Method for making an Fe-based alloy ribbon with a thickness of not more than 10 micrometer

Abstract: In the production by the single-roll technique of a thin amorphous strip as the matrix for the manufacture of a thin Co-based amorphous alloy strip or a thin Fe-based microcrystalline alloy strip, the conditions for the production are controlled to those specified by the invention. The production conditions thus controlled concern the atmosphere and the pressure to be used for ejecting a molten metal onto a rotating cooling member, the shape of a nozzle, the distance between the nozzle and the rotary cooling member, the material for the rotary cooling member and peripheral speed of the rotary cooling member, etc. The individual numerical values of these conditions are severally important. The thin strips thus obtained are in an extremely small thickness and in a wholesome state destitute of pinholes and other similar defects. In the thin Co-based amorphous alloy strip, the extreme decrease of thickness to below 4.8 µm notably enhances the soft magnetic properties such as permeability and core loss in the high frequency range. In the thin Fe-based microcrystalline alloy strip, the extreme decrease of thickness not more than 10 µm permits improvement of resistance to embrittlement in addition to the improvement in the soft magnetic properties.

Description: This invention relates to a method for the production of a very thin soft magnetic alloy strip suitable for use in a noise filter, a saturable reactor, a miniature inductance element for abating spike noise, main transformer, choke coil, a zero-phase current transformer, a magnetic head, etc., namely the devices which are expected to exhibit high levels of permeability at high frequencies, a very thin soft magnetic alloy strip by the use of the method, and an apparatus for the production of a soft magnetic alloy strip. In recent years, the trend of electronic equipments and devices toward reduction in size and weight and enhancement of performance has been urging magnetic parts serving as important functional parts to embody highly advanced improvements. The magnetic materials to be used in such magnetic parts, as a natural consequence, are urged to possess outstanding magnetic properties. Particularly, materials of high permeability are effective in numerous magnetic parts such as current sensors in zero-phase current transformers and noise filters, for example. In the case of a noise filter, for example, a switching power source is widely used as a stabilizing power source for electronic equipments and devices. In the switching power source, adoption of a measure for the abatement of noise constitutes itself an important task. The high-frequency noise including a switching frequency as its basic frequency and the noise of the MHz range issuing from a load such as, for example the logic circuit of a personal computer pose a problem. For the abatement of the conducted noise of this kind, therefore, a common mode choke coil has found acceptance for use as a noise filter. When this filter is inserted in a power source line, the magnitude of the noise output voltage relative to the noise input voltage has such bearing on the permeability of a magnetic core that the noise output voltage decreases in proportion as the permeability increases. Further, the filter is required to function effectively not only in the low frequency range but equally in the high frequency range exceeding 1 MHz. For this reason, the frequency characteristic of the permeability is required to be favorable as well. In recent years, the switching power source of the kind incorporating a magnetic amplifier has been finding widespread utility. The main component in the magnetic amplifier is a saturable reactor and is claimed to require a magnetic core material excelling in the angular magnetization characteristic. The aforementioned trend of recent electronic machines and devices toward reduction in size and weight and enhancement of quality performance has been strongly urging switching power sources to attain generous reduction in size and weight. For the realization of the reduction in size and weight, there has been expressed a desire to heighten the switching frequency as much as possible. In the circumstances, the magnetic core material as one of the component parts of the saturable reactor is strongly desired to suffer from as small loss in the high frequency range as possible. A proprietary product (by trademark designation) made of a Fe-Ni crystalline alloy and found utility to date is far short of fitting use in the high frequency range because it suffers from a notably increase of eddy-current loss in a high frequency range exceeding 20 kHz. The magnetic