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EP1752549B1 - Procédé de fabrication de bande d'acier magnétique à grains orientés - Google Patents

Procédé de fabrication de bande d'acier magnétique à grains orientés Download PDF

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Publication number
EP1752549B1
EP1752549B1 EP05016835.0A EP05016835A EP1752549B1 EP 1752549 B1 EP1752549 B1 EP 1752549B1 EP 05016835 A EP05016835 A EP 05016835A EP 1752549 B1 EP1752549 B1 EP 1752549B1
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EP
European Patent Office
Prior art keywords
strip
hot
strand
annealing
anyone
Prior art date
Legal status (The legal status 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 status listed.)
Expired - Lifetime
Application number
EP05016835.0A
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German (de)
English (en)
Other versions
EP1752549A1 (fr
Inventor
Klaus Günther
Ludger Lahn
Andreas Ploch
Eberhard Sowka
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Steel Europe AG
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
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Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to PL05016835T priority Critical patent/PL1752549T3/pl
Priority to EP05016835.0A priority patent/EP1752549B1/fr
Priority to SI200532056A priority patent/SI1752549T1/sl
Priority to JP2008524481A priority patent/JP2009503265A/ja
Priority to CN2006800288008A priority patent/CN101238227B/zh
Priority to PCT/EP2006/064480 priority patent/WO2007014868A1/fr
Priority to BRPI0614379-2A priority patent/BRPI0614379B1/pt
Priority to US11/997,670 priority patent/US8088229B2/en
Priority to KR1020087005312A priority patent/KR101365653B1/ko
Priority to CA2615586A priority patent/CA2615586C/fr
Priority to RU2008107938/02A priority patent/RU2407807C2/ru
Priority to MX2008001475A priority patent/MX2008001475A/es
Priority to AU2006274901A priority patent/AU2006274901B2/en
Priority to TW095127715A priority patent/TWI402353B/zh
Publication of EP1752549A1 publication Critical patent/EP1752549A1/fr
Priority to ZA200800663A priority patent/ZA200800663B/xx
Publication of EP1752549B1 publication Critical patent/EP1752549B1/fr
Application granted granted Critical
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Classifications

    • 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
    • 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
    • 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
    • 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

Definitions

  • the invention relates to a process for the production of high-quality grain-oriented electrical steel, in particular for the production of so-called HGO material ( Highly G rain O riented - material) based on thin slab continuous casting.
  • HGO material Highly 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.
  • 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 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 economical production of high-quality grain-oriented electrical steel sheet (especially HGO) using thin slab continuous casting plants.
  • 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.
  • the aim is to avoid the formation of nitridic precipitates prior to hot rolling and during hot rolling as much as possible in order to make extensive use of the possibility of a controlled production of such precipitates during the cooling of the hot strip.
  • it is provided according to an advantageous embodiment of the invention to make an inline thickness reduction of cast from the melt, but still core liquid strand.
  • 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.
  • An aspect of the invention which is essential in view of the desired production of HGO material is that the hot rolling is carried out following the first forming pass in the two-phase region ( ⁇ / ⁇ ). Also, this measure has the goal of reducing the formation of nitridic precipitates in the course of hot rolling as far as possible in order to be able to control these precipitates specifically via the cooling conditions on the outlet roller table behind the last mill stand of the hot strip mill.
  • hot rolled at temperatures where mixed in the structure of the hot strip austenitic and ferritic shares are above approximately 800 ° C., in particular in the range from 850 ° C. to 1150 ° C.
  • the AIN In the ⁇ phase, the AIN is kept in solution at these temperatures.
  • Another positive aspect of hot rolling in the two-phase mixed area is the grain refining effect.
  • 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. Accordingly, the reduction should be in last frame to a maximum of 30%, preferably less than 20%, are limited, and it is also favorable for an optimal in terms of the desired properties warm rolling result, if the reduction in the penultimate framework of the finishing mill is less than 25%.
  • a pass plan tested in practice on a seven-stand finish 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 on the first stand is 62%, that on 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 inventive method in the production of the hot strip is preferably carried out so that the hot strip obtained sulfide and / or nitridic precipitates having a mean particle diameter less than 150 nm and a mean density of at least 0.05 .mu.m -2 is reached.
  • This type of hot strip has optimal conditions for the effective control of grain growth during the subsequent process steps.
  • the hot strip thus produced can optionally be annealed after reeling or before cold rolling.
  • the strip obtained is annealed recrystallizing and decarburizing.
  • the cold rolled strip may be annealed during or after decarburization annealing in an NH 3 -containing atmosphere.
  • N-containing adhesive protection additives such as manganese nitride or chromium nitride to the cold strip after the decarburization annealing with the Indiffusion of the nitrogen into the strip during the heating phase of the final annealing until secondary recrystallization.
  • 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 650 ° C.
  • samples for metallographic examinations were also produced by hot rolling after the second pass was stopped by rapid cooling.
  • Hot rolling conditions Decarburizing variant magnetic result variant ⁇ 2 [%] ⁇ 3 [%] ⁇ 6 [%] ⁇ 7 [%] J 800 [T] P 1.7 [W / kg] comment "WW1" 25 20 14 12 E1 (without embroidery) 1.89 1.10 inventively “WW1” E2 (with embroidery) 1.93 0.98 “WW2" 20 15 8th 7 E1 (without embroidery) 1.50 1.90 not according to the invention "WW2" E2 (with embroidery) 1.74 1.68

