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WO1999053106A1 - Procede de production de toles d'acier electrotechniques anisotropes a grains orientes - Google Patents

Procede de production de toles d'acier electrotechniques anisotropes a grains orientes Download PDF

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Publication number
WO1999053106A1
WO1999053106A1 PCT/EP1999/002393 EP9902393W WO9953106A1 WO 1999053106 A1 WO1999053106 A1 WO 1999053106A1 EP 9902393 W EP9902393 W EP 9902393W WO 9953106 A1 WO9953106 A1 WO 9953106A1
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WO
WIPO (PCT)
Prior art keywords
steel
heating
hot rolling
slabs
carried out
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.)
Ceased
Application number
PCT/EP1999/002393
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German (de)
English (en)
Inventor
Georg Königbauer
Zirlin Mikhail Borisovich
Nosov Alksey Dmitrievich
Nosov Sergey Konstantinovich
Lobanov Mikhail Lvovich
Kavtrev Vladislav Mikhailovich
Kavtrev Aleksey Vladislavovich
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Individual
Original Assignee
Individual
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Filing date
Publication date
Application filed by Individual filed Critical Individual
Publication of WO1999053106A1 publication Critical patent/WO1999053106A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/1255—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 with diffusion of elements, e.g. decarburising, nitriding
    • 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