core material using an amorphous alloy capable of exhibiting a low core loss and a high angular shape ratio in the high frequency range is actually used only in a frequency range approximately in the range of 200 to 500 kHz because it entails an increased core loss in the MHz range. Generally, in the case of metallic materials, it has been known that the core loss can be curbed and the high-frequency characteristic improved by decreasing the plate thickness. Even in the case of amorphous alloys, the feasibility of decreasing the plate thickness is being studied. Thin amorphous alloy strips are generally manufactured by the liquid quenching method which resorts to the single roll technique. Under the conventional production condition, in the case of Co-based amorphous alloy, the thickness of 6 µm could be obtained by the single roll technique in vacuum [ J.Appl, Phys. 64 6050, etc. ]. However, it was thought that it was substantial impossible to make the thickness thinner than 5 µm. These thin strips contain relatively numerous pinholes because they entrain bubbles with themselves during the reduction of plate thickness and , therefore, pose problems on practicability as well as adaptability for higher frequency. For perfect realization of a switching frequency in the MHz range, the desirability of further decreasing the plate thickness has been finding enthusiastic recognition. However, it was thought that this desire could not be realized practically. Recently, a Fe-based microcrystalline alloy possessing a practically equal soft magnetic property as amorphous alloys has been reported [EPO Publication No. 0271657, Japanese patent Publication SHO 63(1988)-320,504, etc.]. This alloy is produced by causing a Fe-Si-B type alloy, for example, to incorporate therein Cu and one element selected from among Nb, W, Ta, Zr, Hf, Ti, Mo, etc., forming the resultant alloy tentatively as a thin strip similarly to any amorphous alloy, and thereafter heat-treating the thin amorphous strip in a temperature range exceeding the crystallizing temperature thereof thereby inducing formation of ultrafine crystalline grains. Even in the case of the Fe-based microcrystalline alloy of the nature described above, for the purpose of improving the high frequency property by decreasing the plate thickness thereby effecting crystallization of a thin strip of amorphous alloy, it is necessary that the thin amorphous strip should be produced in a fine state destitute of a pinhole. The existing manufacturing technique such as of the single-role principle, however, has never been successful in turning out a product fully conforming with the recent trend toward higher frequency. Further, since in the case of the Fe-based microcrystalline alloy microcrystalline grains are formed, the thin strip is brittle. Therefore, from quality point of view, it entails the important problem that it tends to sustain chipping and other similar defects during the process of manufacture as like core making. Likewise from this point of view, the desirability of further decreasing the thickness of the strip of amorphous alloy thereby improving the brittleness has been finding growing recognition. J. Appl. Phys. 64(10), 15 November 1988, pages 6050-6052 discloses the production of Co-based amorphous ribbons having a thickness of 6-10 µm. As described above, the magnetic material for various kinds of magnetic cores is expected to manifest high permeability and low core loss at varying levels of frequency up to the high frequency range (to MHz range). This requirement leads electronic machines and devices toward further improvement of efficiency and further reduction in size and weight and magnetic cores toward reduction of size and improvement of quality. An object this invention, therefore, is to provide a method for the production of an extremely thin amorphous alloy strip which fulfills the magnetic properties mentioned above and maintains a fine state destitute of such defects as pinholes. Another object of this invention is to provide a method for producing an extremely thin amorphous alloy strip which is capable of manifesting high permeability and low core loss in varying levels of frequency up to the high frequency range (to MHz range). A further object of this invention is to provide a method for the production of an extremely thin Fe-based microcrystalline alloy strip which fulfills the magnetic properties mentioned above and maintains a fine state destitute of such defects as pinholes. Yet another object of this invention is to provide a method for producing an extremely thin amorphous alloy strip which is capable of manifesting high permeability and low core loss in varying levels of frequency up to the high frequency