US3843424A - Normal grain growth(110)(001)textured iron-cobalt alloys - Google Patents

Normal grain growth(110)(001)textured iron-cobalt alloys Download PDF

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US3843424A
US3843424A US00228071A US22807172A US3843424A US 3843424 A US3843424 A US 3843424A US 00228071 A US00228071 A US 00228071A US 22807172 A US22807172 A US 22807172A US 3843424 A US3843424 A US 3843424A
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cobalt
alloy
iron
silicon
alloys
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US00228071A
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D Thornburg
K Foster
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CBS Corp
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Westinghouse Electric Corp
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Priority to BE795762D priority Critical patent/BE795762A/xx
Application filed by Westinghouse Electric Corp filed Critical Westinghouse Electric Corp
Priority to US00228071A priority patent/US3843424A/en
Priority to CA161,434A priority patent/CA988752A/en
Priority to GB622973A priority patent/GB1420371A/en
Priority to DE19732307929 priority patent/DE2307929A1/de
Priority to JP48019839A priority patent/JPS4897722A/ja
Priority to FR7306322A priority patent/FR2173187B1/fr
Priority to IT41530/73A priority patent/IT976647B/it
Priority to US480075A priority patent/US3892604A/en
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1227—Warm rolling

Definitions

  • NORMAL GRAIN GROWTH (110) [001] TEXTURED IRON-COBALT ALLOYS Filed Feb. 22, 1972 4 Sheets-Sheet 4 United States Patent O1 fice 3,843,424 Patented Oct. 22, 1974 3,843,424 NORMAL GRAIN GROWTH (110) [001] TEXTURED IRON-COBALT ALLOYS Donald R. Thornburg and Karl Foster, Pittsburgh, Pa.,
  • the present invention relates to iron-cobalt alloys having improved magnetic characteristics and a method for producing said alloys.
  • the alloys are characterized by having a high grain volume of (110) ][001] orientation texture, the same having been derived by means of primary recrystallization and normal grain growth.
  • the alloys containing from about 35 to 50% cobalt have a low magnetocrystalline anisotropy and the lowest values occur in the range of about 50% cobalt. Consequently, high inductions are obtained at low field strengths.
  • the cobalt content in the alloy is increased to a value ranging from more than about 35% and up to about 80% by weight, with a corresponding decrease in the iron content, the alloy undergoes atomic ordering. Consequently, high cobalt-iron alloys such as the 50% cobaltiron alloy are quite brittle and can only be cold worked after a drastic quench resulting in high production costs.
  • the present invention relates to an alloy which contains in weight percent between about 5% and about 35% cobalt, up to about 2% chromium, up to about 1% manganese, up to about 3% silicon and the balance iron with incidental impurities.
  • a critical aspect of the invention is recognizing and controlling the sulfur content thereof to a value of less than about 0.005% and preferably less than about 0.002%.
  • the method for obtaining the improved magnetic characteristics in these alloy compositions includes an initial step of hot working of the metal at a temperature of between about 1000 C. and about 1100 C. to a desired intermediate gauge and thereafter a critical cold working the alloy in one or more steps to the desired final gauge and a final critical primary recrystallization anneal. While any hot working will suffice since it is not a critical point in the process, hot rolling is preferred.
  • the alloy is preferably heated rapidly to the recrystallization temperature and finally subjected to a high temperature heat treatment which results in the development of a primarily recrystalliZed microstructure having a majority of the grains displaying an orientation described as [001] in Miller Indices, and the majority or a high proportion of the grains have the cube edges of their crystal lattices parallel within 10 to the direction of rolling of the sheet or strip of the alloy.
  • the final high temperature heat treatment to which the alloy is subjected usually takes place at a temperature between about 800 C. and the A temperature of the alloy undergoing the final heat treatment.
  • the final heat treatment is conducted in a protective atmosphere, such as an atmosphere of substantially pure hydrogen having a dew point of less than about 40 F.
  • the present invention relates to an alloy having improved magnetic characteristics, and which has a composition containing from about to about 35% cobalt, at least one element which is effective for raising the volume resistivity such as up to about 2% chromium, and up to about 3% silicon, less than about 0.005% sulfur, up to about 1% manganese, and the balance essentially iron with incidental impurities.
  • the alloy in its fabricated form is characterized by having a primarily recrystallized-grain structure in which a majority of the grains possess a (110) [00 1] texture.
  • a preferred embodiment contains between about 8% and about 20% cobalt, from about 0.5% to about 2.0% silicon, a sulfur content of less than about 0.005% and the balance iron with incidental impurities.
  • Another preferred composition contains cobalt within the range between about 20% and about 30%, chromium within the range between about 0.25% and about 1%, less than about 0.005% sulfur and the balance essentially iron with the normal impurities.
  • Outstanding results have been obtained where the cobalt content is maintained within the range between about 26.5% and about 28%, from about 0.25% to about 0.75% chromium, less than about 0.002% sulfur and the balance iron with incidental impurities.
  • This latter compositional range has improved magnetic characteristics including a high saturation value, as well as high inductions at low field strengths thereby resulting in an outstanding combination of magnetic characteristics.
  • Excellent magnetic materials have also been obtained where the cobalt content is maintained within the range betwe n about 10% and about 18% cobalt, from about 0.5% and about 2.0% silicon, less than about 0.0025% sulfur with the balance being essentially iron with incidental impurities. While ttu's latter alloy will have greater resistivity from the standpoint of the inclusion of the silicon content and slightly lower saturation induction values, nonetheless thedegree of orientation is outstanding so as to given exceedingly high B value which is a measure indicative not only of the degree of orientation but also is indicative of the attainment of high inductions at low field strengths. Consequently, the various combina tions of magnetic characteristic obtainable in each of the ranges set forth. hereinbefore together with the simplified processing for obtaining these desirable results makes the same quite economically attractive compared with commercially available oriented 3% silicon-iron.
