WO1998002590A1 - Process for producing a grain-orientated electrical steel sheet - Google Patents

Process for producing a grain-orientated electrical steel sheet Download PDF

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Publication number
WO1998002590A1
WO1998002590A1 PCT/EP1997/003509 EP9703509W WO9802590A1 WO 1998002590 A1 WO1998002590 A1 WO 1998002590A1 EP 9703509 W EP9703509 W EP 9703509W WO 9802590 A1 WO9802590 A1 WO 9802590A1
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temperature
cold
strip
range
hot
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PCT/EP1997/003509
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German (de)
French (fr)
Inventor
Manfred Espenhahn
Andreas Böttcher
Klaus Günther
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Thyssen Stahl Ag
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Priority to AU36928/97A priority Critical patent/AU3692897A/en
Publication of WO1998002590A1 publication Critical patent/WO1998002590A1/en

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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 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
    • C21D8/1233—Cold 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
    • C21D8/1216—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
    • C21D8/1205—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
    • 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 method for producing grain-oriented electrical sheet, in which a slab made of steel with (in mass%) more than 0.005 to 0.10% C,
  • Contamination is heated at a temperature lower than the solubility temperature for manganese sulfides, in any case below 1320 ° C, but above the solubility temperature for copper sulfides, with an initial temperature of at least 960 ° C and a final temperature in the range of 880 is hot rolled to a final hot strip thickness in the range from 1.5 to 7.0 mm, the hot strip is then annealed for 100 to 600 ⁇ at a temperature in the range from 880 to 1150 ° C, then with a cooling rate of greater cooled to 15 K / ⁇ and cold rolled to the final cold strip thickness in one or more cold rolling steps.
  • the cold strip is then subjected to a recrystallizing annealing in a humid hydrogen and nitrogen-containing atmosphere with simultaneous decarburization, after the double-sided application of a release agent essentially containing MgO, annealed at high temperature and finally annealed after the application of an insulating coating.
  • Grain-oriented electrical sheet has a structure made of grains with a very sharp, preferred orientation ⁇ 110 ⁇ ⁇ 001>, a so-called Goss texture.
  • the easiest magnetizable direction is parallel to the rolling direction, which is the main direction of magnetization in technical applications.
  • the aim in the development and production of grain-oriented electrical steel is to make the pour orientation as sharp as possible.
  • the magnetic polarization as a material parameter is higher the sharper the orientation of the cast.
  • the formation of this cast texture takes place via a grain growth selection process which is initiated by a so-called control phase. This consists of finely divided particles of a foreign phase, which generally hinder the grain boundary movement in the course of an annealing treatment and thus grain growth.
  • the particles must have very small diameters of less than 100 nm. In the course of long-term annealing, however, they lose their hindering effect and bring about a very sharp selection, which only allows small grains of an initial matrix that are in Goss orientation to enable extremely rapid growth.
  • the practical implementation of this known method provides magnetic values which scatter in different ways in the production of large quantities.
  • the object of the invention is therefore to supplement the known method according to DE 43 11 151 in such a way that the spread of the magnetic values is considerably reduced.
  • this object is achieved by setting the degree of deformation in the last cold rolling step to a value in the range from 83 to 86% in the generic method. If this degree of deformation is below or above the range mentioned, good magnetic properties can also be achieved, but with such strong scatter that unsatisfactory results can occur in individual cases.
  • Table 1 contains the chemical compositions of the melts examined. They represent a typical selection. From these melts, slabs were produced in the same way by continuous casting and hot strips were then produced by hot rolling. The hot strip thickness was varied in a range from 2.00 to 2.85 mm. After annealing these hot strips at 1080 ° C for 240 s and then accelerating them, the hot strips were cold-rolled to finished strip thicknesses of 0.30 and 0.23 mm. Alternatively, some of the hot strips were first cold rolled at 1080 ° C. before the annealing was carried out, thereby reducing their thickness to a range from 1.25 to 1.80 mm. Table 2 shows the areas of the variants created.
  • FIGS. 1 and 2 After further processing by decarburization annealing, anti-adhesive coating, high-temperature annealing and insulation coating and final annealing, the polarization values shown in FIGS. 1 and 2 were achieved. It can be seen that the best magnetic values are achieved with a degree of deformation of approximately 85% and that these values then have the least scatter.

