WO1998046801A1 - Nouveau procede pour la production d'acier electrique a grains orientes a faible temperature - Google Patents

Nouveau procede pour la production d'acier electrique a grains orientes a faible temperature Download PDF

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Publication number
WO1998046801A1
WO1998046801A1 PCT/EP1997/001887 EP9701887W WO9846801A1 WO 1998046801 A1 WO1998046801 A1 WO 1998046801A1 EP 9701887 W EP9701887 W EP 9701887W WO 9846801 A1 WO9846801 A1 WO 9846801A1
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WO
WIPO (PCT)
Prior art keywords
strip
temperature
steel
process according
comprised
Prior art date
Application number
PCT/EP1997/001887
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English (en)
Inventor
Laura Appolloni
Giuseppe Abbruzzese
Giancarlo Di Schino
Original Assignee
Acciai Speciali Terni S.P.A.
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Acciai Speciali Terni S.P.A. filed Critical Acciai Speciali Terni S.P.A.
Priority to AU26980/97A priority Critical patent/AU2698097A/en
Priority to PCT/EP1997/001887 priority patent/WO1998046801A1/fr
Publication of WO1998046801A1 publication Critical patent/WO1998046801A1/fr

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Classifications

    • 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
    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • 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
    • C21D8/1222—Hot rolling
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding

Definitions

  • the present invention refers to a process for the production at low temperature of grain oriented electrical steel strips and, more precisely, refers to a less than usual complex process which, through a specific combination in cooperation relationship of a careful definition of the steel chemical composition with some well calibrated process specifications, allows to obtain a high quality product.
  • Silicon steel consists of a plurality of separate contiguous grains (or crystals), each having a body-centered cubic lattice, in which the axes corresponding to the cube corners, crystallographically designed with ⁇ 100>, are directions of easest magnetization.
  • nuclei for electric transformers which are formed by stacks of silicon steel relatively narrow bands cut parallelely to the rolled strip length and wound in form of torus
  • the working scheme of transformers in which a magnetic field induces in the nucleus a magnetic flux directed along the lines of easiest magnetization of the material forming the nucleus itself, it follows that the ⁇ 001> axes should preferably lay parallel to the rolling direction of the strip, i.e. to the strip lenght.
  • the lattices of said grains are all oriented in the same way, with the minimum degree of mutual disorientation. Further, it is necessary that number and dimensions of said grains are maintained within given limits, well known to the experts.
  • the correct orientation of grains in the end product is obtained during a termal treatment called secondary recrystallization annealing, in which it is possible to allow the growth only of grains having the desired orientation at the beginning of the annealing.
  • the selective grain growth process is temperature activated and is due to the fact that some crystals, for kinetic and/or energetic reasons more "charged” than the others, start to grow at the expenses of adjacent crystals at a lesser temperature than the others, thus more quickly reaching the critical dimensions permitting their predominance in growing.
  • the production process of such steel strips comprises a number of high-temperature treatments, during some of which a grain growth could start which, should it occur with wrong modalities and timing, will prevent to reach the wanted final results.
  • the secondary recrystallization is controlled by some compounds, such as manganese sulfide, manganese selenide, aluminum nitride and the like, which duly precipitated within the steel inhibit the grain growth up to a temperature, at which are solubilized, thus permitting the secondary recrystallization to start.
  • some compounds such as manganese sulfide, manganese selenide, aluminum nitride and the like, which duly precipitated within the steel inhibit the grain growth up to a temperature, at which are solubilized, thus permitting the secondary recrystallization to start.
  • Such slabs are translated, at a temperature not lesser than 300 °C, and then reheated (possibly with a pre-rolling of no more than 25% at 1100-1200 °C) at high temperature, usually at 1300-1400 °C, hot rolled and the strip, if necessary annealed, cold rolled to the final thickness, usually comprised between 0.18 and 0.35 mm ⁇ and then subjected to a number of high-temperature final treatments, intended to drastically reduce the carbon content (decarburation annealing) , sulfur and nitrogen, to obtain the desired magnetic properties (secondary recrystallization annealing), to form on the strip surface insulating inorganic coatings, for instance magnesium phosphate and silica based.
  • the continuous casting requires a quick initial cooling of the molten steel in the mould, to allow a quick extraction of the slab comprising a solid skin, a soft intermediate mass and a quantity of liquid steel at the centre, which will solidify later. From such initial conditions some consequencies ensue requiring opportune careful control.
  • the metal undergo two radically different cooling rates, a first very quick at the surface and then a second more slow at the core, and then solidifies in two different structures, at the surface in small equiaxic crystals and at the core in elongated much larger crystals, called columnar. This starting difference, if not amended, induces a non omogeneous structure in the final product, and a lesser quality.
  • the relatively slow cooling rate of the slabs bulk brings both to an abnormal growth of the fraction of columnar crystals with respect to the fraction of the equaxic ones, and to the segregation of some elements as well as to the coagulation of some compounds , such as manganese sulfide, in large lumps not easily dissolved at the reheating temperatures, which then cannot be reprecipitated as finely dispersed particles, necessary to correctly perform as grain growth inhibitors.
  • the slabs are heated at high temperature, typically above 1330 °C, to dissolve the compounds precipitated during the slab cooling as large lumps, and to allow them to be more homogeneously diffused within the metal.
  • the furnaces usually utilized to reach such a high .
  • heating temperature have a number of inconveniences , among which some very important are temperature differences found between surface and core of the slabs and the high overheating of the slab surface, necessary to let the core assume the desired temperature within an acceptable period of time, which factors induce an unwanted grain growth, as well as the formation of liquid slag on the slab surface, which requires specific furnaces difficult to manage, thus increasing production costs.
  • the metal undergoes a thickness reduction at such temperature and reduction rates to obtain acceptable grain dimensions and to precipitate in fine particles, due to the cooling, the above mentioned compounds, such as manganese sulfide.
  • a pre-rolling is usually utilized, consisting in a first hot rolling pass carried out before the maximum heating temperature is reached; this obviously calls for higher costs, mainly due to the fact that slabs have to be extracted from the furnace , rolled and then put again in the furnace . It is easy to understand now how complex and costly is the production of a good grain oriented silicon steel strip, and hence how important is to utilize in the more efficient way any possible technique to reduce production costs.
  • a first step in this direction was trying to eliminate the prerolling step and to reduce the slab heating temperature before hot rolling; this last step being particularly costly, essentially due to the high temperature to be reached, the long treating time, the large dimensions of the slabs to be treated and the necessity to utilize specific furnaces, as already mentioned.
  • the dissolution temperature of manganese sulfide in the steel is a function of a number of factors, among which the content of oxygen (and then the internal oxidation level of the steel), manganese and sulfur, by careful controlling such elements it is possible to reduce by many tens of degrees the slab heating temperature.
  • Belgian patent 792.173 refers to the continuous casting of grain oriented electrical steel slabs, in which a steel is cast comprising, in wt % , C 0.025-0.060, Mn > 0.035, S > 0.010, Si 2.0-4.0, acid soluble Al ⁇ 0.005, remainig being iron and minor impurities, with a Si0 2 /Al 2 0 ratio of less than 1.1.
  • French patent 2.158.458 refers to a steel comprising, in wt Ji, C 0.02- 0.05, Mn 0.04-1.12, S 0.015-0.035.