  • the alloy of the present invention must be critically controlled with respect to the sulfur content. In this respect. it has been noted that the majority of the grains will developthe required degree of orientation provided the initial sulfur content within the melt is limited to about 0.005% maximum. As will be set forth more fully hereinafter no special desulfurizing heat treatments are performed during the manufacture of the alloy to its desired finished gauge product. Accordingly, it becomes exceedingly important and in fact critical to maintain the sulfur content at less than about .005 and preferably less than about 0.0025 Exceedingly good results have been obtained where the sulfur content has been limited to a value notin excess of about 0.002%
  • silicon is not added as a deliberate alloying element, as for example, where the cobalt content is maintained within the range between about 20%. and about 35%., it is desirable to have the silicon content at a value of less than about 0.25%. While silicon is noted for its effect of improving volume resistivity it has been found that other elements such as chromium, vanadium, aluminum, titanium and molybdenum are more effective where the cobalt content is within the range between 20 and 35%. Consequently, the alloying silicon addition is preferred only where the cobalt is less than about 20%. Any element which is soluble and does not form a'second phase will improve volume resistivity; however care must be exercised so that the other properties are not detrimentally afiected.
  • the manganese content it has also been found that it is preferred, although not critically necessary, to have the manganese content at a value of less than about 0.50%. Where, however, silicon is added as an alloying component, for example, in an alloy with a cobalt content of between 8% and 20% for improved resistivity, the manganese may be quite lownominally about 0.05%.
  • the alloy While during normal processing of the alloys into finished gauge material the alloy may be subjected to a decarburizing anneal, nonetheless it is preferred to maintain the carbon content at less than about 0.030% with a correspondingly low content of oxygen and the balance of the other incidental impurities.
  • Typical levels of these elements may include about 0.003% oxygen, about 0.05% manganese, about 0.1% silicon and the balance essentially of iron.
  • Such levels of incidental impurities are ob tained by vacuum induction melting; however other melting methods may be employed with equal success.
  • the alloy having the desired composition is subjected to a hot working operation and one or more cold working operations in order to reduce the alloy to the desired final gauge thicknessl'n this respect it has been found that good success has been obtained where the alloy in ingot form is hot worked as by rolling from a temperature within the range between about 1000 C. and about 1100" C.
  • the material is hot worked at this temperature range to any desired'intermediate gaugethickness such as a hot rolled band gauge of between about 0.075 and about 0.150 inches.
  • any desired'intermediate gaugethickness such as a hot rolled band gauge of between about 0.075 and about 0.150 inches.
  • the alloy is heat treated for a time period of about 10 minutes to about 60 minutes at a temuperature within the range between about 600 and 900 C.
  • a hydrogen atmosphere such hydrogen atmosphere having a dew point of greater than about -40 F. in order to decarburize the material. It is desired in some cases to decarburize at the intermediate g auge thickness and typical annealing times of about 15 minutes at about 700 C. in a hydrogen atmosphere at approximately a +60 F. dew point is effective for removing about half of the carbon content remaining in the sample following hot working.
  • decarburizing heat treatment can be delayed to just prior to final heat treatment or cut any other step therebetween. After .the decarburizing anneal, the material is pickled in preparation for cold working.
  • Cold working is accomplished in one or more operations. Preferably, the cold working is accomplished in two steps. However, it has been found that it is necessary that at least the last cold working of the material to finish gauge must effect a reduction in the cross sectional area ranging between about 40% and about 75%. In this respect it has been noted that where the final cold reduction is less than about 40% a sharply defined [001] texture is not obtained as where the material has been subjected to at least a 40% reduction in cross sectional area. While reductions in excess of 75% will not adversely affect the final texture to any marked degree, nonetheless some deterioration has been noted and the degree of recrystallization may be some-what affected thereby. Consequently it has been found desirable to limit the cold reduction to finish gauge to avalue between about 40% and about 75% and outstanding results have been obtained where the final cold reduction has been effected in an amount ranging between about 50% and about 60%.
  • the initial cold reduction if more than onecold rdeuction stage ,is contemplated, may be effected by means of a hot-cold working. That is, the material may be heated to a temperature above ambient temperature but at a temperature below the temperature at which spontaneous recrystallization takes place during working. Thus while the material will be warmed well above room temperature it will nonetheless be a cold working and hence has been termed hotcold working.
  • warm rolling may be effected at a temperature within the range between about 200 C. and about 300 C.
  • the material is permitted to cool to ambient temperature where it is then further cold rolled to about 0.025 inch.
  • the total reduction from hot rolled band thickness in the first cold rolling stage is effective for reducing the cross sectional area about 75%.
  • an intermediate anneal is preferably employed, said intermediate anneal being conducted for -a time period of up to about two hours at a temperature in excess of about 800 C.
  • such intermediate anneal is performed in an atmosphere of pure dry hydrogen, that is, a hydrogen content having a dew point of less than about 40 F.
  • the preferred mode of processing includes a strip anneal for five minutes at 800 C. followed by a final box annealing-at a temperature within the range between 800 C. and the A temperature.
  • the foregoing processing removed about half of the original carbon but the other additions including sulfur did not change significantly.
  • the finish gauge material was cut into Epstein strips in the rolling direction.
  • a 1 inch'diameter torque disc of each of the alloys was annealed for 48 hours at 900 C. in dry hydrogen and thereafter furnace cooled.
  • FIG. 1 which superimposes the plots of the torque value versus the angle between the field and the rolling direction in degrees for a highly oriented 3% silicon iron as well as for alloys M 853 and M 849.
