WO2010075797A1 - 用一次冷轧法生产取向硅钢的方法 - Google Patents

用一次冷轧法生产取向硅钢的方法 Download PDF

Info

Publication number
WO2010075797A1
WO2010075797A1 PCT/CN2009/076317 CN2009076317W WO2010075797A1 WO 2010075797 A1 WO2010075797 A1 WO 2010075797A1 CN 2009076317 W CN2009076317 W CN 2009076317W WO 2010075797 A1 WO2010075797 A1 WO 2010075797A1
Authority
WO
WIPO (PCT)
Prior art keywords
annealing
oriented silicon
cold rolling
silicon steel
steel
Prior art date
Application number
PCT/CN2009/076317
Other languages
English (en)
French (fr)
Inventor
李国保
张丕军
杨勇杰
沈侃毅
胡卓超
吴培文
靳伟忠
姜全力
Original Assignee
宝山钢铁股份有限公司
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
Application filed by 宝山钢铁股份有限公司 filed Critical 宝山钢铁股份有限公司
Priority to JP2011502219A priority Critical patent/JP5939797B2/ja
Priority to KR1020117013268A priority patent/KR101462044B1/ko
Priority to RU2011132006/02A priority patent/RU2469104C1/ru
Priority to US13/142,955 priority patent/US9038429B2/en
Priority to EP09836084.5A priority patent/EP2390373B1/en
Publication of WO2010075797A1 publication Critical patent/WO2010075797A1/zh

Links

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
    • C21D8/1233—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
    • C21D8/1255—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
    • 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
    • C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C21D8/1283—Application of a separating or insulating coating
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/30—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process
    • B21B1/32—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process in reversing single stand mills, e.g. with intermediate storage reels for accumulating work
    • B21B1/36—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process in reversing single stand mills, e.g. with intermediate storage reels for accumulating work by cold-rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B9/00—Measures for carrying out rolling operations under special conditions, e.g. in vacuum or inert atmosphere to prevent oxidation of work; Special measures for removing fumes from rolling mills
    • 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
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising

