EP0910676B1 - Verfahren zur herstellung von kornorientiertem elektroblech - Google Patents

Verfahren zur herstellung von kornorientiertem elektroblech Download PDF

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Publication number
EP0910676B1
EP0910676B1 EP97930498A EP97930498A EP0910676B1 EP 0910676 B1 EP0910676 B1 EP 0910676B1 EP 97930498 A EP97930498 A EP 97930498A EP 97930498 A EP97930498 A EP 97930498A EP 0910676 B1 EP0910676 B1 EP 0910676B1
Authority
EP
European Patent Office
Prior art keywords
temperature
annealing
strip
cold
nitrogen
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
EP97930498A
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German (de)
English (en)
French (fr)
Other versions
EP0910676A1 (de
Inventor
Manfred Espenhahn
Andreas Böttcher
Klaus Günther
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 Stahl AG
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Publication of EP0910676A1 publication Critical patent/EP0910676A1/de
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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
    • C21D8/1244—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
    • C21D8/1272—Final recrystallisation annealing
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/76—Adjusting the composition of the atmosphere
    • 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
    • C21D8/1216—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
    • C21D8/1244—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 from which a slab is made a steel with (in mass%) more than 0.005 to 0.10% C, 2.5 to 4.5% Si, 0.03 to 0.15% Mn, more than 0.01 to 0.05% S, 0.01 to 0.035% Al, 0.0045 to 0.012% N, 0.02 up to 0.3% Cu, balance Fe including unavoidable Contamination at a temperature lower than that Solubility temperature for manganese sulfides, anyway below 1320 ° C, but above the solubility temperature for copper sulfides, is heated through, then with an initial temperature of at least 960 ° C and with a final temperature in the range of 880 to 1000 ° C up to the final hot strip thickness in the range from 1.5 to 7.0 mm is hot rolled, the hot strip then 100 to 600 s long at a temperature in the range of 880 to 1150 ° C annealed, then at a cooling rate greater than 15 K / s cooled and in one or more Cold
  • the aim of lowering the temperature before hot rolling is Avoiding liquid slag on the slabs, which Wear on the glow devices is reduced and that Production output increased.
  • EP-B-0 219 611 describes a method which a lowering of the slab preheating temperature in advantageously allows.
  • (Al, Si) N particles used as grain growth inhibitors which via a nitriding process into the finished strip thickness cold-rolled and decarburized strip can be introduced.
  • the measure to carry out this nitriding process is the Annealing atmosphere in the high-temperature annealing selected so that this has a nitriding ability, or it becomes nitriding Additives for glow repair, or combinations of cited both.
  • EP-B-0 321 695 describes a similar process described. As grain growth inhibitors only (Al, Si) N particles are used. It will additional information on the chemical composition made and another way one Nitriding treatment in connection with the Decarburization annealing demonstrated. Furthermore, the hint given that the slab preheating temperatures are preferred should be below 1200 ° C.
  • EP-B-0 339 474 also describes a process, but a nitriding treatment in the form of continuous annealing in the temperature range from 500 to 900 ° C. is carried out in detail in the presence of a sufficient amount of NH 3 in the annealing gas. Furthermore, it is described in detail how the annealing nitriding treatment can be connected directly after the decarburization annealing. The goal here is the formation of (Al, Si) N particles as an effective grain growth inhibitor. It is particularly emphasized that with such a nitriding treatment, at least 100 ppm, but preferably more than 180 ppm, of nitrogen must be introduced. The slab preheating temperature should be below 1200 ° C.
  • EP-B-0 390 140 represents the special meaning of the Grain size distribution of the decarburized cold strip in particular and gives different methods for their determination on.
  • the slab preheating temperature is always one Temperature specified below 1280 ° C. However Always recommended that the slabs be below 1200 ° C preheat all of the exemplary embodiments listed indicate 1150 ° C as preheating temperature.
  • the hot rolled strip is subjected to annealing in order to to excrete the copper sulfide particles, which the Form inhibitor phase. Then there is a Cold rolling to the finished strip thickness.
  • you can the hot-rolled strip is first a first Cold rolling step are then subjected to the inhibitor-eliminating annealing and the last cold rolling to carry out the finished strip thickness.
  • This band eventually becomes a continuous one Decarburization annealing treatment carried out in a moist Nitrogen and hydrogen containing annealing atmosphere.
  • the structure recrystallized and decarburized the tape. Then will an essentially containing MgO Anti-stick coating on the surface of decarburized Cold tape applied and the tape wound up Coils.