  • M 853 it can be seen that by decreasingthe sulfur content to a critically low level and by processing the material as set forth hereinbefore torque curves approaching those of. the commercially available 3% silicon iron are closely approximated.
  • Table II that is, the induction values where the field strength is 100 oersted it is clearly seen that much higher saturation induction values are obtained from the cobalt-iron alloys with overall improved magnetic characteristics resulting from the orientation of the material.
  • FIGS. 2 through 6 inclusive are photomacrographs of alloys identified therein and whose composition is set forth in Table I. These photomacrographs are at a magnification of 20X after annealing the cobalt iron alloy sheets for 48 hours at 900 C., and show a strong correlation between the sulfur content and the final grain size. From FIGS. 2 through 6 it isv apparent that the low sulfur levels result in a large grain size by normal grain growth, that is, from a primarily recrystallized microstructure and not as a result of secondary recrystallization and grain growth. These results as well as the shorter annealing times on M 852 and M 853 indicate that the degree of (110) [001] texture is increased by primary grain growth in alloys containing low sulfur.
  • alloys M 852 and M 853 reflect the additional beneficial aspect that the cobalt iron alloys with low sulfur values have low coercive force values. Moreover it appears that the addition of chromium to these cobalt iron alloys appear to improve the textureiorma tion to some degree while increasing volume resistivity.
  • heat M 853 Another heat of cobalt iron alloy was melted to substantially the same composition as heat M 853. This heat was identified as heat M 903 and was processed employing substantially the same conditions as heat M 853 with the following exception. After annealing for one hour at 900 C. at an intermediate gauge of 0.025 inch, the material was cold rolled to final thicknesses of 0.0095 and 0.012 inch.
  • Heat M 852 was given a final cold reduction of just 50%, consequently, it did not develop as high a texture as heat M 903 rolled to 0.0095 inch thickness. Actual measurements of heat M 852 indicated 61% by volume of the grains had the (110) texture while 16% exhibited the (100) texture. Further, 58% of the cube edges of crystal lattices of the grains deviated less than 10 from the [001] direction and 68% of the grains were within 15 of the [001] direction.
  • each of the alloys which were made and tested contained a cobalt content near the upper limit. Having thus found a high degree of orientation being eifected by means of the process of the present invention, other cobalt contents were investigated in order to determine the relative level of cobalt which would be effective for obtaining improved induction values commensurate with obtaining the required degree of (100) [001] orientation in a primarily recrystallized microstructure.
  • Table VI contains the nominal composition of two alloys which were made and tested in accordance with the teachings of the present invention it being noted that the alloys set forth in Table VI contain 18% cobalt and 10% cobalt with a corresponding amount of silicon of 1% and 2% being added to obtain improved volume resistivity. In these heats, the sulfur content was controlled so as to The alloys were processed in accordance with the following schedule:
  • the torque values indicate a high degree of (110) [001] texture. Although the 10% cobalt sample appears to be a little more highly textured, the 18% cobalt alloy has a higher induction value because of its higher saturation value. These samples exhibited only primary recrystallization and normal grain growth. In other tests, much lower torque values were obtained in similarly processed alloy compositions having sulfur additions of 0.01%. Also samples slowly heated to final annealing temperature, that is, appear to give poorer results.
  • An alloy member which exhibits improved permeabilities at low field strengths resulting from crystallographic orientation compared to unoriented magnetic material of the same composition consisting essentially of from about to about 35% cobalt, up to 2% chromium, up to 1% manganese, up to 3% silicon, less than 0.005% sulfur and the balance essentially iron with incidental impurities, the alloy having a primary recrystallized grain structure in which a major proportion of the grains exhibit a (110) texture and in which a major proportion of the oriented grains have cube edges of their crystal lattices aligned within of the rolling direction.
  • alloy member of claim 1 in which the cobalt is present in an amount between about 8% and about 20% and the silicon is present within the range between about 0.5% and about 2.0%
  • An alloy member which exhibits improved permeabilities at low field strengths resulting from crystallographic orientation compared to unoriented magnetic material of the same composition consisting essentially of from about 26.5% to about 28% cobalt, from about 0.25 to about 0.75% chromium, less than about 0.002% sulfur and the balance iron with incidental impurities, the alloy being characterized by a primary recrystallized microstructure having a major proportion of the grains exhibiting a orientation and a major proportion of the oriented grains having cube edges of their crystal lattices aligned within 10 of the rolling direction.
  • An alloy member which exhibits improved permeabilities at low field strengths resulting from crystallographic orientation compared to unoriented magnetic material of the same composition consisting essentially of from about 10% to about 18% cobalt, from about 0.5 to about 2.0% silicon, less than about 0.0025 sulfur and the balance essentially iron with incidental impurities, the alloy being characterized by a primary recrystallized grain structure with a major proportion of the grains exhibiting a (110) orientation and a major proportion of the oriented grains have cube edges of their crystal lattices aligned within 10 of the rolling direction.
  • An alloy member which exhibits improved permeabilities at low field strengths resulting from crystallographic orientation compared to unoriented magnetic material of the same composition consisting essentially of from about 5% to about 35% cobalt, up to 3% of at least one element for improving the volume resistivity without detrimentally affecting the chemical, physical and mechanical properties of the alloy and selected from the group consisting of silicon, chromium, vanadium, aluminum, titanium and molybdenum, less than about 0.005% sulfur, up to 1% manganese and the balance es sentially iron with incidental impurities, the alloy having a primary recrystallized grain structure with a major proportion of the grains exhibiting a (110) orientation and a major proportion of the oriented grains having the cube edges of their crystal lattices aligned within 10 of the rolling direction.

