EP1752548B1 - Procédé de fabrication de bande en acier magnétique à grains orientés - Google Patents

Procédé de fabrication de bande en acier magnétique à grains orientés Download PDF

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Publication number
EP1752548B1
EP1752548B1 EP05016834.3A EP05016834A EP1752548B1 EP 1752548 B1 EP1752548 B1 EP 1752548B1 EP 05016834 A EP05016834 A EP 05016834A EP 1752548 B1 EP1752548 B1 EP 1752548B1
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EP
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Prior art keywords
strip
hot
strand
anyone
annealing
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EP05016834.3A
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German (de)
English (en)
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EP1752548A1 (fr
Inventor
Klaus Günther
Ludger Lahn
Andreas Ploch
Eberhard Sowka
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to PL05016834T priority Critical patent/PL1752548T3/pl
Priority to SI200532060A priority patent/SI1752548T1/sl
Priority to HUE05016834A priority patent/HUE027079T2/en
Priority to EP05016834.3A priority patent/EP1752548B1/fr
Priority to US11/997,668 priority patent/US8038806B2/en
Priority to BRPI0614374-1A priority patent/BRPI0614374B1/pt
Priority to JP2008524480A priority patent/JP2009503264A/ja
Priority to PCT/EP2006/064479 priority patent/WO2007014867A1/fr
Priority to AU2006274900A priority patent/AU2006274900B2/en
Priority to CA2616088A priority patent/CA2616088C/fr
Priority to RU2008107949/02A priority patent/RU2383634C2/ru
Priority to MX2008001413A priority patent/MX2008001413A/es
Priority to CN2006800287931A priority patent/CN101238226B/zh
Priority to KR1020087005313A priority patent/KR101365652B1/ko
Priority to TW095127714A priority patent/TWI402352B/zh
Publication of EP1752548A1 publication Critical patent/EP1752548A1/fr
Priority to ZA200800662A priority patent/ZA200800662B/xx
Publication of EP1752548B1 publication Critical patent/EP1752548B1/fr
Application granted granted Critical
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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
    • 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
    • C21D8/1261—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 following hot rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • 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