  • the decarburized cold strip coils thus produced are then subjected to a high temperature hood annealing in order to Formation of the Goss Texture on the Process of Initiate secondary recrystallization.
  • the coils with a heating rate of about 10 to 30 K / h slowly heated up in a glowing atmosphere There is hydrogen and nitrogen.
  • the dew point of the hot gas rises sharply because then the crystal water of the essentially MgO containing adhesive protection coating is released.
  • secondary recrystallization takes place at around 950 to 1020 ° C from.
  • a mixture of hydrogen and nitrogen is generally used as the annealing gas, a mixture of 75% hydrogen and 25% nitrogen being particularly common.
  • this gas composition a certain nitrogen nitriding of the tape is effected, because with this stoichiometric composition there are enough NH 3 molecules that are necessary for nitrogen nitriding. This increases the known inhibition based on AlN.
  • the cold strip for high-temperature annealing in an atmosphere containing less than 25% by volume of H 2 the rest nitrogen and / or noble gas, such as argon, is heated at least until the holding temperature is reached. After reaching the holding temperature, the H 2 content can be steadily increased to 100%.
  • heating up phase also significantly increases that Oxidation potential of the annealing atmosphere, which is reflected in Individual cases unfavorable to the later training of the insulating phosphate layer and their adhesion can.
  • This problem only occurs at the beginning of the Heating phase noticeable when the dew point of the hot gas by releasing water vapor from the Anti-adhesive coating increases significantly.
  • a Change in the inhibitor phase occurs through desulfurization but not yet in at these low temperatures Appearance, but occurs only at higher temperatures on. To adversely affect the To avoid surface texture, the Gas composition changed during the heating phase become.
  • Reference The first high-temperature annealing referred to as “reference” corresponded to the prior art and contained an atmosphere of 75% by volume H 2 + 25% by volume N 2 in the heating phase. The temperature was raised from 15 K / h to a holding temperature of 1200 ° C., held at this temperature for 20 hours and then slowly cooled. An atmosphere of 100% H 2 was switched over from the start of the holding time.
  • New variant The second high-temperature annealing, referred to as “new”, represented the measure according to the invention and, in contrast to “Reference”, contained an atmosphere of 10% by volume H 2 + 90% by volume N 2 in the heating phase.
  • inert The third high-temperature annealing, referred to as “inert”, also represented the measure according to the invention, however, in contrast to “new", the inert gas argon was used instead of N 2 in the heating phase.
  • Fig. 1 shows the steep drops of the Coercive field strength that in all three cases one Secondary recrystallization has taken place.
  • the Individual recrystallization test samples were chemical analyzed for their nitrogen and sulfur content.
  • Fig. 3 shows the development of the nitrogen content
  • Fig. 4 shows the development of the sulfur content in Temperature interval from 900 ° C to 1045 ° C during the Warm-up phase of the high glow.
  • Table 1 Table 1 listed melts A to E.
  • the bands were rolled to a finished strip thickness of 0.30 mm.
  • the development of the sulfur content differs between the inventive and the non-inventive annealing variants in a noteworthy manner only from strip temperatures above 900 ° C.
  • the advantageous effect of the variant according to the invention also arises if the low-hydrogen incandescent atmosphere is only used at a later point in time during heating. If, for example, the use of very low-hydrogen glow atmospheres in the heating phase (e.g. 5% by volume hydrogen) should cause problems with the surface properties of the strip due to its very high oxidation potential, the method according to the invention can be modified as follows: The annealing starts with a hydrogen-rich one Annealing atmosphere.
  • the composition of the annealing gas is changed and the annealing continued in a low-hydrogen atmosphere.
  • the gas atmosphere is changed again and the hydrogen content is greatly increased, preferably to 100%.
  • the effect of this modification of the method according to the invention is identical to that of the method according to the invention described above.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Electromagnetism (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Formation And Processing Of Food Products (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Hard Magnetic Materials (AREA)
  • Peptides Or Proteins (AREA)
  • Preparation Of Compounds By Using Micro-Organisms (AREA)
  • Breeding Of Plants And Reproduction By Means Of Culturing (AREA)
EP97930498A 1996-07-12 1997-07-03 Verfahren zur herstellung von kornorientiertem elektroblech Expired - Lifetime EP0910676B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE19628136A DE19628136C1 (de) 1996-07-12 1996-07-12 Verfahren zur Herstellung von kornorientiertem Elektroblech
DE19628136 1996-07-12
PCT/EP1997/003510 WO1998002591A1 (de) 1996-07-12 1997-07-03 Verfahren zur herstellung von kornorientiertem elektroblech

