EP2775007A1 - Procédé de production d'un acier électrique à grains orientés - Google Patents

Procédé de production d'un acier électrique à grains orientés Download PDF

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Publication number
EP2775007A1
EP2775007A1 EP13158409.6A EP13158409A EP2775007A1 EP 2775007 A1 EP2775007 A1 EP 2775007A1 EP 13158409 A EP13158409 A EP 13158409A EP 2775007 A1 EP2775007 A1 EP 2775007A1
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EP
European Patent Office
Prior art keywords
strip
annealing
temperature
process according
hot rolled
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Granted
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EP13158409.6A
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German (de)
English (en)
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EP2775007B1 (fr
Inventor
Herbert Kreuzer
Stefano Cicalé
Luciano Albini
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Voestalpine Stahl GmbH
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Voestalpine Stahl GmbH
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    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a process for the production of grain oriented electrical steel, particularly grain oriented steel sheets to be used for cores in transformers and other electrical machines.
  • the "low heating rate" "high soaking temperature” batch annealing during which secondary recrystallization is performed constitutes a high time-consumption and high cost in the known CRGO production process.
  • Sheets in this context are defined as any flattened steel products that are thinner than a plate, including also strips regardless if the products are slit from wider sheets or not.
  • the final product in which the steel sheets manufactured according to the process of the invention are intended to be employed as core material has a maximum core loss at 1.7 T and 50 Hz (P 17/50 ) of ⁇ 2 W/kg and/or a magnetic polarization at 800 A/m (J 800 ) of > 1.7 T.
  • the thickness of such sheets is typically in the range of 0.23 - 0.35 mm.
  • a process for the manufacturing of a grain oriented electrical steel sheet comprising the steps of: a) providing a hot rolled strip comprising in weight %: C ⁇ 0.006 preferably ⁇ 0.003 Si 3.0 - 3.5 preferably 3.1-3.3 Mn 0.4 - 2.0 preferably 0.45 - 0.65 Als 0.005-0.03 preferably 0.01-0.02 N 0.004 - 0.009 preferably 0.005 -0.008 S ⁇ 0.008 preferably ⁇ 0.005 Ti ⁇ 0.006 preferably ⁇ 0.004 optionally one or more of Cu 0.05 - 0.3 Sn 0.04 - 0.15 Ni ⁇ 0.1 preferably ⁇ 0.05 Cr ⁇ 0.2 preferably ⁇ 0.05 P ⁇ 0.02 preferably ⁇ 0.01 B ⁇ 0.01 preferably 0.001 - 0.005 Te ⁇ 0.01 preferably ⁇ 0.005 Cd ⁇ 0.01 preferably ⁇ 0.005 Zn ⁇ 0.01 preferably ⁇ 0.005 As ⁇ 0.01
  • the new and efficient process results in a final product typically having a maximum core loss at 1.7 T at a sheet thickness of 0.30 mm and 50 Hz (P 17/50 ) of ⁇ 2 W/kg and a magnetic polarization at 800 A/m (J 800 ) of > 1.7 T.
  • Key features of the inventive process includes the provision of a hot rolled strip having a carefully balance composition, in particular a very low carbon content.
  • a decarburization annealing need not be performed during the transformation process of the hot rolled strip down to finished product.
  • a further key feature is that the final annealing during which the secondary recrystallization happens is divided in two steps:
  • This two step annealing allows the possibility of finalizing the recrystallization annealing in the continuous annealing line if not already completed during the batch annealing.
  • the drawing schematically illustrates a process line for the manufacturing of a grain oriented electrical steel sheet according to the invention.
  • the steel composition of the hot rolled band is defined in claim 1.
  • the carbon level is closely reflected in the carbon level of the secondary recrystallized strip since the process dispenses with any deliberate intermediate decarburization annealing. For this reason it is of the utmost importance to control the carbon content during steelmaking such that the carbon content is less than 30 ppm (0.003 wt. %) in the melt to be cast.
  • the inhibition to control the secondary recrystallization is mainly based on the precipitation of AlN. Accordingly, the content of Al and N should be controlled such that AlN is dissolved during slab reheating, precipitation is minimized or avoided during hot rolling but occur during the annealing of the strip performed at intermediate thickness.
  • the contents of Als (acid soluble Al) and N are controlled such that the ratio Als/N is stoichiometric.
  • the ratio Als/N is stoichiometric.
  • ⁇ 35 % of the stoichiometric ratio or preferably within ⁇ 15 % of the stoichiometric ratio can be tolerated.
  • the sulfur content should be maintained at a low level in order to avoid undue precipitation of MnS.
  • the content should be less than 30 ppm, preferably less than 20 ppm and most preferred less than 10 ppm.