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

Abstract

The invention relates to a process for producing a grain-orientated electrical steel sheet during which a soaked slab consisting of a silicon steel is hot-rolled. The hot strip is subsequently annealed and cold rolled. The cold strip is recrystallised and subjected to decarburising annealing, and after application of a separation agent containing MgO to both sides it is annealed at a high temperature. Insulation coating and final annealing subsequently follow. The object of the invention is to set the deformation level in the last cold rolling stage at 83 to 86 % to avoid large dispersions of the magnetic values.

Description

Verfahren zur Herstellung von kornorientiertem ElektroblechProcess for the production of grain-oriented electrical sheet
Die Erfindung betrifft ein Verfahren zur Herstellung von kornorientiertem Elektroblech, bei dem eine Bramme aus einem Stahl mit (in Masεe-%) mehr als 0,005 bis 0,10 % C,The invention relates to a method for producing grain-oriented electrical sheet, in which a slab made of steel with (in mass%) more than 0.005 to 0.10% C,
2,5 bis 4,5 % Si,2.5 to 4.5% Si,
0, 03 bis 0,15 % Mn, mehr als 0,01 bis 0,05 % S,0.03 to 0.15% Mn, more than 0.01 to 0.05% S,
0, 01 bis 0, 035 % AI,0.01 to 0.035% AI,
0, 0045 bis 0, 012 % N,0.0045 to 0.012% N,
0,02 bis 0,3 % Cu,0.02 to 0.3% Cu,
Rest Fe einschl . unvermeidbarerRest Fe incl. inevitable
Verunreinigungen bei einer Temperatur, die tiefer als die Löslichkeitstemperatur für Mangansulfide , jedenfalls unter 1320 °C, aber oberhalb der Löslichkeitstemperatur für Kupfersulfide liegt, durcherwärmt wird, im Anschluß daran mit einer Anfangs emperatur von mindestens 960 °C und mit einer Endtemperatur im Bereich von 880 bis 1000 °C bis auf Warmband-Enddicke im Bereich von 1,5 bis 7,0 mm warmgewalzt wird, das Warmband danach 100 bis 600 ε lang bei einer Temperatur im Bereich von 880 bis 1150 °C geglüht, sodann mit einer Abkühlrate von größer als 15 K/ε abgekühlt und in einem oder mehreren Kaltwalzschritten bis auf Kaltband-Enddicke kaltgewalzt wird. Darauf wird das Kaltband einer rekristallisierenden Glühung in feuchter Wasserstoff und Stickstoff enthaltender Atmosphäre mit gleichzeitiger Entkohlung unterworfen, nach dem beidseitigen Aufbringen eines im wesentlichen MgO enthaltenden Trennmittels hochtemperaturgeglüht und nach dem Aufbringen einer Isolierbeschichtung schlußgeglüht .Contamination is heated at a temperature lower than the solubility temperature for manganese sulfides, in any case below 1320 ° C, but above the solubility temperature for copper sulfides, with an initial temperature of at least 960 ° C and a final temperature in the range of 880 is hot rolled to a final hot strip thickness in the range from 1.5 to 7.0 mm, the hot strip is then annealed for 100 to 600 ε at a temperature in the range from 880 to 1150 ° C, then with a cooling rate of greater cooled to 15 K / ε and cold rolled to the final cold strip thickness in one or more cold rolling steps. The cold strip is then subjected to a recrystallizing annealing in a humid hydrogen and nitrogen-containing atmosphere with simultaneous decarburization, after the double-sided application of a release agent essentially containing MgO, annealed at high temperature and finally annealed after the application of an insulating coating.
Kornorientiertes Elektroblech besitzt ein Gefüge aus Körnern mit einer sehr scharf ausgebildeten Vorzugsorientierungsrichtung { 110 } <001> , einer sog. Goss- Textur . Dabei liegt die am leichtesten magnetisierbare Richtung parallel zur Walzrichtung, die in technischen Anwendungen die wesentliche Magnetisierungsrichtung ist. Ziel bei der Entwicklung und Erzeugung von kornorientiertem Elektroblech ist es, die Gossorientierung möglichst scharf auszubilden. Die magnetische Polarisation als Materialkenngröße ist umso höher, je schärfer die Gossorientierung vorliegt. Die Ausbildung dieser Gosstextur geschieht über einen Kornwachstums-Selektionsprozeß, der von einer sog. Steuerphase initiiert wird. Diese besteht aus fein verteilten Partikeln einer Fremdphase, die die Korngrenzenbewegung im Verlaufe einer Glühbehandlung und somit das Kornwachstum generell behindern. Für diese sehr wichtige Funktion müssen die Partikel sehr kleine Durchmesser von kleiner 100 nm besitzen. Im