Definitions

  • the invention relates to a process for preparing high-quality grain oriented electrical steel, so-called CGO material (C onventional G rain O riented - material) on the basis of thin-slab continuous casting.
  • CGO material C onventional G rain O riented - material
  • thin-slab continuous casting plants are particularly suitable for the production of electrical steel sheets due to the favorable temperature control made possible by the in-line processing of thin slabs.
  • JP 2002212639 A describes a process for the production of grain-oriented electrical steel in which from a melt containing (in mass%) in addition to 2.5 - 4.0% Si and 0.02 - 0.20% Mn as essential inhibitor components 0.0010 - 0.0050% C, 0.002 - 0.010% Al and contents of S and Se and other optional alloying constituents, such as Cu, Sn, Sb, P, Cr, Ni, Mo and Cd, remainder iron and unavoidable impurities, having thin slabs with a thickness of 30 mm to 140 mm are produced.
  • the thin slabs are annealed before hot rolling at a temperature of 1000 ° C to 1250 ° C in order to achieve optimum magnetic properties on the finished electrical steel sheet.
  • the known method provides that the 1.0 mm to 4.5 mm thick hot strip after hot rolling at temperatures of 950 ° C to 1150 ° C for 30 sec to 600 sec is annealed, before it at degrees of deformation of 50% to 85% is rolled to cold strip.
  • CGO material C onventional G rain O Riented - material
  • JP 56-158816 A JP 56-158816 A known.
  • the hot rolling of these thin slabs is started before their temperature drops below 700 ° C.
  • the thin slabs are rolled to a hot strip with a thickness of 1.5 - 3 mm.
  • the thin slabs are rolled to hot strip with a thickness of 1.5 - 3.5 mm.
  • This hot strip thickness has the disadvantage here that the commercial for grain-oriented electrical sheet standard end thicknesses below 0.35 mm only by Kaltwalzgrade above 76% in single-stage cold rolling or conventional multi-stage cold rolling can be produced with intermediate annealing, which is disadvantageous in this operation that the high degree of cold work is not matched to the relatively weak inhibition by MnS and MnSe. This leads to unstable and unsatisfactory magnetic properties of the finished product.
  • a complex and expensive multi-stage cold rolling process with intermediate annealing must be accepted.
  • Temperature is cooled above 700 ° C and divided into thin slabs.
  • the hot rolling parameters are chosen so that the material always remains sufficiently ductile.
  • the ductility is greatest when the strand is cooled after solidification up to about 800 ° C, then only relatively briefly to equilibrium temperature, z. B. 1150 ° C, dwells while being thoroughly heated through.
  • An optimal hot rollability of such a material is therefore given when the first forming pass takes place at temperatures below 1150 ° C and with a degree of deformation of at least 20% and the rolling stock from an intermediate thickness of 40 mm to 8 mm by means of high-pressure inter-frame cooling devices within of not more than two successive Umststichen is brought to rolling temperatures of below 1000 ° C. This avoids that the rolling stock is converted by 1000 ° C in the temperature range critical for ductility.
  • the hot strip thus obtained is then cold rolled one or more stages with recrystallizing intermediate annealing to a final thickness in the range of 0.15 to 0.50 mm.
  • This cold strip is finally recrystallized and decarburizing annealed, provided with a predominantly Mg0 containing Glühseparator and then finally annealed to the expression of a Gosstextur.
  • the tape is coated with an electrical insulation and annealed stress-free.
  • the ladle furnace In this unit, the molten steel for the thin slab caster is provided and set by heating the desired dispensing temperature for potting. In addition, in the ladle furnace, the final adjustment of the chemical composition of the steel in question can be made by adding alloying elements. In addition, the slag is usually conditioned in the ladle furnace. In the processing of aluminum-killed steels, additional small amounts of Ca are added to the molten steel in the ladle furnace in order to ensure the castability of these steels.
  • the invention therefore an object of the invention to provide a method that allows the economic production of high-quality grain-oriented electrical steel using thin slab continuous casting.
  • the predetermined by the invention sequence of operations is tuned so that, using conventional aggregates, an electrical sheet can be produced which has optimized electro-magnetic properties.
  • a molten steel is melted with known composition in the first step.
  • This melt is then treated by secondary metallurgy.
  • This treatment is preferably first carried out in a vacuum plant to adjust the chemical composition of the steel to the required narrow analytical margins and to achieve low hydrogen contents of at most 10 ppm in order to minimize the risk of strand breakage during casting of molten steel.
  • the use of a ladle furnace for slag conditioning would also first be followed by treatment in a vacuum system for adjusting the chemical composition of the molten steel within narrow analytical limits.
  • this combination has the disadvantage that, in the case of casting delays, the temperature of the melt drops to such an extent that the molten steel can no longer be cast.
  • the invention further, only use the vacuum system. On the one hand, however, this involves the risk that, in the case of casting delays, the temperature of the melt drops to such an extent that the molten steel can no longer be cast. On the other hand, there is a risk that the immersion spouts clog in the sequence and thus the sequence must be canceled.
  • both systems are thus used in combination with the availability of ladle furnace and vacuum system depending on the respective melting metallurgical and casting requirements.
  • a strand is then poured, which preferably has a thickness of 25 mm to 150 mm.
  • the molten steel is poured in a continuous casting mold, which is equipped with an electromagnetic brake, such errors can be largely avoided.
  • a brake causes a calming and homogenization of the flow in the mold, especially in the bathroom mirror area by generating a magnetic field, which reduces in interaction with the pouring jets entering the mold their speed due to the effect of the so-called "Lorenzkraft".
  • the formation of a microstructure of the cast steel strand which is favorable with regard to the electromagnetic properties can also be assisted by casting at a low superheating temperature.