Publications (2)

Publication Number Publication Date
EP0910676A1 EP0910676A1 (de) 1999-04-28
EP0910676B1 true EP0910676B1 (de) 2001-01-10

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Country Status (18)

Country Link
US (1) US6153019A (cs)
EP (1) EP0910676B1 (cs)
JP (1) JP4369536B2 (cs)
CN (1) CN1078256C (cs)
AT (1) ATE198629T1 (cs)
AU (1) AU710053B2 (cs)
BR (1) BR9710302A (cs)
CZ (1) CZ288875B6 (cs)
DE (2) DE19628136C1 (cs)
ES (1) ES2154904T3 (cs)
ID (2) ID19071A (cs)
IN (1) IN191758B (cs)
PL (1) PL183750B1 (cs)
RU (1) RU2190025C2 (cs)
SK (1) SK283881B6 (cs)
TW (1) TW425429B (cs)
WO (1) WO1998002591A1 (cs)
ZA (1) ZA976001B (cs)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102011119395A1 (de) 2011-06-06 2012-12-06 Thyssenkrupp Electrical Steel Gmbh Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrostahlflachprodukts
WO2013004747A1 (de) 2011-07-06 2013-01-10 Thyssenkrupp Electrical Steel Gmbh Verfahren zum herstellen eines kornorientierten, für elektrotechnische anwendungen bestimmten elektrostahlflachprodukts

Families Citing this family (25)