Definitions

  • the present invention relates to a method of producing oriented silicon steel, and more particularly to a method of producing oriented silicon steel by a single cold rolling process. Background technique
  • the basic chemical composition is Si (2 ⁇ 5 ⁇ 4 ⁇ 5%), C (0 ⁇ 01 ⁇ 0 ⁇ 10%) ), ⁇ (0 ⁇ 03 ⁇ 0 ⁇ 1%), S (0.012 ⁇ 0 ⁇ 050%), Als (0 ⁇ 01 ⁇ 0 ⁇ 05%), ⁇ (0 ⁇ 003 ⁇ 0 ⁇ 012%), some
  • the component system further contains one or more of elements such as Cu, Mo, Sb, Cr, B, Bi, etc., and the balance is iron and inevitable impurity elements;
  • the slab is heated to a temperature of about 140 CTC in a special high-temperature heating furnace, and is kept for more than 30 minutes to fully dissolve the favorable inclusions, so as to precipitate a small, dispersed second in the silicon steel matrix in the subsequent hot rolling process.
  • a phase point that is, an inhibitor
  • pickling is performed to remove the surface scale
  • the thickness of the finished product is rolled by one cold rolling or two or more cold rolling methods including intermediate annealing.
  • the [C] in the steel plate is removed to the extent that it does not affect the magnetic properties of the finished product (generally should be below 30 ppm); during the high temperature annealing, the steel plate undergoes secondary recrystallization. And the physical and chemical changes such as the formation and purification of the underlying layer of Mg 2 Si0 4 (removing elements harmful to magnetic properties such as S and N in steel), and obtaining oriented silicon steel having high orientation and low iron loss; finally, coated with an insulating coating and Stretch annealing gives oriented silicon steel products in commercial applications.
  • Inhibitors are formed from the beginning of steelmaking. In the subsequent processes, the inhibitors all function and must be controlled and adjusted.
  • the slab is heated at a high temperature, and the heating temperature is up to 1400 °C, which is the limit level of the traditional heating furnace.
  • the control of the temperature drop of the rolling line is also the limit of the existing hot rolling technology;
  • the heating furnace needs frequent repair and low utilization rate; at the same time, the burning energy consumption is high; the hot rolling curling is large, which makes the cold rolling process difficult, the finished product rate is low, and the cost is high.
  • Russia's VIZ and other plants use medium-temperature oriented silicon steel production technology.
  • the slab heating temperature is 1250 ⁇ 1300 °C.
  • the chemical composition contains high Cu, with A1N and Cu as inhibitors.
  • the inhibitor of this method is similar to the high temperature method and is also a congenital inhibitor.
  • the problem of edge cracking caused by high temperature heating can be completely avoided, but the disadvantage is that only general oriented silicon steel can be produced, and high magnetic induction oriented silicon steel cannot be produced.
  • the slab is heated below 125 CTC, and the hot rolled sheet is edgeless and has good productivity.
  • the inhibitor is obtained by nitriding after decarburization annealing, and is an acquired type of inhibitor, which can produce both general oriented silicon steel products and high magnetic induction oriented silicon steel products.
  • the method also solves the problem of hot rolling edge cracking of oriented silicon steel, improves productivity, and reduces production cost. Inhibitors are also acquired, obtained by nitriding.
  • the low temperature slab heating technology completely solves the inherent defects of the high temperature slab heating technology, improves the productivity and reduces the cost, and represents the direction of technological development.
  • Japanese low-temperature oriented silicon steel technology such as the method described in Japanese Patent No. [211-211232], has a chemical composition of 1: [C] 0. 025% ⁇ 0 ⁇ 075%, Si 2. 5. /. ⁇ 4 ⁇ 5%, S ⁇ O. 015%, Als 0. 010 ⁇ 0 ⁇ 050%, ⁇ 0. 0010 ⁇ 0. 0120%, ⁇ 0. 05 ⁇ 0. 45%, Sn 0. 01 ⁇ 0. The remaining 10% is Fe and inevitable inclusions.
  • the slab is heated at 120 CTC or less and then hot rolled, and is rolled to the final product thickness by one cold rolling or two or more intermediate cold rolling methods, and the cold rolling reduction ratio is 80% or more, followed by decarburization.
  • Chemical composition 2 is: [C] 0. 025% ⁇ 0 ⁇ 075%, Si 2. 5% ⁇ 4 ⁇ 5%, S ⁇ O. 015%, Als 0. 010 ⁇ 0 ⁇ 050% ⁇ 0 ⁇ 0010 ⁇ 0 ⁇ 0120%, ⁇ : 0 ⁇ 0005 ⁇ 0 ⁇ 0080%, ⁇ 0 ⁇ 05 ⁇ 0 ⁇ 45%, Sn 0. 01 ⁇ 0. 10%, the rest are Fe and unavoidable inclusions.