Verlauf der Langzeitglühung verlieren sie jedoch ihre behindernde Wirkung und bewirken eine sehr scharfe Selektion, die nur in Gossorientierung befindlichen kleinen Körnern einer Ausgangsmatrix ein extrem schnelles Wachstum ermöglicht.Grain-oriented electrical sheet has a structure made of grains with a very sharp, preferred orientation {110} <001>, a so-called Goss texture. The easiest magnetizable direction is parallel to the rolling direction, which is the main direction of magnetization in technical applications. The aim in the development and production of grain-oriented electrical steel is to make the pour orientation as sharp as possible. The magnetic polarization as a material parameter is higher the sharper the orientation of the cast. The formation of this cast texture takes place via a grain growth selection process which is initiated by a so-called control phase. This consists of finely divided particles of a foreign phase, which generally hinder the grain boundary movement in the course of an annealing treatment and thus grain growth. For this very important function, the particles must have very small diameters of less than 100 nm. In the course of long-term annealing, however, they lose their hindering effect and bring about a very sharp selection, which only allows small grains of an initial matrix that are in Goss orientation to enable extremely rapid growth.
Die meisten klassischen Sorten kornorientierten Elektroblechs benutzen MnS- und AlN-Partikel für diesen Steuerungsprozeß. Dies hat zur Folge, daß die Brammen vor dem Warmwalzvorgang nicht auf nur ca. 1250 °C vorgewärmt werden müssen, so wie dies bei Normalstahlgüten zur Herabsetzung der Streckgrenze üblich ist, sondern bis auf ca. 1400 °C, um die steuerphasenbildenden Elemente hinreichend gut in Lösung zu bringen, damit in den nachfolgenden Herstellungsschritten, wie Warmwalzen und Warmbandglühen genügend viele Partikel feinverteilt ausgeschieden werden können. Diese erhöhte Vorwärmung hat wirtschaf liche Nachteile. Deshalb wurde in der gattungsbildenden DE 43 11 151 Cl vorgeschlagen, durch die Wahl von im wesentlichen Kupfersulfid als Steuerphase auf erhöhte Vorwärmung zu verzichten und die Brammen auf Temperaturen von unter 1320 °C vorzuwärmen.Most classic types of grain-oriented electrical sheet use MnS and AlN particles for this control process. As a result, the slabs are not preheated to only approx. 1250 ° C. before the hot rolling process must be, as is customary for normal steel grades to reduce the yield strength, but up to approx. 1400 ° C in order to bring the control phase-forming elements into solution sufficiently well, so that in the subsequent production steps, such as hot rolling and hot strip annealing, a sufficient number of particles are finely divided can be. This increased preheating has economic disadvantages. It was therefore proposed in the generic DE 43 11 151 Cl to dispense with increased preheating by choosing essentially copper sulfide as the control phase and to preheat the slabs to temperatures below 1320 ° C.
Die praktische Umsetzung dieses bekannten Verfahrens liefert magnetische Werte, die bei der betrieblichen Erzeugung großer Mengen in unterschiedlicher Weise streuen. Aufgabe der Erfindung ist somit, das bekannte Verfahren gemäß der DE 43 11 151 dahingehend zu ergänzen, daß die Streubreite der magnetischen Werte erheblich verringert wird.The practical implementation of this known method provides magnetic values which scatter in different ways in the production of large quantities. The object of the invention is therefore to supplement the known method according to DE 43 11 151 in such a way that the spread of the magnetic values is considerably reduced.
Die Lösung dieser Aufgabe besteht erfindungsgemäß darin, bei dem gattungsgemäßen Verfahren den Umformgrad im letzten Kaltwalzschritt auf einen Wert im Bereich von 83 bis 86 % einzustellen. Liegt dieser Umformgrad unterhalb oder oberhalb des genannten Bereichs, können zwar ebenfalls gute magnetische Eigenschaften erzielt werden, jedoch mit derart starken Streuungen, daß in Einzelfällen unbefriedigende Ergebnisse auftreten können.According to the invention, this object is achieved by setting the degree of deformation in the last cold rolling step to a value in the range from 83 to 86% in the generic method. If this degree of deformation is below or above the range mentioned, good magnetic properties can also be achieved, but with such strong scatter that unsatisfactory results can occur in individual cases.