  • the manganese content is maintained at 0.4 - 2 % in order to increase the resistivity of the alloy and thereby decreasing the core loss.
  • the content of titanium should also be closely controlled since Ti is a strong nitride former. Ti enters the steel melt from the raw materials used in iron- and steelmaking. Accordingly, the ladle slag is normally to be skimmed after tapping and FeSi having a low Ti-content should be used.
  • the content of Ti should be less than 0.006 % , preferably less than 0.004% or even less than 0.0020% (20 ppm).
  • AlN In addition to AlN other inhibitors may be used to assist the control.
  • Other possible elements that may be present are defined in claim 1. It may be noted that in some cases these elements are present as impurities. Cu and Sn may be added, typical in an amount of 0.1 %. As, Pb, P and Zn may be added as defined in claim 1. However, preferably, the total amount of these elements is less than 0.2%, in particular less than 0.05%. B, Ni, Cr, Te and Cd may be present as defined in claim 1. However, in most cases it is preferred that the total amount of these elements is restricted to 0.30%. Bismuth, when used, need to be present in an amount of at least 5 ppm in order to provide an effect. However, if the content is higher than 20 ppm brittleness problems may occur.
  • reference numeral I represents a section for the provision of a steel alloy having the adequate chemical composition prepared for cold rolling, and of a hot rolled strip of the steel alloy according to a) and b) in the foregoing while reference numeral II represents a section for cold rolling of the hot rolled steel strip and for heat treatment of the strip in connection therewith according to c), d) and e) in the foregoing.
  • molten steel is manufactured in a mode, which principles may be conventional per se, by means a complex of iron and steel manufacturing facilities which also may be conventional such as a number of the following ones: blast furnace, LD converter, electric arc furnace, VOD, RH degasser and others.
  • any chosen combination of apparatuses for making molten steel is symbolically represented by complex 1 .
  • the continuously cast strand 4 is successively cut to slabs 5 which are reheated in a walking beam furnace 6 to a temperature of between 1220 and 1300 °C, suitably to a temperature of about 1260 °C.
  • a series of induction heating devices locally reheat the slabs eliminating any skid mark effect.
  • each reheated slab 5 is subjected to roughing at > 1200 °C. in a roughing facility 7 in order to produce a plate or bar having a thickness of 20 - 80 mm.
  • the plate or bar is hot rolled in a hot rolling mill 8 to form a strip 9 with a thickness of 1.5 - 4 mm, preferably 2 - 3 mm or 2 - 2.5 mm.
  • the starting temperature of the hot rolling in the hot rolling mill 8 is > 920 °C, preferably 950 - 1200 °C, and most preferable 970 - 1150 °C, while the finish rolling temperature is > 850 °C.
  • the hot rolled steel strip is cooled at a rate of 5 - 100 C/s down to a coiling temperature ⁇ 600 °C. and coiled at that temperature.
  • the hot rolled strip is passed through a scale breaker (not shown), pickled in the pickling unit 10 and optionally annealed (not shown).
  • pickling may be performed in sulphuric acid at a concentration of 235-245 g/l, which is regenerated by crystallization and centrifugation.
  • the pickling time can be varied in the range 20 - 60 seconds. After pickling, the strip is trimmed and recoiled.
  • the hot rolled strip is cold rolled in a cold rolling mill 12 to an intermediate thickness of 0.38 - 1.2 mm, preferably to 0.5 - 1.0 mm. Then, the cold rolled strip having said intermediate thickness is subjected to continuous intermediate annealing in a continuous type annealing furnace 13 at a temperature of 850 - 1000 °C, preferably at 880 - 930 °C, such that the cold rolled strip material is recrystallized.
  • the atmosphere in the annealing furnace may be 100 % hydrogen or a mixture of hydrogen and nitrogen.
  • the recrystallized strip is cooled and then cold rolled a second time in cold rolling mill 12 , now with a reduction rate of 40 - 70 % to a final thickness of 0.23 - 0.35 mm.
  • the temperature of the strip is maintained in the range of 80 - 400 °C, preferably in the range of 100 - 200 °C.
  • the cold rolled strip is now prepared to be annealed to provoke secondary recrystallization.
  • the annealing is performed in two steps according to the invention.
  • the final microstructure is obtained by secondary recrystallization annealing, which is incubated at low temperature in the batch annealing furnace and may subsequently be completed by the continuous annealing at high temperature, if not already completely recrystallized after batch annealing.
  • the cold rolled and coiled strip 15 having said final thickness is batch annealed in a batch annealing furnace 16 by heating the strip at a rate of less than 200 C/h to a holding temperature of 860 - 950 °C. and holding the strip at that temperature for a period of time of 2 - 20 hours.