range (to MHz range) and which exhibits enhanced resistance to embrittlement. Still another object of this invention is to provide a method for the production of a thin soft magnetic alloy strip which fulfills the magnetic properties mentioned above and maintains a fine state destitute of such defects as pinholes. The present invention is directed to a method for the production of an extremely thin soft magnetic alloy strip and an alloy strip produced by the method. Thus, the present invention is defined by claim 1. As described, this method involves the following process conditions: (1) A reduced pressure of not higher than 1.33Nm -2 (10 -2 Torr) or an He atmosphere of a pressure of not higher than 8000Nm -2 (60 Torr) should be used for the atmosphere in which the molten alloy ejected through the nozzle travels until it impinges on the rotating cooling member. (2) The nozzle should be provided with an orifice of a rectangular cross section, the short side of which lying parallelly to the circumferential direction of the rotary cooling member should possess a length of not more than 0.20mm. (3) The distance between the nozzle and the rotary cooling member should be not more than 0.2mm. (4) The pressure to be used for ejecting the molten alloy onto the rotary cooling member should be not more than 0.03 kg/cm 2 . (5) The peripheral speed of the rotary cooling member should be not less than 20 m/sec. (6) the molten alloy is rapidly quenched to produce an extremely thin strip, and then the quenched strip is heat-treated at temperature of not lower than the crystallizing temperature of the used alloy, said strip containing microcrystallin grains having a diameter of not more than 100 nm (1000 Å). By above mentioned method, it is made possible to provide a thin Fe-based microcrystalline alloy strip having a thickness of not more than 10 µm and consequently conforming with the trend toward higher frequency and having educed therein ultrafine crystalline grains of a diameter of not more than 1,000 Å. The alloy to be used for the production of the aforementioned thin Fe-based soft magnetic alloy strip has a composition essentially represented by the following general formula: Fe 100-e-f-g-h-i-j E e G f J g Si h B i Z j [wherein E stands for at least one element selected from the class consisting of Cu and Au, G for at least one element selected from the class consisting of the elements of Group IVa, the elements of Group Va, the elements of Group VIa, and rare-earth elements, J for at least one element of selected the class consisting of Mn, Al, Ga, Ge, In, Sn, and the platinum-group elements, Z for at least one element selected from the class consisting of C, N, and P, and e, f, g, h, i, and j for numbers satisfying the following formulas, 0.1 ≦ e ≦ 8, 0.1 ≦ f≦ 10, 0 ≦ g ≦ 10, 12 ≦ h ≦ 25, 3 ≦ i ≦ 12, 0≦ j ≦ 10, and 15 ≦ h+i+j ≦ 30 All numerical values in these formulas are represented by at % ]. In accordance with the method of this invention for the production of a very thin soft magnetic alloy strip, a thin Co-based amorphous alloy strip possessing a thickness of less than 4.8 µm, or a thin Fe-based microcrystalline alloy strip possessing a thickness of not more than 10 µm is obtained as described above. Since these alloy strips exhibit excellent soft magnetic properties such as permeability and core loss in the high frequency range, they can be offered as magnetic materials for use in a noise filer, a saturable reactor, a miniature inductance element for the abatement of spike noise, main transformer, choke coil, a zero-phase current transformer, a magnetic head, etc. which invariably demand excellent soft magnetic properties to be exhibited in the high frequency range. In the case of the thin-Fe-based microcrystalline alloy strip, the phenomenon of embrittlement can be improved by having the plate thickness decreased below 10 µm. Fig. 1 is a diagram illustrating in model a typical construction of the apparatus for the production a thin soft magnetic alloy strip used in one embodiment of the present invention, Fig. 2 is a diagram illustrating the shape of a nozzle for the apparatus from a bottom end view, Fig. 3 is a diagram illustrating the nozzle and the cooling roll, Fig. 4 is a graph showing the frequency characteristic of the initial permeability of a thin Fe-based microcrystalline alloy strip produced in yet another embodiment of this invention, as compared with that of the conventional countertype. Now, the present invention will be described more specifically below with reference to working examples. Now, the first aspect of this invention, namely the method for the production of an extremely thin soft magnetic alloy strip will be described in detail below. Fig. 1 is a diagram