  • the latter are preferably at most 25 K above the liquidus temperature of the cast melt. If this advantageous variant of the invention is taken into account, a freezing of the molten steel cast at low superheat at the bath level and hence casting disturbances up to the casting break can likewise be avoided by using an electromagnetic brake on the casting mold.
  • the force exerted by the electromagnetic brake directs the hot melt to the bath level and there causes a temperature increase sufficient to ensure a smooth casting process.
  • the homogeneous and fine-grained solidification structure of the cast strand achieved in this way has a favorable effect on the magnetic properties of the grain-oriented electrical steel produced according to the invention.
  • LCR Liquid Core Reduction
  • SR Soft Reduction
  • the strand thickness is reduced at the core liquid inside the strand just below the mold.
  • LCR is used in the prior art in thin slab continuous casters primarily to achieve lower hot strip thicknesses, especially for higher strength steels.
  • the reduction in the number of stitches and the rolling forces in the rolling mills of the hot strip mill can be reduced with the result that the work roll wear of the rolling mills and the slumpiness of the hot strip can be reduced and the strip run can be improved.
  • the thickness reduction achieved by LCR according to the invention is preferably in the range of 5 mm to 30 mm.
  • SR Under SR is meant the targeted reduction in thickness of the strand in the swamp tip near Enderstarrung.
  • the SR aims to reduce mitigation and core porosity. This method has hitherto been used predominantly in billet and slab continuous casting plants.
  • the usually emerging from the casting mold strand is bent at lower points and guided in a horizontal direction.
  • the strand cast from the melt is bent and straightened at a temperature of 700 ° C. to 1000 ° C. (preferably 850 to 950 ° C.), cracks may be formed on the surface of the thin slabs separated from the strand avoided, which may otherwise occur, in particular, as a result of edge cracks of the strand.
  • the steel used according to the invention has a good ductility at the strand surface or in the edge region, so that it can follow well the deformations occurring during bending and straightening.
  • the cast strand thin slabs are divided in a conventional manner, which are then heated in an oven to the appropriate hot rolling start temperature and then fed to hot rolling.
  • the temperature at which the thin slabs enter the furnace is preferably above 650 ° C.
  • the residence time in the oven should be less than 60 minutes in order to avoid adhesive scale.
  • the first pass of the hot rolling is carried out at 900 to 1200 ° C. in order to be able to realize the degree of deformation of> 40% in this pass.
  • a degree of deformation of at least 40% is achieved in the first forming pass of the hot rolling to have only relatively small Stichabures in the last frameworks to achieve the desired Endbanddicke necessary.
  • the use of high reduction rates (degrees of deformation) in the first two stands causes the required conversion of the coarse-grained solidification microstructure into a fine rolling structure, which is the prerequisite for good magnetic properties of the final product to be produced.
  • the reduction in stitching in the last stand should be limited to a maximum of 30%, preferably less than 20%, and it is also favorable for an optimum in terms of the desired properties warm rolling result, if the reduction in the penultimate stand of the finishing mill is less than 25% .
  • a pass plan tested in practice on a seven-stand finished hot rolling mill which has led to optimum properties of the finished electrical sheet, provides that with a pre-strip thickness of 63 mm and a hot-strip thickness of 2 mm, the degree of deformation achieved at the first stand is 62%, that at the second stand achieved 54%, the third scaffold 47%, the fourth scaffold 35%, the fifth scaffold 28%, the sixth scaffold 17% and the seventh scaffold 11%.
  • an early onset of cooling of the hot strip behind the last rolling stand of the finishing train is advantageous. According to a practical embodiment of the invention, it is therefore intended to start within a maximum of five seconds after leaving the last mill stand with the water cooling.
  • the aim is to have the shortest possible break times, for example, of one second and less.
  • the cooling of the hot strip can also be controlled so that it is cooled in two stages with water. For this purpose, first after the last rolling mill to a temperature close to the alpha / gamma transformation temperature can be cooled to then, preferably after to equalize the temperature over the tape thickness inserted cooling pause of one to five seconds, a further cooling by water until to perform the required reel temperature.
  • the first phase of the cooling can take place as a so-called "compact cooling", in which the hot strip is cooled rapidly over a short conveyor line with high intensity and cooling rate (at least 200 K / s) while discharging large amounts of water, while in the second phase of the Water cooling is cooled over a longer conveyor line with reduced intensity in order to achieve the most uniform possible cooling over the belt cross-section.
  • the reel temperature should preferably be in the temperature range of 500-780 ° C. Overlying temperatures would on the one hand lead to undesirably coarse precipitates and on the other hand worsen the treatability.
  • a so-called short distance reel is used, which is located directly after the compact cooling zone.
  • the hot strip thus produced can optionally be annealed after reeling or before cold rolling.
  • cold rolling of the hot strip is carried out in several stages, it may be expedient to perform an intermediate annealing between the stages of cold rolling.
  • the strip obtained is annealed recrystallizing and decarburizing.
  • the cold rolled strip may or may not be peeled off during or after annealed to the decarburization annealing in a NH 3 -containing atmosphere.
  • N-containing antacid additives such as manganese nitride or chromium nitride
  • the cooling was identical for both hot rolling variants with the use of water spraying within 7 s after leaving the last stand and a coiler temperature of 610 ° C.
  • samples for metallographic examinations were also produced by hot rolling after the 2nd pass was stopped by rapid cooling.