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

Claims (11)

  1. Procédé de fabrication d'une bande d'acier électrique 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: 0,02 à 0,10 %,
    Al : 0,01 à 0,065 %
    N : 0,003 à 0,015 %
    Optionnel - jusqu'à 0,30 % de Mn,
    - jusqu'à 0,05 % de Ti,
    - jusqu'à 0,3 % de P,
    - un ou plusieurs éléments du groupe S, Se en teneurs dont la somme est d'au plus 0,04 %,
    - 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 0,5 %,
    - 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,
    - 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 du plusieurs cages en ligne multiple 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,
    - au moins les 2 passages de déformation suivants du laminage à chaud étant laminés dans la zone de mélange à deux phases (α-y),
    - la réduction du passage lors du dernier passage de déformation du laminage 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) optionnel : 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) optionnel : 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) optionnel: 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) ; en variante, l'ordre four poche tout d'abord, puis unité sous vide peut également être choisi, ainsi qu'un traitement métallurgique secondaire exclusif uniquement dans l'unité sous vide ou uniquement dans le four poche.
  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 coulé dans une lingotière de coulée continue (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 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 fondu 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 coulé entre dans le four de compensation 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.
EP05016835.0A 2005-08-03 2005-08-03 Procédé de fabrication de bande d'acier magnétique à grains orientés Expired - Lifetime EP1752549B1 (fr)

Priority Applications (15)

Application Number Priority Date Filing Date Title
PL05016835T PL1752549T3 (pl) 2005-08-03 2005-08-03 Sposób wytwarzania taśmy elektrotechnicznej o zorientowanych ziarnach
EP05016835.0A EP1752549B1 (fr) 2005-08-03 2005-08-03 Procédé de fabrication de bande d'acier magnétique à grains orientés
SI200532056A SI1752549T1 (sl) 2005-08-03 2005-08-03 Postopek za proizvodnjo zrnato usmerjene magnetne jeklene vzmeti
KR1020087005312A KR101365653B1 (ko) 2005-08-03 2006-07-20 방향성 전자 강 스트립 제조 방법
AU2006274901A AU2006274901B2 (en) 2005-08-03 2006-07-20 Method for producing a grain-oriented electrical steel strip
PCT/EP2006/064480 WO2007014868A1 (fr) 2005-08-03 2006-07-20 Procede de production d'une bande magnetique a grains orientes
BRPI0614379-2A BRPI0614379B1 (pt) 2005-08-03 2006-07-20 Método para produção de tira de aço magnética de grãos orientados
US11/997,670 US8088229B2 (en) 2005-08-03 2006-07-20 Method for producing grain oriented magnetic steel strip
JP2008524481A JP2009503265A (ja) 2005-08-03 2006-07-20 方向性電磁鋼ストリップの製造方法
CA2615586A CA2615586C (fr) 2005-08-03 2006-07-20 Procede de production d'une bande magnetique a grains orientes
RU2008107938/02A RU2407807C2 (ru) 2005-08-03 2006-07-20 Способ изготовления структурно-ориентированной стальной магнитной полосы
MX2008001475A MX2008001475A (es) 2005-08-03 2006-07-20 Metodo para producir una cinta de acero electrica de grano orientado.
CN2006800288008A CN101238227B (zh) 2005-08-03 2006-07-20 生产晶粒取向的电工带钢的方法
TW095127715A TWI402353B (zh) 2005-08-03 2006-07-28 製造晶粒取向性磁鋼帶的方法（二）
ZA200800663A ZA200800663B (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
EP05016835.0A EP1752549B1 (fr) 2005-08-03 2005-08-03 Procédé de fabrication de bande d'acier magnétique à grains orientés