  • the slab is heated at a temperature below 120 CTC, then hot rolled, and rolled to a final product thickness by one cold rolling or two or more intermediate cold rolling methods, and the cold rolling reduction ratio is 80% or more, followed by decarburization annealing and High temperature annealing, nitriding at the beginning of secondary recrystallization of decarburization annealing and high temperature annealing.
  • the protective atmosphere is a mixed gas of N 2 , wherein the NH 3 content is more than 1000 ppm, the oxygen potential is ⁇ ⁇ 2 0 / ⁇ 0.04, and the nitriding temperature is 500 ⁇ 900 ° C.
  • a weak oxidizing atmosphere is maintained in a temperature range of 600 to 850 °C.
  • the technology of the low-temperature oriented silicon steel production technology of the company is the method described in Chinese patent CN1228817A. Its chemical composition: Si 2. 5 - 5%, C 0. 002 ⁇ 0. 075%, Mn 0 05 ⁇ 0 ⁇ 4%, S (or S+0. 503Se) ⁇ 0. 015%, acid soluble A1 0. 010 ⁇ 0 ⁇ 045%, ⁇ 0. 003 ⁇ 0 ⁇ 013%, Sn ⁇ O. 2%, the rest is Fe and unavoidable impurities.
  • the steel of the above composition is cast into a thin slab and heated at a temperature of 1150 to 1300 ° C. After hot rolling, normalizing annealing and final cold rolling with a reduction ratio of more than 80% are performed.
  • the annealing atmosphere is controlled to make the steel
  • the nitrogen uptake is less than 50 ppm. This method is mainly suitable for the production of oriented silicon steel in thin slab continuous casting. No nitriding process was used.
  • Chinese patent CN1231703A discloses a method in which the chemical composition system belongs to a low carbon and copper-containing component system, and the production method is basically the same as the aforementioned patent. The difference is that the steel sheet is nitrided after decarburization annealing, and the nitriding temperature is 900 ⁇ 1050 °C, the nitriding amount is less than 50ppm. Suitable for thin slab production of oriented silicon steel.
  • the Chinese patent CN1242057A also discloses a method, the chemical composition thereof: Si 2. 5 ⁇ 4. 5%; C 150
  • ⁇ 750ppm preferably 250 ⁇ 500ppm; Mn 300 ⁇ 4000ppm, preferably 500 ⁇ 2000ppm; S ⁇ 120ppm, Preferably, 50 to 70 ppm; acid soluble Al 100 to 400 ppm, preferably 200 to 350 ppm; N 30 to 130 ppm, preferably 60 to 100 ppm; Ti ⁇ 50 ppm, preferably less than 30 ppm; and the balance being Fe and unavoidable impurities.
  • the slab heating temperature is 1200 ⁇ 1320 °C, and the nitriding temperature is 850 ⁇ 1050 °C. The rest of the process is basically the same as the above two.
  • the main point of other patents is that there is a dispersed phase in the hot rolled sheet to facilitate high temperature nitriding.
  • the nitriding temperature is 900 to 1000 °C.
  • the low temperature technology of Azias Speyer Aliteni is limited to the production of oriented silicon steel by high temperature nitriding and/or thin slab continuous casting.
  • the key point is that there is a dispersed phase in the hot rolled sheet, which is convenient for high temperature application.
  • Nitriding method, nitriding is simultaneous decarburization and nitriding or nitriding after decarburization.
  • Japanese technology focuses on the process of decarburization annealing to secondary recrystallization.
  • the nitriding of the steel plate is low, the nitriding temperature is low, and the inhibitor is formed in the early stage of high temperature annealing.
  • the European technology is nitriding after decarburization annealing, or Carbon annealing and nitriding are carried out simultaneously, and the nitriding temperature is high; the technology of P0SC0 is suitable for the low carbon and low A1 component system, and nitriding and decarburization are simultaneously performed.
  • the slab is heated.
  • the temperature is higher, such as around 125 CTC, so it is necessary to control the favorable inclusions in the hot rolled sheet.
  • the nitriding is carried out after decarburization or simultaneously with decarburization annealing.
  • P0SC0 is also a process of decarburization and nitriding.
  • the effect of oxide layer on the surface of steel plate is inevitable.
  • the content of A1 in steel is low, and BN is the main inhibitor.
  • the instability of B will lead to inhibition.
  • the instability of the ability, the stability of the magnetic properties will be greatly affected.
  • the high temperature slab heating method produces oriented silicon steel with inherent disadvantages such as high energy consumption, low efficiency of heating furnace, large edge cracking of hot rolled sheet, poor productivity, low cost, etc.