Nachfolgend soll dieser Zusammenhang anhand der Tabellen und Figuren exemplarisch verdeutlicht werden. Tabelle 1 enthält die chemischen Zusammensetzungen der untersuchten Schmelzen. Sie stellen eine typische Auswahl dar. Von diesen Schmelzen wurden in jeweils gleicher Weise Brammen durch Stranggießen erzeugt und anschließend Warmbänder durch Warmwalzen hergestellt. Die Warmbanddicke wurde dabei in einem Bereich von 2,00 bis 2,85 mm variiert. Nach einer Glühung dieser Warmbänder bei 1080 °C für 240 s Dauer und nachfolgender beschleunigter Abkühlung wurden die Warmbänder kaltgewalzt auf Fertigbandnenndicken von 0,30 und 0,23 mm. Alternativ dazu wurde ein Teil der Warmbänder zunächst vor Durchführung der Glühung bei 1080 °C kalt vorgewalzt und dadurch ihre Dicke auf einen Bereich von 1,25 bis 1,80 mm reduziert. Tabelle 2 zeigt die Bereiche der dabei erzeugten Varianten.In the following, this relationship will be exemplified using the tables and figures. Table 1 contains the chemical compositions of the melts examined. They represent a typical selection. From these melts, slabs were produced in the same way by continuous casting and hot strips were then produced by hot rolling. The hot strip thickness was varied in a range from 2.00 to 2.85 mm. After annealing these hot strips at 1080 ° C for 240 s and then accelerating them, the hot strips were cold-rolled to finished strip thicknesses of 0.30 and 0.23 mm. Alternatively, some of the hot strips were first cold rolled at 1080 ° C. before the annealing was carried out, thereby reducing their thickness to a range from 1.25 to 1.80 mm. Table 2 shows the areas of the variants created.
Nach der weiteren Verarbeitung durch Entkohlungsglühen, Klebschutzbeschichten, Hochtemperaturglühen und Isolationsbeschichten und Schlußglühen wurden die in den Fig. 1 und 2 dargestellten Polarisationswerte erzielt. Es zeigt sich, daß bei einem Umformgrad von etwa 85 % die besten magnetischen Werte erzielt werden und daß diese Werte dann die geringste Streuung aufweisen. After further processing by decarburization annealing, anti-adhesive coating, high-temperature annealing and insulation coating and final annealing, the polarization values shown in FIGS. 1 and 2 were achieved. It can be seen that the best magnetic values are achieved with a degree of deformation of approximately 85% and that these values then have the least scatter.
c n s Si Cu AI N SDc n s Si Cu AI N SD
0.059 0.087 0.023 3,22 0.072 0.022 0.0075 0.0600.059 0.087 0.023 3.22 0.072 0.022 0.0075 0.060
0.058 0,097 0.022 3,21 0.070 0.021 0,0073 0.0630.058 0.097 0.022 3.21 0.070 0.021 0.0073 0.063
0.055 0.085 0.026 3.15 0.080 0.022 0,0081 0.0710.055 0.085 0.026 3.15 0.080 0.022 0.0081 0.071
0,056 0.085 0.027 3.16 0.079 0.023 0.0082 0.0710.056 0.085 0.027 3.16 0.079 0.023 0.0082 0.071
0.057 0.081 0.027 3.12 0.078 0.022 0,0074 0.0700.057 0.081 0.027 3.12 0.078 0.022 0.0074 0.070
0.057 0.088 0,026 3.14 0,080 0,024 0,0080 0.0690.057 0.088 0.026 3.14 0.080 0.024 0.0080 0.069
0,085 0,08 L 0,023 3,20 1 0.071 0.023 0,0085 0.1 190.085 0.08 L 0.023 3.20 1 0.071 0.023 0.0085 0.1 19
Tabelle 1) Chemische Zusammensetzungen der betrachteten SchmelzenTable 1) Chemical compositions of the considered melts
Dicke nach Umformgrad beimThickness by degree of deformation at
Warmband-Dicke !) Vonvalzen 2> Fertigbanddicke letzten KaltwalzenHot strip thickness! ) Vonvalzen 2 > Finished strip thickness last cold rolls
2,00 bis 2,85 mm kein Vorwaken 0,30 mm 85 bis 89 %2.00 to 2.85 mm no pre-hook 0.30 mm 85 to 89%
2,30 bis 2,85 mm 1,50 bis 1,80 mm 0,30 mm 80 bis 83 %2.30 to 2.85 mm 1.50 to 1.80 mm 0.30 mm 80 to 83%
2,30 bis 2,85 mm 1,25 bis 1,80 mm 0,23 mm 82 bis 87 %2.30 to 2.85 mm 1.25 to 1.80 mm 0.23 mm 82 to 87%
2,00 bis 2,50 mm kein Vorwaken 0,23 mm 88 bis 91 %2.00 to 2.50 mm no pre-hooking 0.23 mm 88 to 91%
1) Dicke des warmgewalzten Bandes1) Thickness of the hot rolled strip
2) Banddicke nach Kaltwalzen des warmgewalzten Bandes vor der Glαhung des BaDdes bei 1080°C2) Strip thickness after cold-rolling the hot-rolled strip before the bath was annealed at 1080 ° C
Tabelle 2) Untersuchte Varianten Table 2) Variants examined