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DE19628136C1 (de) * 1996-07-12 1997-04-24 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech
DE19735062A1 (de) * 1997-08-13 1999-02-18 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech und Verwendung eines Stahls für Elektroblech
DE19745445C1 (de) * 1997-10-15 1999-07-08 Thyssenkrupp Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech mit geringem Ummagnetisierungsverlust und hoher Polarisation
DE19821299A1 (de) * 1998-05-13 1999-11-18 Abb Patent Gmbh Anordnung und Verfahren zum Erzeugen von Warmband
JP4258349B2 (ja) * 2002-10-29 2009-04-30 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
EP1752549B1 (de) * 2005-08-03 2016-01-20 ThyssenKrupp Steel Europe AG Verfahren zur Herstellung von kornorientiertem Elektroband
SI1752548T1 (sl) * 2005-08-03 2016-09-30 Thyssenkrupp Steel Europe Ag Metoda za proizvodnjo magnetnega zrnato usmerjenega jeklenega traku
CN100418697C (zh) * 2006-05-18 2008-09-17 武汉科技大学 一种高磁感取向电工钢板及其制造方法
CN100436042C (zh) * 2006-05-18 2008-11-26 武汉科技大学 一种薄板坯工艺高磁感取向电工钢板及其制造方法
CN101545072B (zh) * 2008-03-25 2012-07-04 宝山钢铁股份有限公司 一种高电磁性能取向硅钢的生产方法
EP2304061A1 (de) * 2008-06-13 2011-04-06 LOI Thermprocess GmbH Verfahren zum hochtemperatur-glühen von kornorientiertem elektroband in einer schutzgasatmospäre in einem wärmebehandlungsofen
CN101333589B (zh) * 2008-07-04 2010-10-06 武汉钢铁工程技术集团有限责任公司 一种用于薄钢板无氧化加热的方法及专用加热炉
CN101603148B (zh) * 2009-07-28 2011-01-05 首钢总公司 一种生产经济的低温加热取向电工钢的方法
JP5772410B2 (ja) * 2010-11-26 2015-09-02 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
CN102127708A (zh) * 2011-01-16 2011-07-20 首钢总公司 一种低温板坯加热生产取向电工钢的方法
CN102294358B (zh) * 2011-08-19 2012-12-05 江苏新中信电器设备有限公司 一种铜包铝排型材压力连铸轧制工艺
DE102011054004A1 (de) * 2011-09-28 2013-03-28 Thyssenkrupp Electrical Steel Gmbh Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrobands oder -blechs
RU2610204C1 (ru) * 2013-02-27 2017-02-08 ДжФЕ СТИЛ КОРПОРЕЙШН Способ изготовления листа из текстурированной электротехнической стали
EP2933350A1 (en) * 2014-04-14 2015-10-21 Mikhail Borisovich Tsyrlin Production method for high-permeability grain-oriented electrical steel
CZ305521B6 (cs) * 2014-05-12 2015-11-11 Arcelormittal Ostrava A.S. Pás z orientované transformátorové oceli a způsob jeho výroby
CN104294155B (zh) * 2014-09-28 2016-05-11 东北大学 一种超低碳取向硅钢及其制备方法
JP6354957B2 (ja) * 2015-07-08 2018-07-11 Ｊｆｅスチール株式会社 方向性電磁鋼板とその製造方法
CN106048411A (zh) * 2016-06-27 2016-10-26 马鞍山钢铁股份有限公司 一种变压器用冷轧取向电工钢及其生产方法
KR102405173B1 (ko) * 2019-12-20 2022-06-02 주식회사 포스코 방향성 전기강판 및 그의 제조방법
WO2025036572A1 (en) 2023-08-01 2025-02-20 Nlmk International B.V. Insulating layer and method for installing rolls of metals and alloys on an insulating layer in a bell-type furnace

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102011119395A1 (de) 2011-06-06 2012-12-06 Thyssenkrupp Electrical Steel Gmbh Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrostahlflachprodukts
WO2012168253A1 (de) 2011-06-06 2012-12-13 Thyssenkrupp Electrical Steel Gmbh Verfahren zum herstellen eines kornorientierten, für elektrotechnische anwendungen bestimmten elektrostahlflachprodukts
WO2013004747A1 (de) 2011-07-06 2013-01-10 Thyssenkrupp Electrical Steel Gmbh Verfahren zum herstellen eines kornorientierten, für elektrotechnische anwendungen bestimmten elektrostahlflachprodukts
DE102011107304A1 (de) 2011-07-06 2013-01-10 Thyssenkrupp Electrical Steel Gmbh Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrostahlflachprodukts

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ES2154904T3 (es) 2001-04-16
ID19071A (id) 1998-06-11
ZA976001B (en) 1998-09-01
IN191758B (cs) 2003-12-27
RU2190025C2 (ru) 2002-09-27
WO1998002591A1 (de) 1998-01-22
PL183750B1 (pl) 2002-07-31
PL331166A1 (en) 1999-06-21
CN1078256C (zh) 2002-01-23
CN1219977A (zh) 1999-06-16
US6153019A (en) 2000-11-28
SK283881B6 (sk) 2004-04-06
JP2000514506A (ja) 2000-10-31
DE59702901D1 (de) 2001-02-15
CZ288875B6 (cs) 2001-09-12
CZ6899A3 (cs) 1999-10-13
JP4369536B2 (ja) 2009-11-25
DE19628136C1 (de) 1997-04-24
TW425429B (en) 2001-03-11
AU3442897A (en) 1998-02-09
ID17500A (id) 1998-01-08
ATE198629T1 (de) 2001-01-15
EP0910676A1 (de) 1999-04-28
SK1899A3 (en) 2000-02-14
AU710053B2 (en) 1999-09-09
BR9710302A (pt) 1999-08-17

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