Definitions

  • the present invention relates to the field of iron metallurgy or black metallurgy, and in particular to a process for the production of grain-oriented anisotropic electrotechnical steel sheets, and in particular for the production of grain-oriented electrotechnical steel sheets with a small thickness of typically 0.2 to 0.4 mm, as used in the Manufacture of magnetic lines used by transformers ..
  • a finished electrotechnical steel sheet should have a high magnetic flux density or induction and low power losses during the remagnetization. Furthermore, they should have permanent surface insulation, which is usually created by applying a ceramic layer to the surface.
  • High temperature slab heating at 1400 ° C (a slab or plate typically has a thickness of 200 mm) before the hot rolling step (rolling to 2.5 mm) is the special characteristic for steel with a sulfide inhibitor. This warming has 2
  • the aim is to dissolve the MnS in Mn and S and their subsequent elimination during rapid cooling in the course of hot rolling.
  • the said process is extremely non-technological, requires special equipment, is labor-intensive and is accompanied by metal losses due to oxidation.
  • hot rolling of the slabs with a specified content of C, Si, acid-soluble Al (e.g. AlN) and S is carried out.
  • the hot-rolled sheet thus obtained is cold-rolled to reduce the thickness in the range between 5 and 40% and then annealed in the temperature range 950 to 1200 ° C. in order to produce AlN precipitates.
  • the usual decarburization and high-temperature annealing steps are carried out.
  • This known method is referred to below as the prototype method.
  • steels with a nitride inhibitor are different because they do not require high temperature heating before the hot rolling step.
  • these steels with only one inhibitor show instability in the secondary recrystallization, which results in significant differences in the magnetic properties between different furnace cycles and in a lower yield of steel with high quality of the magnetic properties.
  • the magnetic properties are unstable.
  • the ceramic coating is not uniform in length and width.
  • heating is reduced during primary recrystallization before hot rolling. Furthermore, the electrotechnical steel with additives of Se or S can be heated for 0.5 to 10 minutes at temperatures of 660 to 650 ° C before the decarburization annealing.
  • the object of the present invention is to provide a method for producing electrotechnical steel sheets with aluminum nitride inhibitor, which offers improved magnetic properties and a more stable secondary recrystallization of the steel.
  • the ⁇ lll ⁇ ⁇ 112> orientation in the steel was strengthened with an aluminum nitride inhibitor (without copper or with an addition of 0.4 to 0.7% copper) before the secondary recrystallization.
  • an aluminum nitride inhibitor without copper or with an addition of 0.4 to 0.7% copper
  • the temperature T of the slab heating is set depending on the Al content according to the following equation (1):
  • Al% denotes the percentage by weight of aluminum in the melt. 5
  • the method according to the invention creates steel sheets with excellent magnetic properties and stable secondary recrystallization in steel with nitride inhibition without copper or with an addition of 0.4 to 0.7% copper.
  • the invention is based on the knowledge that the degree of dissolution of aluminum nitride (AlN) is mainly determined by the concentration of the aluminum, by the heating temperature and by the heating time of the slabs.
  • AlN aluminum nitride
  • the relationship between the austenite and ferrite structures also plays a role in the process of allowing the slabs to protrude. All of these parameters must be selected so that the nitride dissolution takes place at temperatures at which oxidation and melting of the slab surfaces does not take place.
  • the concentration of aluminum must be chosen so that the dissolution of nitrides at lower temperatures is guaranteed. This is achieved according to the invention in that the slab heating temperature is set as a function of the aluminum content.
  • the steel sheet is wound up at temperatures of 520 to 570 ° C. after hot rolling.
  • the addition of nitrides can not only prevent the growth of the grains before secondary recrystallization, but can also control the entire process of primary recrystallization by strengthening the orientations in the matrix that are favorable for texture formation. This requires a portion of the nitrogen 6 stay in the solid solution. This is achieved in that the temperature after hot rolling is reduced to 540 to 570 ° C. when the strips are wound up.
  • slow heating for high-temperature annealing is carried out at a heating rate of 5 to 15 ° C./hour in the temperature range from 400 to 700 ° C.
  • Disperse nitrogen precipitates which are responsible for the formation of the ⁇ lll ⁇ ⁇ 112> texture, appear in the final thickness of the cold-rolled material at the start of primary recrystallization (polygonization) when slow heating (5 - 15 ° C / Hour) in the temperature range of 400 - 700 ° C during high-temperature annealing or during a special heat treatment (aging).
  • decarburization annealing is carried out in the step of vacuum treatment of the non-deoxidized liquid steel or in the step of heat treatment of the steel sheet with the initial, intermediate or final thickness.
  • Decarburization can advantageously alternatively by vacuum treatment of liquid steel or by heat treatment of rolled strips in the initial (typically 2.5 mm after hot rolling), intermediate (typically 0.7 mm after first cold rolling) or final thickness (typically after second cold rolling) 0.3 mm).
  • the invention is particularly applicable to steels with the following composition: 2.8 to 3.5% Si, 0.030 to 0.045% C, 0.10 to 0.30% Mn, 0.003 to 0.020% S, 0.008 - 0.025% Al, 0 , 4 - 0.7% Cu.
  • the aluminum concentration falls below 0.008%, sufficient structural stabilization by the aluminum nitride is not possible, since a large part of the nitrogen is bound in silicon nitride.
  • the nitrides dissolve in the high temperature range (above 1320 ° C.), the slab surfaces melting and a useful feature of the process according to the invention being lost.
  • the temperature of the slab heating should therefore be 1230 to 1300 ° C, preferably 1250 to 1270 ° C. This prevents the surface from melting and reduces the energy consumption for heating to a minimum.
  • FIG. 2 shows the distribution of the specific losses PI 7/50 (W / kg) for the example according to FIG. 1.
  • the hot rolled strips 2.5 mm thick, they were cold rolled to 0.65 mm thick, annealed in a humid nitrogen-hydrogen mixture environment, and then cold rolled to a final thickness of 0.3 mm.
  • a magnesium suspension was then applied to the strips with the final thickness. Then high temperature annealing took place at 1150 ° C. Disperse precipitation particles made of AlN, which effects the secondary recrystallization, were produced in the process step of slowly heating (5-25 ° C./hour) the cold-rolled strip with the final thickness in the high-temperature annealing phase.