Claims

PatentanspruchClaim
Verfahren zur Herstellung von kornorientiertem Elektroblech, bei dem eine Bramme aus einem Stahl mit (Masεe-%) mehr als 0,005 bis 0,10 % C,Process for the production of grain-oriented electrical sheet, in which a slab made of steel with (mass%) more than 0.005 to 0.10% C,
2, 5 bis 4,5 % Si,2.5 to 4.5% Si,
0, 03 bis 0, 15 % Mn, mehr als 0,01 bis 0,05 % S,0.03 to 0.15% Mn, more than 0.01 to 0.05% S,
0, 01 bis 0, 035 % AI,0.01 to 0.035% AI,
0, 0045 bis 0, 012 % N,0.0045 to 0.012% N,
0, 02 bis 0,3 % Cu,0.02 to 0.3% Cu,
Rest Fe einschl . unvermeidbarerRest Fe incl. inevitable
Verunreinigungen bei einer Temperatur, die tiefer als die Löslichkeitstemperatur für Mangansulfid, jedenfalls unter 1320 °C, aber oberhalb der Löslichkeitstemperatur für Kupfersulfide liegt, durcherwärmt wird, im Anschluß daran mit einer Anfangstemperatur von mindestens 960 °C und mit einer Endtemperatur im Bereich von 880 bis 1000 °C bis auf Warmband-Enddicke im Bereich von 1,5 bis 7 , 0 mm warmgewalzt wird, das Warmband danach 100 bis 600 ε lang bei einer Temperatur im Bereich von 880 bis 1150 °C geglüht, sodann mit einer Abkühlrate von größer als 15 K/s abgekühlt und in einem oder mehreren Kaltwalzschritten bis auf Kaltband-Enddicke kaltgewalzt wird, worauf das Kaltband einer rekristallisierenden Glühung in feuchter Wasserstoff und Stickstoff enthaltender Atmosphäre mit gleichzeitiger Entkohlung unterworfen wird und nach dem beidseitigen Aufbringen eines im wesentlichen MgO enthaltenden Trennmittels hochtemperaturgeglüht und nach dem Aufbringen einer Isolierbeschichtung schlußgeglüht wird, d a d u r c h g e k e n n z e i c h n e t, daß der Umformgrad im letzten Kaltwalzschritt auf einen Wert im Bereich von 83 bis 86 % eingestellt wird. Contamination is heated at a temperature which is lower than the solubility temperature for manganese sulfide, in any case below 1320 ° C, but above the solubility temperature for copper sulfides, with an initial temperature of at least 960 ° C and a final temperature in the range of 880 to 1000 ° C to hot strip final thickness in the range from 1.5 to 7.0 mm is hot rolled, the hot strip is then annealed for 100 to 600 ε at a temperature in the range from 880 to 1150 ° C, then with a cooling rate of greater than 15 K / s cooled and cold rolled in one or more cold rolling steps to the final cold strip thickness, whereupon the cold strip is subjected to a recrystallizing annealing in a humid hydrogen and nitrogen-containing atmosphere with simultaneous decarburization and after the double-sided application of a release agent essentially containing MgO, it is subjected to high-temperature annealing and after applying an insulating coating is finally annealed, characterized in that the degree of deformation in the last cold rolling step is set to a value in the range from 83 to 86%.
PCT/EP1997/003509 1996-07-12 1997-07-03 Process for producing a grain-orientated electrical steel sheet WO1998002590A1 (en)