  • Published german patent application DE 4.311-1 1 refers to a steel comprising, in wt % , C 0.02-0.10, Si 2.5 ⁇ 5, Mn 0.04-0.15, S 0.010, Al 0.010-0.035, N 0.0045-0.0120, Cu 0.020-0.300, remaining being essentially iron; slabs of this steel are heated at a temperature insufficient to dissolve manganese sulfide but sufficient to dissolve copper sulfide; the slabs are then hot rolled with an end-rolling temperature between 880 and 1000 °C to a thickness of between 1.5 and 7 mm, the strip so obtained is annealed at 880-1150 °C for 100-600 s and then cooled at a rate of 15 °K/s. The secondary recrystallization mechanism is thus controlled by finely precipitated copper sulfide. In JP 04 301 035-A and 05 2 442-A the cooling rate after the last hot-rolling stand is controlled.
  • the strip is reduced by O.5-I5 % before cold rolling in a rolling stand whose rolls have a diametre of 0 times the strip thickness, and then annealed at 700-1100 °C.
  • a process is described referring to a silicon steel comprising, in wt % , C 0.021-0.100, Si 2.5 ⁇ 4.5 > one or more elements inhibiting the grain growt such as Al, N, Mn, S, Se, Sb, B, Cu, Bi, Nb, Cr, Sn, Ti .
  • the hot rolled strip is coiled at a temperature comprised between 00 and 700 °C and the coil, of a weight comprised between 5 and 20 t, is cooled in air or preferably in water.
  • the usual cold rolling and annealing follow.
  • JP 02 133 5-A the hot rolling ends at a temperature of at least 900 °C and the strip is cooled at a rate of at least 40 °C/s and coiled at a temperature of between 300 and 500 °C.
  • JP 61 186456 discloses a steel comprising, in wt % , C 0.01-0.06, Si 3.1-4.5, Mn 0.01-0.2, Mo 0.003-0.1, Sb 0.005-0.2, S and/or Se 0.005- 0.1, and at least one between Cr 0.01-0.03, Cu 0.01-0.5, Sn 0.005-0.2.
  • JP 61 79722-A discloses a steel comprising, in wt % , C ⁇ O.O85, Si 2- 4, Mn 0.03-0.1, Al s 0.01-0.05, and moreover Sn O.O3-O.5 and Cu 0.02- 0.3; it is specified that Sn helps reducing the grain dimensions in the secondary recrystallization while Cu enhances adhesion of final glass coatings; moreover, both of said elements act as grain growth inhibitors .
  • BE 89 038 discloses a treating process for a silicon steel comprising, in wt % , Cu 0.02-0.2, in which the entering temperature of the strip in the last hot-rolling stand is comprised between 1100-1250 °C, while the exit temperature is of 900-1050 °C for the upper part of the strip and of 950-1100 °C for the middle and lower parts.
  • JP 01 309924-A discloses a treating process for a silicon steel in which a slab is heated at a maximum temperature of 1270 °C, hot rolled at an exit temperature of 700-900 °C and coiled at less than 600 °C.
  • JP 02 101120-A disclosed a process allowing to eliminate the precipitation annealing, yet permitting to obtain excellent magnetic characteristics. The process comprises finishing the hot rolling at a temperature higher than 900 °C, with the temperature at the beginning and at the end of the strip within 10 % of its entire length, higher by 50-200 °C than the one of the remaining of the strip, which is coiled at a temperature of more than 700 °C, held at this temperature for 5 _ 6 ⁇ min and then water cooled. DESCRIPTION OF THE INVENTION
  • composition As far as the composition is concerned, it is necessary to keep a relatively low initial content of carbon and acid soluble aluminum (Al s ), respectively lower than 400 and 200 ppm, preferably between 200 and 350 ppm for C amd between 30 and 100 ppm for Al s>
  • the silicon is controlled within weigth percentages between 2.5 and 4.5, particularly between 2.9 and 3-3-
  • To this composition are added from 0.030 and 0.300 % Sn and from 0.100 and O.35O Cu.
  • grain growth inhibiting elements can be utilized, together to or instead of elements such as Al, elements chosen between Nb and/or Ti and/or V, in total percentages comprised between 0.01 and 0. 3% .
  • the steel slabs thus obtained are heated at a temperature lesser than 1300 °C, preferably between 1200 and 1290 °C, and then hot rolled, the entering temperature into the finishing stand being comprised between 1050 and 1200 °C and the exit temperature being comprised between 900 and 1059 °C, preferably between 950 and 1000 °C.
  • the thermal homogeinity of the steel bar must also be carefully controlled, ensuring that the entrance temperature into the finishing stand is kept within 30 °C.
  • the cooling of the strip is started _ 0 s after the exit from the finishing stand, and is preferably carried out in water; the strip is then coiled at a temperature of beteen 00 and 800 °C, preferably lesser than 56O °C.
  • the thus obtained hot rolled strip undergoes the usual treatments before being cold rolled in at least two rolling steps; the last cold rolling pass must have a reduction rate of 45 _ 70 if the Al content is lesser than 80 ppm, and of 60-80% if the Al content is higher than 8 ⁇ ppm.
  • the cold rolled strip undergoes the usual final treatments of decarburization, secondary recrystallization and formation of an inorganic insulating coating, keeping m mind that during the decarburization annealing the heating rate must be higher than 10 °C/s, preferably between 1 and 20 °C/s.
  • composition A is according to the invention but for the Cu and Sn content sum; compositions B and C are according to the invention; compositions D and E are known in the literature. All those steels did undergo the following transformation cycle: A- CASTING
  • Steels A, B, C and D were continuously cast and the slabs were reduced by 8% (from 222 to 202 mm) during the secondary cooling outside of the casting mould when their cores not fully solidified, with a solidification percentage of between 50 and 60 % .
  • Hot rolling was performed in a number of passes, keeping the steel temperature at the entrance of the finishing stand between 1090 and
  • the final thickness of the hot rolled strip was 2.1 mm .
  • the hot rolled strip was then annealed at 1000 °C for 1 min.
  • the steel E did undergo a fully traditional transformation cycle well known to the experts.
  • the obtained magnetic characteristics are now reported, expressed as core losses, in W/kg at an induction of 1.5 and 1.7 T (PI.5 and PI.7 W/kg) at 50 Hz, and as permeability in a field of 800 As/m (B ⁇ OO) in T.
  • compositions B and C, treated according to the invention show magnetic characteristics similar to those of composition E, which is traditional and was treated according to the conventional method, while composition A, m which the sum of Sn and Cu contents is out of present invention, and composition D, which is conventional, both treated according to the invention, do not reach satisfactory results.
  • composition expressed in wt % unless otherwhise specified, was prepared: C 290 ppm, Si 3-30, Al 70 ppm, N 51 ppm, Mn 0.058%, S 210 ppm, Cu 0.28, Sn 0.030, remaining being iron and minor impurities .
  • This composition was cast according to Example 1, which was followed also for slab heating and hot rolling. At the exit from the finishing stand the cooling was started after:
  • the magnetic characteristics obtained on cold rolled strip 0.30 mm thick were the following:
  • a steel was used similar to composition B of Example 1, but with an Al content of 85 ppm.
  • the transformation cycle was according to the invention, but with the following final cold rolling reduction rates, in % , to obtain a final thickness of 0.23 mm-