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

Abstract

L'invention concerne un procédé de production de tôles d'acier électrotechniques anisotropes à grains orientés comprenant 0,008 à 0,025 % d'aluminium, 2,8 à 3,5 % de silicium, 0,1 à 0,7 % de cuivre, 0,005 à 0,012 % d'azote, moins de 0,06 % de carbone, 0,1 à 0,3 % de manganèse et moins de 0,02 % de soufre. Ce procédé comprend la fusion de la matière première et la production de brames; le chauffage de ces brames à une température comprise entre 1230 et 1300 °C; le laminage à chaud; le laminage à froid en deux temps; le recuit; de préférence l'application d'un revêtement à base d'oxyde de magnésium; et le recuit à haute température. La température T de chauffage des brames avant le laminage à chaud est réglée en fonction de la teneur de l'acier en aluminium selon la relation suivante : T(°C) = 1230 + ((Al%) - 0,008) * 5300 + 20, Al % représentant le pourcentage en poids d'aluminium dans la masse en fusion.
PCT/EP1999/002393 1998-04-09 1999-04-08 Procede de production de toles d'acier electrotechniques anisotropes a grains orientes Ceased WO1999053106A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE19816158.1 1998-04-09
DE1998116158 DE19816158A1 (de) 1998-04-09 1998-04-09 Verfahren zur Herstellung von korn-orientierten anisotropen, elektrotechnischen Stahlblechen

Publications (1)

Publication Number Publication Date
WO1999053106A1 true WO1999053106A1 (fr) 1999-10-21

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PCT/EP1999/002393 Ceased WO1999053106A1 (fr) 1998-04-09 1999-04-08 Procede de production de toles d'acier electrotechniques anisotropes a grains orientes

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DE (1) DE19816158A1 (fr)
WO (1) WO1999053106A1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2009117959A1 (fr) * 2008-03-25 2009-10-01 宝山钢铁股份有限公司 Procédé de fabrication d'acier au si orienté à hautes propriétés électriques et magnétiques
US7736444B1 (en) 2006-04-19 2010-06-15 Silicon Steel Technology, Inc. Method and system for manufacturing electrical silicon steel

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2407808C1 (ru) * 2009-08-03 2010-12-27 Открытое акционерное общество "Новолипецкий металлургический комбинат" Способ производства анизотропной электротехнической стали с низкими удельными потерями на перемагничивание
RU2407809C1 (ru) * 2009-08-03 2010-12-27 Открытое акционерное общество "Новолипецкий металлургический комбинат" Способ производства анизотропной электротехнической стали с высокими магнитными свойствами
WO2011114178A1 (fr) * 2010-03-19 2011-09-22 Arcelormittal Investigación Y Desarrollo Sl Procédé de fabrication d'acier magnétique à grains orientés

Citations (11)

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US3287183A (en) * 1964-06-22 1966-11-22 Yawata Iron & Steel Co Process for producing single-oriented silicon steel sheets having a high magnetic induction
US3873381A (en) * 1973-03-01 1975-03-25 Armco Steel Corp High permeability cube-on-edge oriented silicon steel and method of making it
US4115160A (en) * 1977-06-16 1978-09-19 Allegheny Ludlum Industries, Inc. Electromagnetic silicon steel from thin castings
US4698272A (en) * 1985-02-22 1987-10-06 Kawasaki Steel Corporation Extra-low iron loss grain oriented silicon steel sheets
US4909864A (en) * 1986-09-16 1990-03-20 Kawasaki Steel Corp. Method of producing extra-low iron loss grain oriented silicon steel sheets
US4975127A (en) * 1987-05-11 1990-12-04 Kawasaki Steel Corp. Method of producing grain oriented silicon steel sheets having magnetic properties
US5061326A (en) * 1990-07-09 1991-10-29 Armco Inc. Method of making high silicon, low carbon regular grain oriented silicon steel
EP0732413A1 (fr) * 1995-03-14 1996-09-18 USINOR SACILOR Société Anonyme Procédé de fabrication d'une tÔle d'acier électrique à grains orientés notamment pour transformateurs
US5679178A (en) * 1994-07-22 1997-10-21 Kawasaki Steel Corporation Method of manufacturing grain-oriented silicon steel sheet exhibiting excellent magnetic characteristics over the entire length of coil thereof
US5711825A (en) * 1993-04-05 1998-01-27 Thyssen Stahl Ag Process for the production of grain oriented magnetic steel sheets having improved remagnetization losses
US5725681A (en) * 1995-09-07 1998-03-10 Kawasaki Steel Corporation Process for producing grain oriented silicon steel sheet, and decarburized sheet