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DE19628137A DE19628137C1 (en) 1996-07-12 1996-07-12 Grain-oriented electrical steel sheet prodn.

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DE19628137C1 (en) * 1996-07-12 1997-04-10 Thyssen Stahl Ag Grain-oriented electrical steel sheet prodn.
AU2698097A (en) * 1997-04-16 1998-11-11 Acciai Speciali Terni S.P.A. New process for the production at low temperature of grain oriented electrical steel
AU2701197A (en) * 1997-04-24 1998-12-11 Acciai Speciali Terni S.P.A. New process for the production of high-permeability electrical steel fr om thin slabs
DE19745445C1 (en) * 1997-10-15 1999-07-08 Thyssenkrupp Stahl Ag Process for the production of grain-oriented electrical sheet with low magnetic loss and high polarization

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Publication number Priority date Publication date Assignee Title
EP0266422A1 (en) * 1986-03-25 1988-05-11 Kawasaki Steel Corporation Process for producing low core loss, thin, unidirectional silicon steel plate having excellent surface properties
EP0315948A2 (en) * 1987-11-10 1989-05-17 Nippon Steel Corporation Process for preparation of thin grain oriented electrical steel sheet having excellent iron loss and high flux density
EP0398114A2 (en) * 1989-05-13 1990-11-22 Nippon Steel Corporation Process for preparation of thin grain oriented electrical steel sheet having superior iron loss and high flux density
DE4311151C1 (en) * 1993-04-05 1994-07-28 Thyssen Stahl Ag Grain-orientated electro-steel sheets with good properties
EP0732413A1 (en) * 1995-03-14 1996-09-18 USINOR SACILOR Société Anonyme Process for manufacturing grain oriented electrical steel sheets for transformers
DE19628137C1 (en) * 1996-07-12 1997-04-10 Thyssen Stahl Ag Grain-oriented electrical steel sheet prodn.

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0266422A1 (en) * 1986-03-25 1988-05-11 Kawasaki Steel Corporation Process for producing low core loss, thin, unidirectional silicon steel plate having excellent surface properties
EP0315948A2 (en) * 1987-11-10 1989-05-17 Nippon Steel Corporation Process for preparation of thin grain oriented electrical steel sheet having excellent iron loss and high flux density
EP0398114A2 (en) * 1989-05-13 1990-11-22 Nippon Steel Corporation Process for preparation of thin grain oriented electrical steel sheet having superior iron loss and high flux density
DE4311151C1 (en) * 1993-04-05 1994-07-28 Thyssen Stahl Ag Grain-orientated electro-steel sheets with good properties
EP0732413A1 (en) * 1995-03-14 1996-09-18 USINOR SACILOR Société Anonyme Process for manufacturing grain oriented electrical steel sheets for transformers
DE19628137C1 (en) * 1996-07-12 1997-04-10 Thyssen Stahl Ag Grain-oriented electrical steel sheet prodn.

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DE19628137C1 (en) 1997-04-10
AU3692897A (en) 1998-02-09

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