illustrating the construction of an apparatus for the production of a thin soft magnetic alloy strip embodying the method of this invention for the production of a thin soft magnetic alloy strip. With reference to this diagram, a vacuum chamber 10 is provided with a supply system 12 and a discharge system 14. Inside this vacuum chamber 10, a single-roll mechanism 40 consisting mainly of a cooling roll 20 capable of being cooled to a prescribed temperature and controlled to a prescribed peripheral speed and a raw material melting container 30. In the lower part of the raw material melting container 30 is disposed a nozzle 32 which opens in the direction of a peripheral surface 32 of the cooling roll 20. The shape of the orifice of this nozzle 32 is rectangular as illustrated in Fig. 2. The short side of the rectangular cross section of the orifice falls parallelly to the circumferential direction of the cooling roll 20. The long side a and the short side b of the orifice of the nozzle 32 are to be set in accordance with the particular raw material to be used. As showed in Fig. 3, the nozzle 32 are set so the appropriate distance c between the nozzle 32 and the peripheral surface 22 of the working roll 20 can be formed. This distance c can be varied depending on the particular raw material to be used. The angle of ejection onto the cooling roll 20 is not limited to 90°. An induction heating coil 34 is disposed on the outer periphery of the raw material melting container 30 and is used for melting the raw material to be introduced. The molten raw material is ejected through the nozzle 32 onto the peripheral surface 22 of the cooling roll 20. A method for the production of an extremely thin Fe-based microcrystalline soft magnetic alloy strip, will now be described. The apparatus used for this production was configured similarly to the apparatus of production illustrated in Fig. 1. The conditions for manufacture were different. First, the raw materials for a Fe-based alloy composition represented by the aforementioned formula: Fe 100-e-f-g-h-i-j E e G f J g Si h B i Z j was placed in the raw material melting container 30 and melted therein. Then, E (Cu or Au) in the aforementioned formula (II) represents an element effective in heightening the corrosion-resistance, preventing crystalline grains from being coarsened, and improving the soft magnetic properties such as core loss and permeability. It is particularly effective in the precipitation of the bcc phase at low temperatures. If the amount of this element is unduly small, the effects mentioned above are not obtained. Conversely, if this amount is unduly large, the magnetic properties are degraded. Suitably, therefore, the content of E is in the range of 0.1 to 8 atomic %. Preferably, this range is from 0.1 to 5 atomic %. G (at least one element selected from the class consisting of the elements of Group IVa, the elements of Group Va, the elements of Group VIa, and the rare-earth elements) is an element for effectively uniformizing the diameter of crystalline grains, diminishing magnetostriction and magnetic anisotropy, improving the soft magnetic properties, and also improving the magnetic properties against temperature changes. The combined addition of G and E (Cu, for example) allows the stabilization of the bcc phase to be attained over a wide range of temperature. If the amount of this element, G, is unduly small, the aforementioned effects are not attained. Conversely, if this amount is unduly large, amorphous phase can not be obtained during the course of manufacture and, what is more, the saturated magnetic flux density is unduly low. The content of G, therefore, is suitably in the range of 0.1 to 10 atomic %. Preferably, this range is from 1 to 8 atomic %. As concerns the effects of a varying element as E, in addition to the effects mentioned above, the elements of Group IVa are effective in widening the ranges of conditions of the heat treatment for the attainment of the optimum magnetic properties, the elements of Group Va are effective in improving the resistance to embrittlement and improving the workability as for cutting, and the elements of Group VIa are effective in improving the corrosionresistance and improving the surface quality. Among other elements mentioned above, Ta, Nb, W, and Mo are particularly effective in improving the soft magnetic properties and V is conspicuously effective in improving the resistance to embrittlement and the surface quality. These elements are, therefore, constitute themselves preferred choices. J (at least one element selected from the class consisting of Mn, Al, Ga, Ge, In, Sn, and the platinum-group elements) is an element effective in improving the soft magnetic properties or