  • the batch annealing is preferably performed in an atmosphere of dry hydrogen.
  • an annealing separator in particular a MgO powder layer is built on the strip surface before entering the batch annealing furnace in order to prevent sticking.
  • the atmosphere of the continuous intermediate annealing performed in a continuous type annealing furnace 13 contains water so that the water partial pressure and hydrogen partial pressure is in the range 0.1-0.7. Due to this presence of water an oxide layer, which is composed of Silica, Fayalite and Iron Oxide, adherent to the strip surface is built on the strip surface. During cold rolling such iron oxide remains adherent to the strip surface, and during box annealing react with MgO powder to form and adherent layer of forsterite, which act as a coating of the strip surface.
  • MgO powder is not used during box annealing, oxidation during the continuous intermediate annealing, performed in a continuous type annealing furnace 13 , is detrimental and the presence of water during the annealing has to be avoided; in such a case the water partial pressure and hydrogen partial pressure has to be lower than 0.01.
  • the cold rolled and batch annealed strip 17 is continuously annealed at a temperature of 800-1200 °C for 30 - 600 seconds in a continuous annealing furnace 18 in an atmosphere preferably consisting of dry hydrogen or dry hydrogen/nitrogen mixture.
  • the continuous annealing mainly effects thermo-flattening and the temperature may be in the range of 800-950 °C.
  • the secondary recrystallization is to be completed during this step, then it is better to perform the continuous annealing in the range of 950-1200 °C, preferably 1050-1150°C.
  • the process further includes coating the continuously annealed sheet 19 with an organic or inorganic coating as an annealing separator, optionally with tensioning properties and curing the sheet for more than 20 seconds at a temperature exceeding 150 °C. in a continuous curing furnace 20 before coiling. Due to the invention as described in this patent specification and claims, the final product will have a maximum core loss at 1.7 T and 50 Hz (P 17/50 ) of ⁇ 2 W/kg and/or a magnetic polarization at 800 A/m (J 800 ) of > 1.7 T.
  • the final annealing temperature may be optimized according to the starting rolling temperature.
  • the starting finishing rolling temperature is ⁇ 1050°C then the final annealing as specified in point g) of claim 1 can be performed with a soaking temperature laying in the lower part of said range.
  • the temperature could be in the range of 800-950 °C, preferably 860-950° because an annealing temperature above 950°C does not improve the final characteristics of the material but it increases the consumption of energy necessary to perform the annealing.
  • the starting finishing rolling temperature is higher than 1050°C then the final annealing temperature specified in point g) of claim 1 should be the upper part of said.
  • the temperature should in this case be in the range of 950°C-1200°C, preferably in the range of 1050°C-1150°C.
  • the final annealing optimal temperature range varies depending on the starting rolling temperature is not completely clear but it would appear that when the starting rolling temperature is below 1050°C then the secondary recrystallization is virtually completed during the low temperature batch annealing. In this case, the final annealing is necessary only for performing thermo-flattening of the steel strip when the batch annealing is performed with the strip wound in a coil.
  • a steel with a chemical composition as reported in Table 1 has been cast to form a slab, slab has been reheated at 1260 °C temperature, and hot rolled.
  • a steel with a chemical composition as reported in Table 3 has been cast, slab have been treated at 1250 °C slab reheating temperature and hot rolled.
  • a steel with a chemical composition as reported in Table 5 has been cast in 3 different slabs: a, b, c. Cast slabs have been reheated at A:1210 °C, B:1240 °C and C:1260 °C, and hot rolled.
  • a steel with a chemical composition as reported in Table 9 has been cast in 2 different slabs: a, b. Cast slabs have been reheated at 1240 °C and hot rolled, after roughing, with two different starting finishing rolling temperature:
  • Samples after hot rolling have been cold rolled down to 0,70 mm intermediate thickness.
  • Samples at intermediate thickness have been annealed at 900°C for 100 sec.
  • Annealed samples have been cold rolled down to final thickness of 0,30 mm and have been undergone to batch annealing with following cycle: heating from 25°C to 900°C in 6 h ; holding at 900°C for 10 h; cooling from 900°C to 25°C in 18 h.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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EP13158409.6A 2013-03-08 2013-03-08 Procédé de production d'un acier électrique à grains orientés Not-in-force EP2775007B1 (fr)