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)

Abstract

L'invention a pour objet un procédé pour la production de feuilles d'acier de silicone à grains orientés. Selon ce procédé, une feuille est coulée en continu en brames. Cette feuille se compose des éléments suivants, en pourcentage en poids: moins de 0,040 de C, moins de 0,020 d'AL, de 2,5 - 4,5 de Si, de 0,03 - 0,30 de Sn, de 0,1 - 0,35 de Cu, de 0,010 - 0,025 de S, de 0,030 - 0,30 de Mn, ainsi que de fer et d'impuretés mineures. Ces brames, dont l'épaisseur est réduite de 1 à 10 %, sont ensuite laminées à chaud à une température comprise entre 1050 et 1200 °C au niveau de l'entrée de la cage finisseuse, et une température située entre 900 et 1050 °C au niveau de la sortie de cette cage. La bande peut ensuite être refroidie 5 à 10 secondes après la sortie, à une température comprise entre 500 et 700 °C. Cette bande est ensuite laminée à froid en au moins deux étapes de réduction, avant de procéder aux traitements terminaux, au cours desquels pendant la malléabilisation par décarburation, la vitesse de chauffage est supérieure à 10 °C/s.
PCT/EP1997/001887 1997-04-16 1997-04-16 Nouveau procede pour la production d'acier electrique a grains orientes a faible temperature WO1998046801A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
AU26980/97A AU2698097A (en) 1997-04-16 1997-04-16 New process for the production at low temperature of grain oriented electrical steel
PCT/EP1997/001887 WO1998046801A1 (fr) 1997-04-16 1997-04-16 Nouveau procede pour la production d'acier electrique a grains orientes a faible temperature

