetic properties of the samples shown in Table 1 above were heat-treated at 1100 ° C for 3 hours in an atmosphere of a high-purity hydrogen gas which had been purified by permeating a palladium film, and the magnetic properties were measured at 1100 ° C to 650 ° C.
It was cooled at 400 ° C / hr between ℃, and then cooled in a furnace to measure it. The result of μi was the permeability at 0.005 Oersted and the shielding, effective permeability, squareness at 50 Hz, and The results of the magnetic force, the magnetic flux density and the initial magnetic permeability when the surface pressure is applied are as shown in Table 2 below.

The shielding degree is the same manufacturing history as described above, and a material with a thickness of 0.5 mm is processed into a cylinder with a diameter of 50 mm and a length of 200 mm, which is heat-treated under the same magnetic annealing conditions as described above. ₀ ), 500 milligauss was applied in the direction perpendicular to the axial direction of the cylinder, and the internal magnetic field H ₁ at the inner center of the cylinder was measured. The degree of shielding (= H ₀ / H ₁ ) was measured in a box that was magnetically shielded to a level where the effect of geomagnetism could be sufficiently ignored.

The effective permeability of 1 KHz is the same as the above, the thickness of the sheet after magnetic annealing is 0.
Using a ring sample of 20 mm, it was obtained by measuring the inductance magnetic permeability at 5 mOersted, 50 Hz
The squareness of the magnetic field was measured by measuring the residual magnetic flux density (B
r) and the magnetic flux density (Bo.1).

The magnetic flux density and the coercive force were measured on the same ring sample as that used for obtaining the initial magnetic permeability. Magnetic flux density B ₁₀₀₀ is 1000 A / m
Is the magnetic flux density when an external magnetic field is applied, and the coercive force is 1000
It is the strength of the magnetic field that makes the magnetic flux density zero by applying an external magnetic field of A / m and then reversing.

For the initial permeability when surface pressure is applied, use the sample for which the above initial permeability was measured and apply a uniform load (contact pressure 4 kgf / mm ² ) in the vertical direction to the plate surface of the ring sample to determine the initial permeability. It was determined by measuring.

That is, each alloy No. 1 and No. 2 according to the present invention is C,
The amounts of S, O, N, B, P, Ni, Mo, Cu and Mn are within the ranges of the components of the present invention, and particularly No. 1 and No. 2 alloys are the first invention and the second invention, respectively. Although it is an alloy that corresponds to the invention, μi is 300,000 or more, the shielding degree is about 250 or more, the effective magnetic permeability (hereinafter abbreviated as μe) is 15,000 or more, and the squareness at 50 Hz (hereinafter abbreviated as Br / Bm) is 0.90. The above shows excellent magnetic characteristics as compared with the comparative alloy. Further, No. 2 is a case where Si was added within the range specified by the present invention, and μe shows a higher value than No. 1.

Alloy No. 3 is C, S, O, N, B, Ni, Mo, Cu and Mn.
Within the composition range of the present invention, a trace amount of an alloy which corresponds to the claims of the present invention and which is intended to improve hot workability
Although it is an alloy with Ca added, in this case as well,
The magnetic properties are almost at the same level as the alloys No. 1 and No. 2 described above. That is, it was confirmed that the effects of the present invention are sufficiently exerted even in the alloy in which the trace amount of Ca is added.

Furthermore, in alloy No. 4 material, C, S, O, and N are reduced to more preferable levels, and μi, shielding degree, μe, Br / B
m is higher than that of No. 1 to No. 3 materials. In addition, in these No. 1 to No. 4 alloys of the present invention, deterioration of initial magnetic permeability when a surface pressure of 4 kgf / mm ^{2 is} added is also smaller than that of Comparative Alloys No. 5 to No. 21 described later, and characteristics against strain. It is understood that the deterioration of is small.