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

Claims (11)

  1. Procédé de fabrication d'une bande d'acier magnétique à grains orientés à base d'une coulée continue de lingot mince, comprenant les étapes suivantes :
    a) la fusion d'un acier constitué par, outre du fer et des impuretés inévitables (en % en masse) :
    Si : 2,5 à 4,0 %
    C:0,01 à 0,10%
    Mn : 0,02 à 0,50 %
    S et Se en teneurs dont la somme est de 0,005 à 0,04 %,
    au choix
    - jusqu'à 0,07 % d'Al,
    - jusqu'à 0,015 % de N,
    - jusqu'à 0,035 % de Ti,
    - jusqu'à 0,3 % de P,
    - un ou plusieurs éléments du groupe As, Sn, Sb, Te, Bi en teneurs respectives de jusqu'à 0,2 %,
    - un ou plusieurs éléments du groupe Cu, Ni, Cr, Co, Mo en teneurs respectives de jusqu'à 0,3 %,
    - un ou plusieurs éléments du groupe B, V, Nb en teneurs respectives de jusqu'à 0,012 %,
    b) le traitement métallurgique secondaire de la masse fondue dans une unité sous vide et un four poche,
    c) la coulée continue de la masse fondue en un cordon,
    d) la fragmentation du cordon en lingots minces,
    e) le chauffage des lingots minces dans un four en ligne à une température comprise entre 1 050 °C et 1 300 °C,
    - dans lequel le temps de séjour dans le four étant d'au plus 60 min,
    f) le laminage à chaud continu des lingots minces dans un laminoir à chaud en ligne à plusieurs cages en une bande chaude d'une épaisseur de 0,5 à 4,0 mm,
    - le premier passage de déformation pendant ce laminage à chaud étant réalisé à une température de 900 à 1 200 °C à un degré de déformation de plus de 40,
    - la réduction lors du deuxième passage de déformation étant de plus 30%,
    - la réduction lors du dernier passage de déformation du cylindrage à chaud étant d'au plus 30 %,
    g) le refroidissement de la bande chaude,
    h) l'enroulement de la bande chaude en une bobine,
    i) au choix : le recuit de la bande chaude après l'enroulement ou avant le laminage à froid,
    j) le laminage à froid de la bande chaude en une bande froide d'une épaisseur finale de 0,15 mm à 0,50 mm,
    k) le recuit de recristallisation et décarbonisation de la bande à froid,
    l) l'application d'un séparateur de recuit sur la surface de la bande,
    m) le recuit final de la bande froide ayant subi un recuit de recristallisation et décarbonisation pour la formation d'une structure de Goss,
    n) au choix : le revêtement de la bande froide ayant subi un recuit final avec un isolement électrique, puis le recuit de détente de la bande froide revêtue,
    o) au choix : l'affinage des domaines de la bande froide revêtue.
  2. Procédé selon la revendication 1, caractérisé en ce que la masse fondue d'acier est tout d'abord traitée dans l'unité sous vide, puis dans le four poche au cours de son traitement métallurgique secondaire (étape b).
  3. Procédé selon la revendication 1, caractérisé en ce que la masse fondue est traitée en alternance dans le four poche et dans l'unité sous vide au cours de son traitement métallurgique secondaire (étape b).
  4. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le traitement métallurgique secondaire (étape b) de la masse fondue est poursuivi jusqu'à ce que sa teneur en hydrogène lors de la coulée (étape c) soit d'au plus 10 ppm.
  5. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la masse fondue d'acier est coulée pour former le cordon dans une lingotière de moulage de cordon (étape c) munie d'un frein électromagnétique.
  6. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce qu'au cours de l'étape c), une réduction d'épaisseur intégré en ligne du cordon coulé à partir de la masse fondue, mais toutefois encore liquide au centre, est réalisée.
  7. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le cordon coulé à partir de la masse fondue est incurvé et aligné au cours de l'étape c) à une température de 700 °C à 1 000 °C (de préférence 850 °C à 950 °C).
  8. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le cordon entre dans le four d'équilibrage à une température supérieure à 650 °C.
  9. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le refroidissement accéléré de la bande chaude débute au plus cinq secondes après la sortie du dernier laminoir.
  10. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la bande froide est nitrée pendant la décarbonisation ou après la décarbonisation par recuit dans une atmosphère contenant de l'ammoniac.
  11. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce qu'un ou plusieurs composés chimiques sont ajoutés au séparateur de recuit, qui provoquent une nitration de la bande froide pendant la phase de chauffage du recuit final jusqu'à la recristallisation secondaire.
EP05016834.3A 2005-08-03 2005-08-03 Procédé de fabrication de bande en acier magnétique à grains orientés Active EP1752548B1 (fr)