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/EP1997/001887 WO1998046801A1 (fr) 1997-04-16 1997-04-16 Nouveau procede pour la production d'acier electrique a grains orientes a faible temperature

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WO1998046801A1 true WO1998046801A1 (fr) 1998-10-22

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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2012207278A (ja) * 2011-03-30 2012-10-25 Jfe Steel Corp 方向性電磁鋼板の製造方法
WO2013045339A1 (fr) * 2011-09-28 2013-04-04 Thyssenkrupp Steel Europe Ag Procédé de fabrication de feuillard ou tôle magnétique à grains orientés pour applications électrotechniques
CZ305521B6 (cs) * 2014-05-12 2015-11-11 Arcelormittal Ostrava A.S. Pás z orientované transformátorové oceli a způsob jeho výroby
EP3358031A4 (fr) * 2015-09-28 2019-07-03 Nippon Steel Corporation Tôle d'acier électromagnétique à grains orientés et tôle d'acier laminée à chaud pour tôle d'acier électromagnétique à grains orientés
JP2021509150A (ja) * 2017-12-26 2021-03-18 ポスコＰｏｓｃｏ 方向性電磁鋼板およびその製造方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59159934A (ja) * 1983-03-02 1984-09-10 Kawasaki Steel Corp 方向性けい素鋼板製造用素材の連続鋳造法
EP0393508A1 (fr) * 1989-04-17 1990-10-24 Nippon Steel Corporation Procédé de production de tôles d'acier électrique à grains orientés ayant des propriétés magnétiques supérieures
JPH0387315A (ja) * 1989-08-30 1991-04-12 Kawasaki Steel Corp 磁気特性および表面性状に優れた一方向性電磁鋼板の製造方法
DE4311151C1 (de) * 1993-04-05 1994-07-28 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten
JPH08225843A (ja) * 1995-02-15 1996-09-03 Nippon Steel Corp 方向性珪素鋼板の製造方法
DE19628137C1 (de) * 1996-07-12 1997-04-10 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59159934A (ja) * 1983-03-02 1984-09-10 Kawasaki Steel Corp 方向性けい素鋼板製造用素材の連続鋳造法
EP0393508A1 (fr) * 1989-04-17 1990-10-24 Nippon Steel Corporation Procédé de production de tôles d'acier électrique à grains orientés ayant des propriétés magnétiques supérieures
JPH0387315A (ja) * 1989-08-30 1991-04-12 Kawasaki Steel Corp 磁気特性および表面性状に優れた一方向性電磁鋼板の製造方法
DE4311151C1 (de) * 1993-04-05 1994-07-28 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten
JPH08225843A (ja) * 1995-02-15 1996-09-03 Nippon Steel Corp 方向性珪素鋼板の製造方法
DE19628137C1 (de) * 1996-07-12 1997-04-10 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech

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PATENT ABSTRACTS OF JAPAN vol. 015, no. 259 (C - 0846) 2 July 1991 (1991-07-02) *
PATENT ABSTRACTS OF JAPAN vol. 097, no. 001 31 January 1997 (1997-01-31) *

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2012207278A (ja) * 2011-03-30 2012-10-25 Jfe Steel Corp 方向性電磁鋼板の製造方法
WO2013045339A1 (fr) * 2011-09-28 2013-04-04 Thyssenkrupp Steel Europe Ag Procédé de fabrication de feuillard ou tôle magnétique à grains orientés pour applications électrotechniques
CZ305521B6 (cs) * 2014-05-12 2015-11-11 Arcelormittal Ostrava A.S. Pás z orientované transformátorové oceli a způsob jeho výroby
EP3358031A4 (fr) * 2015-09-28 2019-07-03 Nippon Steel Corporation Tôle d'acier électromagnétique à grains orientés et tôle d'acier laminée à chaud pour tôle d'acier électromagnétique à grains orientés
US11680302B2 (en) 2015-09-28 2023-06-20 Nippon Steel Corporation Grain-oriented electrical steel sheet and hot-rolled steel sheet for grain-oriented electrical steel sheet
JP2021509150A (ja) * 2017-12-26 2021-03-18 ポスコＰｏｓｃｏ 方向性電磁鋼板およびその製造方法

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