  • Low temperature slab heating technology produces oriented silicon steel. These problems can be solved well, and thus have strong development motivation.
  • the low temperature slab heating technology disclosed in the patent literature produces oriented silicon steel, which is almost based on the nitriding process.
  • the object of the present invention is to provide a method for producing oriented silicon steel by a single cold rolling method, by controlling the normalized cooling process of the hot rolled sheet, utilizing the nitrogen absorption of the slab in the decarburization annealing and high temperature annealing low heat preservation stage to form a sufficient amount.
  • the (Al, Si) N is beneficially mixed, and the primary recrystallized structure of the steel sheet can be effectively controlled by using the inhibitory effect on the primary recrystallized grains, which is very stable for obtaining a stable and perfect secondary recrystallized product.
  • the present invention overcomes the adverse effects of ammonia nitriding on the underlayer in other patents, and is advantageous for obtaining a good glass film underlayer.
  • a method for producing oriented silicon steel by a cold rolling method comprising the steps of:
  • the slab of the following composition is obtained: C 0. 035 ⁇ 0 ⁇ 065%, Si 2. 9 ⁇ 4 ⁇ 0%, ⁇ 0. 08 ⁇ 0 ⁇ 18%, S 0. 005 ⁇ 0 ⁇ 012%, Als 0. 015 ⁇ 0 ⁇ 035%, ⁇ 0 ⁇ 0050 ⁇ 0 ⁇ 0130%, Sn 0 ⁇ 001 ⁇ 0 ⁇ 15%, ⁇ 0 ⁇ 010 ⁇ 0 ⁇ 030%, Cu 0. 05 ⁇ 0. 60%, Cr ⁇ 0.2%, the balance being Fe and unavoidable inclusions, by mass percentage;
  • the slab is heated to a temperature of 1090 to 1200 ° C, less than 118 CTC, and a temperature of more than 86 CTC is rolled, and rolled into a thickness of 1. 5 ⁇ 3. 5mm thick rolled sheet, coiling temperature of 500 ⁇ 650 ° C;
  • annealing temperature 1050 ⁇ 1180 ° C (1 ⁇ 20 seconds) + (850 ⁇ 950 ° C X 30 ⁇ 200 seconds), cooling rate: 10 ° C / s ⁇ 6 (TC / s;
  • the cold rolling reduction rate is 75 ⁇ 92%
  • the steel sheet rolled to the thickness of the finished product is subjected to decarburization annealing, and a high temperature annealing separator containing MgO as a main component is applied;
  • the decarburization temperature control range is 780 to 880 ° C ;
  • the protective atmosphere dew point is 40 to 80 ° C ;
  • decarburization time 80 ⁇ 350 seconds;
  • protective atmosphere mixed gas with N 2 , content: 15 ⁇ 85%; total oxygen on the surface of decarburized plate [0] : 171/t ⁇ [0] ⁇ 313/t (t is the actual thickness of the steel plate, mm ), the nitrogen uptake is 2 ⁇ 10 ppm;
  • the oriented silicon steel may be added with MoO. 01 ⁇ 0. 10%, and/or Sb ⁇ 0.2% in terms of mass percentage.
  • the plate thickness is 1/4 to 1/3 and the plate thickness is 2/3 to 3/4, Gaussian texture
  • the ratio of (110) [001] and cubic texture (001) [110] is controlled at: 0 ⁇ 2 ⁇ ⁇ (110) [001] / ⁇ (001) [1 ⁇ 8, I (110) [001] and I (001) [110] is the intensity of Gaussian texture and cubic texture respectively; preferably: 0.5 ⁇ 1 (
  • the normal plate thickness is 1/4 to 1/3 and the plate thickness is 2/3 to 3/4, and the ratio of the number of crystal grains having a Gaussian texture to the total number of crystal grains is ⁇ 5%.
  • the billet In the traditional oriented steel production process, in order to form fine and uniform inhibitors such as MnS and AlN during the annealing of hot-rolled or hot-rolled sheets, the billet must be heated to 1350 ⁇ 1400 °C to make the billet coarse.
  • the precipitates of MnS and A1N are solid solution, so it is a high temperature heating technology for slabs.
  • low-temperature heating technology of oriented silicon steel slabs such as nitriding forming inhibitors
  • nitriding forming inhibitors mainly in the following categories: First, adding in high-temperature annealing separators Nitriding chemical composition, and then nitriding the steel strip to form inhibitors such as (Al, Si)N in the high-temperature annealing stage, such as Japanese Patent Laid-Open No. 1-230721, Ping 1 283324, etc.; The nitriding atmosphere of the stage is nitriding. Both of these types have failed to obtain magnetically stable products due to uneven nitriding and the like.
  • the present invention utilizes a conventional continuous casting process, and thus the production process of oriented steel using thin slab continuous casting and rolling disclosed in the patents US Pat. No. 6,273,964 B1 and US Pat. No. 6,296,719 B1 is quite different.
  • the technology of Azias Speyer Aitelni Company belongs to the patent of high temperature nitriding.
  • the nitriding method is also a method of simultaneous nitriding or decarburization and nitriding after decarburization, which is different from the method of the present invention;