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US4010050A (en) * 1975-09-08 1977-03-01 Allegheny Ludlum Industries, Inc. Processing for aluminum nitride inhibited oriented silicon steel
JPS5933170B2 (ja) * 1978-10-02 1984-08-14 新日本製鐵株式会社 磁束密度の極めて高い、含Ａｌ一方向性珪素鋼板の製造法
JPS585970B2 (ja) * 1979-05-16 1983-02-02 新日本製鐵株式会社 線状細粒のない一方向性珪素鋼板の製造方法
JPS5948934B2 (ja) * 1981-05-30 1984-11-29 新日本製鐵株式会社 高磁束密度一方向性電磁鋼板の製造方法
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Patent Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3287183A (en) * 1964-06-22 1966-11-22 Yawata Iron & Steel Co Process for producing single-oriented silicon steel sheets having a high magnetic induction
US3873381A (en) * 1973-03-01 1975-03-25 Armco Steel Corp High permeability cube-on-edge oriented silicon steel and method of making it
US4115160A (en) * 1977-06-16 1978-09-19 Allegheny Ludlum Industries, Inc. Electromagnetic silicon steel from thin castings
US4698272A (en) * 1985-02-22 1987-10-06 Kawasaki Steel Corporation Extra-low iron loss grain oriented silicon steel sheets
US4909864A (en) * 1986-09-16 1990-03-20 Kawasaki Steel Corp. Method of producing extra-low iron loss grain oriented silicon steel sheets
US4975127A (en) * 1987-05-11 1990-12-04 Kawasaki Steel Corp. Method of producing grain oriented silicon steel sheets having magnetic properties
US5061326A (en) * 1990-07-09 1991-10-29 Armco Inc. Method of making high silicon, low carbon regular grain oriented silicon steel
US5711825A (en) * 1993-04-05 1998-01-27 Thyssen Stahl Ag Process for the production of grain oriented magnetic steel sheets having improved remagnetization losses
US5679178A (en) * 1994-07-22 1997-10-21 Kawasaki Steel Corporation Method of manufacturing grain-oriented silicon steel sheet exhibiting excellent magnetic characteristics over the entire length of coil thereof
EP0732413A1 (fr) * 1995-03-14 1996-09-18 USINOR SACILOR Société Anonyme Procédé de fabrication d'une tÔle d'acier électrique à grains orientés notamment pour transformateurs
US5725681A (en) * 1995-09-07 1998-03-10 Kawasaki Steel Corporation Process for producing grain oriented silicon steel sheet, and decarburized sheet

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7736444B1 (en) 2006-04-19 2010-06-15 Silicon Steel Technology, Inc. Method and system for manufacturing electrical silicon steel
WO2009117959A1 (fr) * 2008-03-25 2009-10-01 宝山钢铁股份有限公司 Procédé de fabrication d'acier au si orienté à hautes propriétés électriques et magnétiques
JP2011517732A (ja) * 2008-03-25 2011-06-16 宝山鋼鉄股▲ふん▼有限公司 高電磁気性能の方向性珪素鋼の製造方法
US8333846B2 (en) 2008-03-25 2012-12-18 Baoshan Iron & Steel Co., Ltd. Manufacturing method of oriented SI steel with high electric-magnetic property
KR101252561B1 (ko) * 2008-03-25 2013-04-08 바오샨 아이론 앤 스틸 유한공사 높은 전-자기 특성을 가진 방향성 ｓｉ 강의 제조 방법

Also Published As

Publication number Publication date
DE19816158A1 (de) 1999-10-14

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