On the other hand, the alloys No. 5 and No. 6 have a Ni content exceeding the upper limit or less than the lower limit, respectively, and the alloys No. 7 and No. 8 have a Mo content at the upper limit. Alloys below the lower limit or below the lower limit, alloy Nos. 9 and 10
Indicates that the amount of Cu exceeds the upper limit or is less than the lower limit, respectively. Further, alloy No. 11 has an Mn amount exceeding the upper limit, alloy No. 12 has an Si amount exceeding the upper limit, and alloys No. 13 and No. 14 have B amounts respectively. Exceeds the upper limit or is less than the lower limit, and
Alloy No. 15 to No. 19 are C, P, S, O,
Any of N exceeds the composition range of the present invention, or alloy No. 2
0 and No. 21 are those in which the parameter X exceeds the upper limit and less than the lower limit specified in the present invention, respectively, but these test materials No. 5 to No. 21 are all in comparison with the present invention example. And is at a low level.

That is, according to the present invention, Ni, Mo, Cu, Mn, B, and Fe are controlled within the range in which their individual amounts and balances are strictly defined under the reduction of impurity elements such as C, P, S, O, and N. As a result, excellent initial permeability, shielding degree, effective permeability, and squareness at 50 Hz can be achieved for the first time. In addition, in order to obtain the required characteristics in the present invention, the gas used for the heat treatment is
Although it is possible with high purity of the H ₂ gas as shown in this embodiment, similar properties are usually as specified in JIS H ₂
It can also be obtained by performing heat treatment in an atmosphere, that is, in a H ₂ gas stream having a dew point of −40 ° C. or lower.

Example 2 J of the outer diameter of 45 mm and the inner diameter of 33 mm from a thin plate sample of 0.5 mm which was cold-rolled and annealed with respect to the alloy No. 4 of the present invention of Example 1 described above.
An IS ring was punched out and used as a sample. In addition, a notched test piece that can be attached to the stage for auger observation was cut out from the same sample.

The samples obtained as described above were heat-treated at 1100 ° C for 3 hours in various atmospheres as shown in Table 3 below, and the cooling rate was different between 1100 ° C and 650 ° C. The magnetic properties and the degree of shielding were measured using a sample that was cooled in a furnace and then cooled in a furnace. The amount of B in the austenite grain boundaries and in the vicinity thereof is such that after the heat treatment, grain boundary embrittlement treatment is performed by adding electrolytic hydrogen by the cathode electrolysis method, and grain boundary fracture is performed in a vacuum. The surface components were analyzed for ten different points by Auger spectroscopy and averaged. These results are as shown in Table 4 together.

That is, the test material No. 1 using the alloy No. 4 of the present invention
In Nos. 4 to 4, the amount of B in the austenite grain boundary and its vicinity is within the scope of the present invention, and μi, shielding degree, μe, Br / Bm
Has a higher B content in the austenite grain boundaries and in the vicinity thereof than that of the sample material No. 6 which does not meet the requirements of the present invention. Also,
It can also be seen that in these test materials, the deterioration of initial magnetic permeability when a surface pressure of 4 kgf / cm ^{2 is} applied is smaller than that of the comparative alloy of Example 1, and the characteristic deterioration due to strain is small.

In addition, sample material No. 4 in Tables 3 and 4 is 1100 ° C x 3hr
When the dew point of H ₂ is higher than −40 ° C during holding in the atmosphere of, the μ of the sample heat-treated under such conditions is
i, the degree of shielding, μe, and Br / Bm are lower than those of other invention examples. That is, the effect of the present invention is −40 dew point specified in JIS.
Properly exhibited by heat treatment at H ₂ below ℃. Further, the effect of the present invention can be exhibited even by heat treatment under a high vacuum of 1 × 10 ⁻⁵ Torr.