the corrosion resistant properties. If the amount of this element is unduly large, the saturated magnetic flux density is not sufficient. Thus, the upper limit of this amount is fixed at 10 atomic %. Among other elements of this class, Al is particularly effective in promoting fine division of crystalline grains, improving the magnetic properties, and stabilizing the bcc phase, Ge is effective in assisting the bcc phase, and the platinum-group elements is effective in improving the corrosion resistant properties. Si and B are elements effective in obtaining amorphous phase during the course of manufacture, improving the crystallizing temperature, and promoting the heat treatment for the improvement of the magnetic properties. Particularly, Si forms a solid solution with Fe as the main component of microcrystalline grains and contributes to diminishing magnetostriction and magnetic anisotropy. If the amount of Si is less than 12 atomic %, the improvement of the soft magnetic properties is not conspicuous. If this amount exceeds 25 atomic %, the rapidly quenching effect is not sufficient, the educed crystalline grains are relatively coarse on the order of µm, and the soft magnetic properties are not satisfactory. Further, Si is an essential element for the construction of a order phase. For the appearance of this order phase lattice, the content of Si is preferably in the range of 12 to 22 atomic %. If the content of B is less than 3 atomic %, the educed crystalline grains are relatively coarse and do not exhibit satisfactory properties. If this content exceeds 12 atomic %, B is liable to form a compound of B in consequence of the heat treatment and the soft magnetic properties are not satisfactory. Optionally, as an element for promoting the conversion of the crystalline phase of the thin strip to the amorphous texture, Z (C, N, or P) may be contained in the alloy composition in an amount of not more than 10 atomic %. The total amount of Si, B, and the element contributing to the conversion into the amorphous texture is desired to be in the range of 15 to 30 atomic %. For the acquisition of highly satisfactory soft magnetic properties, Si and B are desired to be sued in such amounts as to satisfy the relation, Si/B≧1. Particularly when the content of Si is in the range of 13 to 21 atomic %, the diminution of magnetostriction, λs, close to 0 is attained, the deterioration of the magnetic properties by resin mold is eliminated, and the outstanding soft magnetic properties aimed at are effectively manifested. The effect of this invention is not impaired when the Fe-based soft magnetic alloy mentioned above contains in a very small amount such unavoidable impurities as O and S which are contained in ordinary Fe-based alloys. Then, after the vacuum chamber 10 has been evacuated to a reduced pressure of not higher than 1.33Nm -2 (10 -2 Torr) or filled with a He atmosphere of not higher than 8000NM -2 (60 Torr), the molten alloy composition is ejected under a pressure of 0.03 kg/cm 2 through the nozzle 32 onto the peripheral surface of the cooling roll 20 operated at a controlled peripheral speed of not less than 20 m/sec, to quench the molted metal and produce a thin amorphous strip 40. The reason for setting the upper limit of the reduced pressure or the pressure of the atmosphere of inert gas at 10 -2 Torr or 60 Torrs is that particularly in the production of a thin strip of a large width exceeding 1.5 mm, the thin strip having a sufficient small thickness, excelling in surface quality, and containing no pinhole is obtained when the upper limit is not surpassed. If this upper limit is surpassed, the produced thin strip acquires a laterally undulating surface, abounds with pinholes, and fails to acquire a thickness of not more than 10 µm. The peripheral speed is required only to exceed 20 m/sec. In view of the facility of manufacture of the thin strip, however, this peripheral speed is desired to be not more than 50 m/sec. Then, the pressure for the ejection of the molten alloy is required only not to exceed 0.03 kg/cm 2 , desirably not more than 0.025 kg/cm 2 , and more desirably not more than 0.02 kg/cm 2 . If this pressure is less than 0.001 kg/cm 2 , the ejection of the molten metal is not easily attained. The cooling roll 20 is desired to be made of a Cu-based alloy (such as, for example, brass). Where the plate thickness of the thin strip to be produced is not more than 8 µm, the cooling roll 20 may be made of a Fe-based alloy. The cooling roll made of this material allows the produced thin strip to acquire improved surface quality and fine quality. The long side a of the rectangular cross section of the orifice of the nozzle 32 determines the width of the produced thin strip. It