  • Chinese Patent No. The methods described in 85100664 and 88101506. 7 are established in a conventional process in which the inhibitor is solid solution during heating and controlled to precipitate during the rolling process.
  • the actual heating temperature is close to 1300 ° C, which is substantially different from the method of the present invention. .
  • the invention realizes the optimization of the texture and favorable inclusion amount of the steel sheet after normalization by adjusting the normalization process of the hot rolled sheet; in the decarburization annealing process, by controlling the nitrogen-hydrogen ratio, temperature, time and dew point in the protective atmosphere, Achieve decarburization and precise control of the oxygen content on the surface of the steel sheet to ensure a good bottom layer; at the same time control the nitrogen-hydrogen ratio in the protective atmosphere to make the steel sheet absorb nitrogen; through the control of the nitrogen-hydrogen ratio in the protective atmosphere at low heat preservation stage in the high-temperature annealing process, Obtain an appropriate amount of inhibitor to ensure the perfection of secondary recrystallization.
  • 1 is a schematic view showing a normalized plate thickness of 1/4 to 1/3 and a plate thickness of 2/3 to 3/4;
  • FIG. 2 is a control range diagram of a decarburization process that may obtain a good underlayer of the present invention
  • Fig. 3 is a schematic view showing the control of the nitrogen uptake of the present invention being greater than or equal to 10 ppm.
  • the normalized condition test was carried out using the A component in Table 2 and the hot rolled condition steel in Table 3, and the influence of the normalization process conditions on 1120 ° C X6s + 910 ° C XX s + Y ° C / s on the texture is as shown in Table 5, often The relationship between the process conditions and the magnetic properties is shown in Table 6.
  • the normalized condition test was carried out using the A component in Table 2 and the hot rolled condition steel in Table 3, and the normalization process conditions were 1120 ° C X 5s + 910 ° C X 70 + 20 ° C / s, decarburization time, temperature, dew point on magnetic properties.
  • the effects of the bottom layer and the bottom layer are shown in Tables 7 and 8.
  • the normalized condition test was carried out using the A component in Table 2 and the hot rolled condition steel in Table 3, and the normalization process conditions were 1120 ° C X 5s + 910 ° C X 70 + 20 ° C / s , decarburization 850 ° C X 200 s , dew point + The effect of nitrogen ratio, dew point and time on the magnetic properties in a protective atmosphere at 60 ° C, high temperature annealing and heating temperature of 1000 ° or less is shown in Table 9.
  • the steel was made by a 500 kg vacuum furnace, and the chemical composition was as shown in Table 10. Hot rolling was carried out according to the hot rolling conditions shown in C of Table 3; thereafter, the hot rolled sheet was subjected to a process of cooling at 1150 ° C X 5 s + 93 (TCX 70 s + 35 ° C / s). Normalization, strip cold rolling to 0.30mm, 850 °C X200s decarburization, coating MgO release agent, high temperature annealing and annealing, coating the insulation layer, measuring magnetic properties, the results are also listed in Table 10.
  • the thickness of the slab is generally 200 ⁇ 250mm. In order to heat evenly, it must be heated for a long time, which can consume energy;
  • the method of the present invention effectively solves the above problems, and is compatible with Japan, Korea P0SC0 and Agia Compared with methods such as Speth Aritzelni, the method of the present invention optimizes the size and texture of the inhibitor by normalization, and in the stage of decarburization annealing and high temperature annealing, the steel sheet absorbs nitrogen to form additional (Al, Si) N.
  • the favorable inclusions can effectively control the primary recrystallized structure of the steel sheet, which is very advantageous for obtaining a stable and perfect secondary recrystallized finished structure.
  • the method does not use special nitriding treatment, and does not require a nitriding device, which is extremely advantageous for the formation of a good underlayer.
  • the production of oriented silicon steel by low temperature slab heating technology represents the leading edge technology of oriented silicon steel development.
  • the implementation equipment of the method of the invention is a conventional equipment for producing oriented silicon steel, and the realization technology is simple and easy, so it has a good promotion and application prospect.