Priority Applications (16)

Application Number Priority Date Filing Date Title
PL05016834T PL1752548T3 (pl) 2005-08-03 2005-08-03 Sposób wytwarzania taśmy elektrotechnicznej o zorientowanych ziarnach
SI200532060A SI1752548T1 (sl) 2005-08-03 2005-08-03 Metoda za proizvodnjo magnetnega zrnato usmerjenega jeklenega traku
HUE05016834A HUE027079T2 (en) 2005-08-03 2005-08-03 A method for producing magnetizable, grain oriented steel strip
EP05016834.3A EP1752548B1 (fr) 2005-08-03 2005-08-03 Procédé de fabrication de bande en acier magnétique à grains orientés
AU2006274900A AU2006274900B2 (en) 2005-08-03 2006-07-20 Method for producing a grain-oriented electrical steel strip
KR1020087005313A KR101365652B1 (ko) 2005-08-03 2006-07-20 방향성 전자 강 스트립 제조 방법
JP2008524480A JP2009503264A (ja) 2005-08-03 2006-07-20 方向性電磁鋼ストリップの製造方法
PCT/EP2006/064479 WO2007014867A1 (fr) 2005-08-03 2006-07-20 Procede de production d'une bande magnetique a grains orientes
US11/997,668 US8038806B2 (en) 2005-08-03 2006-07-20 Method for producing grain oriented magnetic steel strip
CA2616088A CA2616088C (fr) 2005-08-03 2006-07-20 Procede de production d'une bande magnetique en acier a grains orientes
RU2008107949/02A RU2383634C2 (ru) 2005-08-03 2006-07-20 Способ получения электротехнической полосовой стали с ориентированным зерном
MX2008001413A MX2008001413A (es) 2005-08-03 2006-07-20 Metodo para producir una tira de acero electrica de grano orientado.
CN2006800287931A CN101238226B (zh) 2005-08-03 2006-07-20 生产晶粒取向的电工带钢的方法
BRPI0614374-1A BRPI0614374B1 (pt) 2005-08-03 2006-07-20 Método para produção de tira de aço magnética com grão orientado
TW095127714A TWI402352B (zh) 2005-08-03 2006-07-28 製造晶粒取向性磁鋼帶的方法（一）
ZA200800662A ZA200800662B (en) 2005-08-03 2008-01-22 Method for producing a grain-oriented electrical steel strip

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP05016834.3A EP1752548B1 (fr) 2005-08-03 2005-08-03 Procédé de fabrication de bande en acier magnétique à grains orientés

Publications (2)

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EP1752548A1 EP1752548A1 (fr) 2007-02-14
EP1752548B1 true EP1752548B1 (fr) 2016-02-03

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Country Status (16)

Country Link
US (1) US8038806B2 (fr)
EP (1) EP1752548B1 (fr)
JP (1) JP2009503264A (fr)
KR (1) KR101365652B1 (fr)
CN (1) CN101238226B (fr)
AU (1) AU2006274900B2 (fr)
BR (1) BRPI0614374B1 (fr)
CA (1) CA2616088C (fr)
HU (1) HUE027079T2 (fr)
MX (1) MX2008001413A (fr)
PL (1) PL1752548T3 (fr)
RU (1) RU2383634C2 (fr)
SI (1) SI1752548T1 (fr)
TW (1) TWI402352B (fr)
WO (1) WO2007014867A1 (fr)
ZA (1) ZA200800662B (fr)

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JP2009503264A (ja) 2009-01-29
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RU2383634C2 (ru) 2010-03-10
KR20080042860A (ko) 2008-05-15
US20090139609A1 (en) 2009-06-04
BRPI0614374A2 (pt) 2011-03-22
AU2006274900A1 (en) 2007-02-08
CA2616088C (fr) 2015-05-05
EP1752548A1 (fr) 2007-02-14
CN101238226B (zh) 2011-07-13
AU2006274900B2 (en) 2011-07-28
CA2616088A1 (fr) 2007-02-08
RU2008107949A (ru) 2009-09-10
US8038806B2 (en) 2011-10-18
KR101365652B1 (ko) 2014-02-19
SI1752548T1 (sl) 2016-09-30
WO2007014867A1 (fr) 2007-02-08
TW200710225A (en) 2007-03-16
ZA200800662B (en) 2009-07-29
HUE027079T2 (en) 2016-10-28
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CN101238226A (zh) 2008-08-06
BRPI0614374B1 (pt) 2014-04-29

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