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EP13158409.6A EP2775007B1 (fr) 2013-03-08 2013-03-08 Procédé de production d'un acier électrique à grains orientés

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EP2775007B1 EP2775007B1 (fr) 2018-12-05

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Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2016035530A1 (fr) * 2014-09-01 2016-03-10 新日鐵住金株式会社 Tôle d'acier électromagnétique à grains orientés
CN106298221A (zh) * 2016-08-30 2017-01-04 河南中岳非晶新型材料股份有限公司 非晶体抗直流铁芯及其热处理方法
WO2017073615A1 (fr) * 2015-10-26 2017-05-04 新日鐵住金株式会社 Tôle d'acier électromagnétique à grains orientés et tôle d'acier décarburé utilisée pour produire celle-ci
CN108277429A (zh) * 2017-01-05 2018-07-13 鞍钢股份有限公司 一种高硅电工钢的生产方法
US20190032168A1 (en) * 2017-07-25 2019-01-31 Hyundai Motor Company Continuous annealing apparatus
JP2019019359A (ja) * 2017-07-13 2019-02-07 新日鐵住金株式会社 皮膜密着性に優れる一方向性珪素鋼板及びその製造方法
JP2019019358A (ja) * 2017-07-13 2019-02-07 新日鐵住金株式会社 皮膜密着性に優れる一方向性電磁鋼板及びその製造方法
JP2019505671A (ja) * 2015-12-21 2019-02-28 ポスコＰｏｓｃｏ 方向性電磁鋼板及びその製造方法

Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2287467A (en) 1940-01-03 1942-06-23 American Rolling Mill Co Process of producing silicon steel
JPH08134542A (ja) * 1994-11-08 1996-05-28 Sumitomo Metal Ind Ltd 打抜き性に優れた方向性電磁鋼板の製造方法
EP0789093A1 (fr) 1994-11-16 1997-08-13 Nippon Steel Corporation Procede de production de tole magnetique directive pouvant facilement etre revetue de verre et presentant d'excellentes proprietes magnetiques
EP0869190A1 (fr) 1997-03-26 1998-10-07 Kawasaki Steel Corporation TÔle en acier électrique à grain orienté présentant une très faible perte dans le fer et procédé pour sa production
JPH10273725A (ja) * 1997-03-31 1998-10-13 Sumitomo Metal Ind Ltd 方向性電磁鋼板の製造方法
EP0997540A1 (fr) * 1998-10-27 2000-05-03 Kawasaki Steel Corporation Tôle d' acier électromagnetique et procédé de sa fabrication
EP1004680A1 (fr) * 1998-10-09 2000-05-31 Kawasaki Steel Corporation Procédé de fabrication de tôle d'acier magnétique à grains orientés à faible perte dans le fer
JP2001107147A (ja) * 1999-10-12 2001-04-17 Kawasaki Steel Corp 方向性電磁鋼板の製造方法
EP1279747A2 (fr) * 2001-07-24 2003-01-29 Kawasaki Steel Corporation Procédé pour la fabrication de tôles d'acier électrique à grains orientés
EP1577405A1 (fr) 2002-10-29 2005-09-21 JFE Steel Corporation Procede de fabrication d'une tole d'acier magnetique a grains orientes et tole correspondante
JP2009228118A (ja) * 2008-03-25 2009-10-08 Jfe Steel Corp 方向性電磁鋼板の製造方法