is required only to exceed 2 mm. The short side b constitutes itself an important value for determining the plate thickness of the thin strip. For the sake of the production of this thin strip in an extremely small thickness of not more than 0.15 mm, the value of b is desired to be not more than 0.2 mm, preferably not more than 0.15 mm. In due consideration of the ejectability of the molten metal, however, the value of b is desired to be not less than 0.07 mm. The distance c between the leading end of the nozzle 32 and the cooling roll 20 is not more than 0.2 mm. The reason for this upper limit is that the strip is not easily obtained in an extremely small thickness if this distance exceeds 0.20 mm. If this distance c is unduly small, the produced thin strip suffers from inferior surface quality. Thus, the distance is desired to be not less than 0.05 mm. By quenching the molten metal faithfully under the conditions described above, the thin strip 40 of an amorphous state is obtained in a thickness of not more than 10 µm. Where the thin Fe-based microcrystalline alloy strip is to be produced thereafter, the thin amorphous layer obtained as described above is subjected to a heat treatment at a suitable temperature exceeding the crystallizing temperature of the amorphous alloy for a period in the range of 10 minutes to 15 hours. This heat treatment allows the thin amorphous strip to effect precipitation of not more than 1000 Å microcrystalline grains and acquire improved magnetic properties. Optionally, the thin Fe-based microcrystalline alloy strip may be given an additional heat treatment in the presence of a magnetic field (in the direction of the axis of the thin strip, the direction of the width, the direction of the thickness, or in the rotary magnetic field). The kind of the atmosphere in which this heat treatment is carried out is not critical. The heat treatment effectively proceeds in the insert gas such as N 2 or Ar, in the vacuum, in the reducing atmosphere such as of H 2 , or in the ambient air, for example. The microcrystalline grains not more than 1,000 Å in diameter present in the thin Fe-based microcrystalline alloy strip obtained as described above are desired to be such that they exist therein in an area ratio in the range of 25 to 95%. If the area ratio of the microcrystalline grains is unduly small, namely if the area ratio of the amorphous is unduly large, the core loss is large, the permeability low, and the magnetostriction large. Conversely, if the area ratio of the microcrystalline grains is unduly large, the magnetic properties are unsatisfactory. The preferable ratio of presence of the microcrystalline grains in the alloy is in the range of 40 to 90% as area ratio. Within this range, the soft magnetic properties are obtained particularly stably. The reason for setting the upper limit of the thickness of the thin Fe-based microcrystalline alloy strip at 10 µm is that the magnetic properties in the high frequency range such as of MHz are highly satisfactory and the resistance to embrittlement is improved when this upper limit is observed. The improvement of the resistance to embrittlement is prominent when the thickness is restricted below 8 µm. Now, the production of the thin Fe-based microcrystalline alloy strip will be described specifically below with reference to typical examples. Example 4: An alloy composition represented by the formula, Fe 72 Cu 1 V 6 Si 13 B 8 , was prepared, placed in the raw material melting container, and melted therein. The nozzle used herein had a rectangular orifice measuring 5.2 mm x 0.15 mm (a x b). The distance c between the nozzle and the cooling roll was 0.15 mm. The cooling roll was made of a Cu alloy. Then, after the vacuum chamber had been evacuated to 5 x 10 -5 Torr, the molten alloy composition was ejected under a pressure of 0.025 kg/cm 2 through the nozzle onto the peripheral surface of the cooling roll operated under a controlled peripheral speed of 42 m/sec, to quench the molten metal and obtain a thin strip. The thin strip thus obtained measured 5 mm in width and 7.8 µm in thickness and possessed an amorphous state. Then, the thin strip was wound in a toroidal core with 12 mm outermost diameter and 8mm inner diameter). This core was subjected to a heat treatment in an atmosphere of N 2 at 570°C for two hours. The core after the heat treatment was tested for core loss, and frequency characteristic of initial permeability by the use of a U function meter and a LCR meter. Fig. 4 shows the frequency characteristic of the initial permeability in an excited magnetic field of 2mOe. For comparison, the results similarly obtained of a thin Fe-based microcrystalline alloy strip using the same alloy composition and