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US00228071A 1972-02-22 1972-02-22 Normal grain growth(110)(001)textured iron-cobalt alloys Expired - Lifetime US3843424A (en)

Priority Applications (9)

Application Number Priority Date Filing Date Title
BE795762D BE795762A (fr) 1972-02-22 Alliages fer-cobalt ameliores
US00228071A US3843424A (en) 1972-02-22 1972-02-22 Normal grain growth(110)(001)textured iron-cobalt alloys
CA161,434A CA988752A (en) 1972-02-22 1973-01-17 Normal grain growth (110) (001) textured iron-cobalt alloys
GB622973A GB1420371A (en) 1972-02-22 1973-02-08 Iron-cobalt alloys
DE19732307929 DE2307929A1 (de) 1972-02-22 1973-02-17 Verfahren zur herstellung von eisenkobalt-legierungsmaterial
JP48019839A JPS4897722A (it) 1972-02-22 1973-02-20
FR7306322A FR2173187B1 (it) 1972-02-22 1973-02-22
IT41530/73A IT976647B (it) 1972-02-22 1973-02-22 Procedimento per produrre leghe di ferro cobalto con migliorate caratteristiche magnetiche e le ghe cosi ottenute
US480075A US3892604A (en) 1972-02-22 1974-06-17 Method of producing normal grain growth (110) {8 001{9 {0 textured iron-cobalt alloys