Example 3 Alloy No. 4 of the present invention in the above-mentioned Example 1 and the following fifth
A sample was prepared under the same preparation conditions as in Example 2 for Comparative Alloy No. 22 having the components shown in the table, and heat treated under the magnetic annealing conditions shown in Table 6, to obtain the magnetic properties and The degree of shielding was the same as in Example 2. The results are shown in Table 7.

In addition, in this comparative alloy No. 22, Ni, Cu, and P are outside the scope of the present invention, and the other components are within the scope of the present invention.

Using the invention alloy No. 4, the properties obtained after magnetic annealing at 1000 ° C for 1 hour are 1100 ° C x 1 using the comparative alloy No. 22.
The magnetic properties obtained after the magnetic annealing for a long time, that is, μi, the degree of shielding, μe, Br / Bm, μm, and Hc, show almost the same level or slightly higher values. That is, according to the present invention,
To obtain the same properties as the comparative alloy, a magnetic annealing temperature of about 100
It can be seen that the temperature can be lowered by ℃.

The present invention is not only the manufacturing method of the above-described embodiment, but also melting / melting, casting into a thin cast plate, as-cast or after hot working and / or descaling, cold rolling, annealing. May be.

Instead of hot working, or warm working may be performed to improve the efficiency of cold rolling.

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

Further, instead of one cold rolling, cold rolling, recrystallization annealing (for example, 800 ° C. or higher), and cold rolling may be repeated.

Even with the manufacturing method as described above, almost the same products can be obtained within the scope of the present invention.

"Effects of the Invention" According to the present invention as described above, the magnetic characteristics of the Ni-Fe-based high-permeability magnetic alloy are appropriately improved, and particularly, magnetic characteristics such as the magnetic permeability in the direct current and low frequency regions and It provides a magnetic alloy with high magnetic permeability, which has dramatically superior shield performance and AC magnetic permeability than conventional PC Permalloy. It can be widely applied to cases, cores, and materials used for non-linear applications such as magnetic amplifiers and pulse transformers. In addition, the magnetic annealing temperature is 10
It has the effect that it is possible to lower the temperature by about 0 ° C, the characteristic deterioration due to strain is small, and the required magnetic characteristics can be exhibited even when it is used as a structural member such as a shield room. It is an invention that has a great effect industrially because it can respond promptly to the demands of the electronics industry.

Claims (4)

[Claims] 1. Ni: 77.5 to 79.5 wt%, Mo: 3.8 to 4.6 wt%, Cu: 1.8 to 2.5 wt%, Mn: 0.1 to 1.10 wt% P: 0.010 to 0.080 wt%, Si: less than 0.20 wt% , S: 0.0020 wt% or less, O: 0.0030 wt% or less, N: 0.0010 wt% or less, C: 0.020 wt% or less, and Contained within the range of, and the balance basically consists of Fe, and Ni, Mo, Cu, Mn, Fe (However, the content in [] is wt%).
-Fe-based high-permeability magnetic alloy. 2. Ni: 77.5 to 79.5 wt%, Mo: 3.8 to 4.6 wt%, Cu: 1.8 to 2.5 wt%, Mn: 0.1 to 1.10 wt%, P: 0.010 to 0.080 wt%, Si: 0.2 to 1.0 wt%, S: 0.0020 wt% or less, O: 0.0030 wt% or less, N: 0.0010 wt% or less, C: 0.020 wt% or less, and Contained within the range of, and the balance basically consists of Fe, and Ni, Mo, Cu, Mn, Fe (However, the content in [] is wt%).
-Fe-based high-permeability magnetic alloy. 3. The B having the composition as defined in claim 1, and B at the austenite grain boundary and its vicinity after magnetic annealing.
Ni-Fe based high permeability magnetic alloy, characterized in that the amount is 10 to 50 atm%. 4. A Ni—Fe-based high permeability having the composition of claim 2 and having a B content of 10 to 50 atm% at and near the austenite grain boundaries after magnetic annealing. Magnetic susceptibility magnetic alloy.