Patent Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2287467A (en) 1940-01-03 1942-06-23 American Rolling Mill Co Process of producing silicon steel
JPH08134542A (ja) * 1994-11-08 1996-05-28 Sumitomo Metal Ind Ltd 打抜き性に優れた方向性電磁鋼板の製造方法
EP0789093A1 (fr) 1994-11-16 1997-08-13 Nippon Steel Corporation Procede de production de tole magnetique directive pouvant facilement etre revetue de verre et presentant d'excellentes proprietes magnetiques
US5840131A (en) * 1994-11-16 1998-11-24 Nippon Steel Corporation Process for producing grain-oriented electrical steel sheet having excellent glass film and magnetic properties
EP0869190A1 (fr) 1997-03-26 1998-10-07 Kawasaki Steel Corporation TÔle en acier électrique à grain orienté présentant une très faible perte dans le fer et procédé pour sa production
JPH10273725A (ja) * 1997-03-31 1998-10-13 Sumitomo Metal Ind Ltd 方向性電磁鋼板の製造方法
EP1004680A1 (fr) * 1998-10-09 2000-05-31 Kawasaki Steel Corporation Procédé de fabrication de tôle d'acier magnétique à grains orientés à faible perte dans le fer
EP0997540A1 (fr) * 1998-10-27 2000-05-03 Kawasaki Steel Corporation Tôle d' acier électromagnetique et procédé de sa fabrication
JP2001107147A (ja) * 1999-10-12 2001-04-17 Kawasaki Steel Corp 方向性電磁鋼板の製造方法
EP1279747A2 (fr) * 2001-07-24 2003-01-29 Kawasaki Steel Corporation Procédé pour la fabrication de tôles d'acier électrique à grains orientés
EP1577405A1 (fr) 2002-10-29 2005-09-21 JFE Steel Corporation Procede de fabrication d'une tole d'acier magnetique a grains orientes et tole correspondante
JP2009228118A (ja) * 2008-03-25 2009-10-08 Jfe Steel Corp 方向性電磁鋼板の製造方法

Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2016035530A1 (fr) * 2014-09-01 2016-03-10 新日鐵住金株式会社 Tôle d'acier électromagnétique à grains orientés
US11377705B2 (en) 2014-09-01 2022-07-05 Nippon Steel Corporation Grain-oriented electrical steel sheet
US10604818B2 (en) 2014-09-01 2020-03-31 Nippon Steel Corporation Grain-oriented electrical steel sheet
CN108138291A (zh) * 2015-10-26 2018-06-08 新日铁住金株式会社 方向性电磁钢板及用于其制造的脱碳钢板
JPWO2017073615A1 (ja) * 2015-10-26 2018-08-16 新日鐵住金株式会社 方向性電磁鋼板及びその製造に用いる脱炭鋼板
WO2017073615A1 (fr) * 2015-10-26 2017-05-04 新日鐵住金株式会社 Tôle d'acier électromagnétique à grains orientés et tôle d'acier décarburé utilisée pour produire celle-ci
CN108138291B (zh) * 2015-10-26 2020-06-05 日本制铁株式会社 方向性电磁钢板及用于其制造的脱碳钢板
US10907234B2 (en) 2015-10-26 2021-02-02 Nippon Steel Corporation Grain-oriented electrical steel sheet and decarburized steel sheet used for manufacturing the same
JP2019505671A (ja) * 2015-12-21 2019-02-28 ポスコＰｏｓｃｏ 方向性電磁鋼板及びその製造方法
CN106298221B (zh) * 2016-08-30 2018-01-30 河南中岳非晶新型材料股份有限公司 非晶体抗直流铁芯及其热处理方法
CN106298221A (zh) * 2016-08-30 2017-01-04 河南中岳非晶新型材料股份有限公司 非晶体抗直流铁芯及其热处理方法
CN108277429A (zh) * 2017-01-05 2018-07-13 鞍钢股份有限公司 一种高硅电工钢的生产方法
JP2019019359A (ja) * 2017-07-13 2019-02-07 新日鐵住金株式会社 皮膜密着性に優れる一方向性珪素鋼板及びその製造方法
JP2019019358A (ja) * 2017-07-13 2019-02-07 新日鐵住金株式会社 皮膜密着性に優れる一方向性電磁鋼板及びその製造方法
US20190032168A1 (en) * 2017-07-25 2019-01-31 Hyundai Motor Company Continuous annealing apparatus
US10597749B2 (en) * 2017-07-25 2020-03-24 Hyundai Motor Company Continuous annealing apparatus

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