Publications (2)

Publication Number Publication Date
EP1752549A1 EP1752549A1 (fr) 2007-02-14
EP1752549B1 true EP1752549B1 (fr) 2016-01-20

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WO2020193717A1 (fr) 2019-03-26 2020-10-01 Thyssenkrupp Electrical Steel Gmbh Matériau en fer-silicium approprié pour des applications à moyenne fréquence
RU2818560C1 (ru) * 2020-07-23 2024-05-02 Смс Груп Гмбх Способ изготовления стальной полосы
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JP6631725B2 (ja) * 2016-11-01 2020-01-15 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
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DE102017220718A1 (de) 2017-11-20 2019-05-23 Thyssenkrupp Ag Optimierung des Stickstofflevels während der Haubenglühung II
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PL3856938T3 (pl) 2018-09-26 2024-07-29 Thyssenkrupp Electrical Steel Gmbh Sposób wytwarzania taśmy elektrotechnicznej o ziarnie zorientowanym zaopatrzonej w warstwę izolacyjną i taśma elektrotechniczna o ziarnie zorientowanym
KR102142511B1 (ko) * 2018-11-30 2020-08-07 주식회사 포스코 방향성 전기강판 및 그의 제조방법
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WO2020193634A1 (fr) 2019-03-26 2020-10-01 Thyssenkrupp Electrical Steel Gmbh Procédé à mélange pauvre pour la recristallisation secondaire d'acier électrique à grains orientés dans une ligne de traitement continu
WO2020193717A1 (fr) 2019-03-26 2020-10-01 Thyssenkrupp Electrical Steel Gmbh Matériau en fer-silicium approprié pour des applications à moyenne fréquence
RU2818560C1 (ru) * 2020-07-23 2024-05-02 Смс Груп Гмбх Способ изготовления стальной полосы
EP4365319A1 (fr) 2022-11-03 2024-05-08 Thyssenkrupp Electrical Steel Gmbh Bande d'acier électrique à grains orientés et son procédé de fabrication

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AU2006274901A1 (en) 2007-02-08
ZA200800663B (en) 2009-04-29
KR101365653B1 (ko) 2014-02-19
BRPI0614379B1 (pt) 2014-04-29
CA2615586A1 (fr) 2007-02-08
US8088229B2 (en) 2012-01-03
CN101238227A (zh) 2008-08-06
US20080216985A1 (en) 2008-09-11
TW200710226A (en) 2007-03-16
WO2007014868A1 (fr) 2007-02-08
JP2009503265A (ja) 2009-01-29
SI1752549T1 (sl) 2016-09-30
MX2008001475A (es) 2008-04-02
TWI402353B (zh) 2013-07-21
CN101238227B (zh) 2011-11-16
EP1752549A1 (fr) 2007-02-14
RU2008107938A (ru) 2009-09-10
RU2407807C2 (ru) 2010-12-27
KR20080042859A (ko) 2008-05-15
AU2006274901B2 (en) 2011-07-28
BRPI0614379A2 (pt) 2011-03-22
CA2615586C (fr) 2015-04-21
PL1752549T3 (pl) 2017-08-31

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