possessing a thickness of 18 µm are shown in the diagram. It is clearly noted from the diagram that the effect of plate thickness on permeability appeared conspicuously at a high frequency exceeding 100 kHz. The test results on core loss where as shown in Table 1 below, indicating the extreme decrease in plate thickness was evidently effective. Plate thickness (µm) Core loss (mW/cc) f=100kHz B=2kG f=1MHz B=1kG Example 4 7.8 80 1350 Comparative Experiment 4 18 350 4600 The thin Fe-based microcrystalline alloy strips of Example 4 and Comparative Experiment 4 were subjected to a bending test. This test was carried out by disposing a given thin heat-treated Fe-based microcrystalline alloy strip in a bent state between two plates, narrowing the distance between the two plates until the bent sample broke, measuring the distance, ℓ, between the two plates at the time of breakage of the sample, and calculating the following formula using the found distance . ε = t ℓ - t (wherein t stands for the average thickness of the sample thin strip by gravimetric method based on weight / density x length x width ). The value resulting from the calculation was ε = 5 x 10 -3 for the thin Fe-based microcrystalline alloy strip of Example 4 and ε = 2 x 10 -4 for that of Comparative Experiment 4. This fact clearly indicates that the resistance to embrittlement was improved by the extreme decrease of plate thickness. ε is not less than 1 x 10 -3 , preferably not less than 3 x 10 -3 . Example 5: Thin amorphous strips were produced by following the procedure of Example 4, excepting varying alloy compositions indicated in Table 2 were used instead and the conditions of production were varied as indicated in Table 2. Then, the thin strips were wound to produce cores and the cores were heat-treated similarly. It is clearly noted form Table 2 that thin Fe-based microcrystalline alloy strips of fine quality measuring not more than 10 µm in thickness and containing few pinholes were obtained by first preparing thin strips of an amorphous state under the conditions invariably falling in the ranges specified by this invention and then heat-treating these thin amorphous strips. It is also clear that they satisfied the requirements for low core loss and high permeability in the high frequency range.

Claims: A method for the production of a Fe-based thin soft magnetic alloy strip having a thickness of not more than 10 µm, characterised by the fact that a molten alloy is ejected through a nozzle onto the surface of a rotating cooling member under an ejecting pressure of not higher than 0.03 kg/cm 2 in atmosphere of reduced pressure of not higher than 1.33Nm -2 (1 x 10 -2 Torr) or in a He atmosphere of reduced pressure of not higher than 8000Nm -2 (60 Torr), thereby rapidly quenching said ejected molten alloy to produce said strip, wherein said nozzle is provided with an orifice of a rectangular cross section, the short side of which falling parallelly to the peripheral direction of said rotary cooling member is set at or below 0.2 mm, the distance between said nozzle and said rotary cooling member is set at or below 0.2 mm, and said rotary cooling member is rotated at a peripheral speed of not less than 20m/sec, and then said thin strip is subjected to a heat treatment at a temperature exceeding the crystallizing temperature of the alloy used, said strip containing microcrystalline grains having a diameter of not more than 100 nm (1,000Å). A method according to claim 1, wherein said rotary cooling member is made of a Cu-based alloy. A method according to claim 1, wherein the thickness of said thin Fe-based alloy strip is not more than 8 µm. A method according to any of claims 1 to 3, wherein said thin Fe-based soft magnetic alloy strip to be produced has an alloy composition substantially represented by the general formula Fe 100-e-f-g-h-i-j E e G f J g Si h B i Z j , wherein E stands for at least one element selected from the group consisting of Cu and Au, G for at least one element selected from the group consisting of the elements of Group IVa, the elements of Group Va, the elements of Group VIa, and the rare-earth elements, J for at least one element selected from the group consisting of Mn, Al, Ga, Ge, In, Sn, and the platinum-group elements, z for at least one element selected from the group consisting of C,N and P and e, f, g, h, i, and j for an atomic % satisfying 0.1 < e < 8,0.1 < f < 10,0 < g < 10, 12 < h < 25,3 < 1 < 12,0 < j < 10, and 15 < h+i+j < 30.

Inventors: SAWA TAKAO, YAGI MASAAKI, SAWA, TAKAO, YAGI, MASAAKI, SAWA, TAKAO, C/O PATENT DIVISION
Applicants: TOSHIBA KK, YAGI MASAAKI, KABUSHIKI KAISHA TOSHIBA, YAGI, MASAAKI
Application year: 1989
Main classification: H01F1
IPC codes: B22D11, H01F1, H01F41