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FR (1) FR2173187B1 (it)
GB (1) GB1420371A (it)
IT (1) IT976647B (it)

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3977919A (en) * 1973-09-28 1976-08-31 Westinghouse Electric Corporation Method of producing doubly oriented cobalt iron alloys
US4204887A (en) * 1975-04-04 1980-05-27 The Foundation: The Research Institute Of Electric And Magnetic Alloys High damping capacity alloy
US4208254A (en) * 1976-09-22 1980-06-17 Satoshi Ichioka Method of plating an iron-cobalt alloy on a substrate
WO2016083866A1 (fr) 2014-11-25 2016-06-02 Aperam Module élémentaire de noyau magnétique de transformateur électrique, noyau magnétique le comportant et son procédé de fabrication, et transformateur le comportant
US20160329139A1 (en) * 2015-05-04 2016-11-10 Carpenter Technology Corporation Ultra-low cobalt iron-cobalt magnetic alloys
WO2017017256A1 (fr) 2015-07-29 2017-02-02 Aperam Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant
WO2018109509A1 (fr) 2016-09-30 2018-06-21 Aperam Noyau de transformateur du type d'écoupé-empilé, et transformateur le comportant
EP3529386B1 (en) 2016-10-21 2021-04-14 CRS Holdings, Inc. Reducing ordered growth in soft-magnetic fe-co alloys
CN113897558A (zh) * 2021-10-08 2022-01-07 北京北冶功能材料有限公司 一种高饱和磁感高磁导率铁基软磁材料及其制备方法

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4529445A (en) * 1983-02-08 1985-07-16 U.S. Philips Corporation Invar alloy on the basis of iron having a crystal structure of the cubic NaZn13 type
DE19928764B4 (de) * 1999-06-23 2005-03-17 Vacuumschmelze Gmbh Eisen-Kobalt-Legierung mit geringer Koerzitivfeldstärke und Verfahren zur Herstellung von Halbzeug aus einer Eisen-Kobalt-Legierung

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR903197A (fr) * 1943-02-20 1945-09-26 Fides Gmbh Alliage magnétique

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3977919A (en) * 1973-09-28 1976-08-31 Westinghouse Electric Corporation Method of producing doubly oriented cobalt iron alloys
US4204887A (en) * 1975-04-04 1980-05-27 The Foundation: The Research Institute Of Electric And Magnetic Alloys High damping capacity alloy
US4208254A (en) * 1976-09-22 1980-06-17 Satoshi Ichioka Method of plating an iron-cobalt alloy on a substrate
WO2016083866A1 (fr) 2014-11-25 2016-06-02 Aperam Module élémentaire de noyau magnétique de transformateur électrique, noyau magnétique le comportant et son procédé de fabrication, et transformateur le comportant
US10515756B2 (en) 2014-11-25 2019-12-24 Aperam Basic module for magnetic core of an electrical transformer, magnetic core comprising said basic module, method for manufacturing said magnetic core, and transformer comprising said magnetic core
US20160329139A1 (en) * 2015-05-04 2016-11-10 Carpenter Technology Corporation Ultra-low cobalt iron-cobalt magnetic alloys
CN106119719A (zh) * 2015-05-04 2016-11-16 卡彭特科技公司 超低钴的铁-钴磁性合金
US11114226B2 (en) 2015-05-04 2021-09-07 Carpenter Technology Corporation Ultra-low cobalt iron-cobalt magnetic alloys
WO2017017256A1 (fr) 2015-07-29 2017-02-02 Aperam Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant
WO2018109509A1 (fr) 2016-09-30 2018-06-21 Aperam Noyau de transformateur du type d'écoupé-empilé, et transformateur le comportant
EP3529386B1 (en) 2016-10-21 2021-04-14 CRS Holdings, Inc. Reducing ordered growth in soft-magnetic fe-co alloys
CN113897558A (zh) * 2021-10-08 2022-01-07 北京北冶功能材料有限公司 一种高饱和磁感高磁导率铁基软磁材料及其制备方法

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IT976647B (it) 1974-09-10
FR2173187A1 (it) 1973-10-05
GB1420371A (en) 1976-01-07
BE795762A (fr) 1973-08-22
JPS4897722A (it) 1973-12-12
CA988752A (en) 1976-05-11
DE2307929A1 (de) 1973-09-06

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