Landscapes

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

Description

用一次冷轧法生产取向硅钢的方法
技术领域
本发明涉及取向硅钢的生产方法，特别涉及用一次冷轧法生产取向硅钢的方 法。 背景技术
传统上取向硅钢的生产方法如下：
用转炉 （或电炉） 炼钢， 进行二次精炼及合金化， 连铸成板坯， 其基本化 学成分为 Si (2·5〜4·5%) 、 C (0·01〜0· 10%) 、 Μη (0·03〜0· 1%) 、 S (0.012 〜0·050%) 、 Als (0·01〜0·05%) 、 Ν ( 0· 003〜0· 012%) ， 有的成分体系还含有 Cu、 Mo、 Sb、 Cr、 B、 Bi等元素中的一种或多种， 其余为铁及不可避免的杂质元 素；
板坯在专用高温加热炉内加热到 140CTC左右的温度，并进行 30分钟以上的 保温，使有利夹杂物充分固溶，以便在随后的热轧过程中在硅钢基体内析出细小、 弥散的第二相质点， 即抑制剂； 热轧板常化 （或不常化） 后， 进行酸洗， 除去表 面氧化铁皮； 用一次冷轧或包括中间退火的两次以上冷轧法轧到成品厚度， 进行 脱碳退火和涂布以 MgO为主要成分的退火隔离剂， 把钢板中的 [C]脱到不影响成 品磁性的程度（一般应在 30ppm以下）； 高温退火过程中， 钢板发生二次再结晶、 Mg2Si04底层形成及净化 （除去钢中的 S、 N等对磁性有害的元素） 等物理化学变 化， 获得取向度高、 铁损低的取向硅钢； 最后， 经过涂布绝缘涂层和拉伸退火， 得到商业应用形态的取向硅钢产品。
传统取向硅钢的显著特点有：
(1) 抑制剂从炼钢开始就形成， 在其后的各工序， 抑制剂都发挥作用， 必 须对它进行控制与调整；
(2) 板坯高温加热， 加热温度高达 1400°C， 为传统加热炉的极限水平， 轧 线温降的控制也是现有热轧技术的极限；
(3) 生产工艺技术的关键是控制各阶段钢板的组织、 织构， 以及抑制剂的 行为；
(4) 由于高温加热， 加热炉需频繁修补， 利用率低； 同时， 烧损大能耗高 ； 热轧卷边裂大， 致使冷轧工序生产困难， 成材率低， 成本高。
高温取向硅钢生产技术经过半个多世纪的发展， 已经非常成熟， 为电力电 子工业的发展做出了贡献， 生产出了顶级的取向硅钢产品， 但由于其生产工艺复 杂、技术含量高、企业间的技术封锁严重及产品的专用性和总需求量较小等原因， 掌握该项技术的钢铁制造商较少； 另一方面， 由于高温加热的特点， 出现了一系 列问题， 如必须有专用高温加热炉、 生产性差、 成本高等。
为了解决这些问题， 在长期的生产实践和研究工作中， 人们摸索和开发出 了一些成功的办法， 现简述如下：
( 1 ) 电磁感应加热方法
新日铁和川崎都有电磁感应加热技术， 从本质上来看， 该方法仍然属于高 温板坯加热方法， 所不同的是在板坯的高温加热阶段， 在电磁感应加热炉内， 通 入 N2、 两种保护气体， 精确控制气氛， 减少板坯的高温氧化， 同时， 由于加热 速度快， 降低高温在炉时间。 该方法较好地解决了边裂问题， 可以将边裂减少到 15讓以下， 改善了取向硅钢的生产性， 但不能完全消除边裂。
( 2 ) 中温取向硅钢生产方法
俄罗斯的 VIZ 等厂采用中温取向硅钢生产技术， 板坯加热温度 1250〜 1300°C， 化学成分中含较高的 Cu， 以 A1N和 Cu为抑制剂。 该方法的抑制剂与高 温法类似， 也是一种先天性的抑制剂。 可以完全避免高温加热带来的边裂问题， 但缺点是只能生产一般取向硅钢， 不能生产高磁感取向硅钢。
( 3 ) 日本的低温板坯加热方法
板坯在 125CTC以下加热， 热轧板无边裂， 生产性好。 抑制剂通过脱碳退火 后的渗氮而获得， 是一种后天的获得型抑制剂， 既可以生产一般取向硅钢产品， 又可以生产高磁感取向硅钢产品。
( 4 ) CSP生产取向硅钢方法
该方法也解决了取向硅钢的热轧边裂问题， 提高了生产性， 降低了生产成 本。 抑制剂也是后天获得型， 通过渗氮获得。
显然， 低温板坯加热技术彻底解决了高温板坯加热技术的固有缺陷， 提高 了生产性， 降低了成本， 代表了技术发展的方向。
日本的低温取向硅钢技术如日本专利 [平 3-211232]中介绍的方法， 其化学 成分 1为： [C] 0. 025%〜0· 075%, Si 2. 5。/。〜4· 5%， S^ O. 015%, Als 0. 010〜0· 050%, Ν 0. 0010〜0. 0120%， Μη 0. 05〜0. 45%， Sn 0. 01〜0. 10%其余为 Fe及不可避免 的夹杂物。 板坯在 120CTC以下加热后进行热轧， 用 1 次冷轧或有中间退火两次 以上的冷轧方法轧制到最终产品厚度， 冷轧压下率在 80%以上， 接着进行脱碳退 火和高温退火， 在脱碳退火和高温退火的二次再结晶开始阶段渗氮。 化学成分 2为: [C] 0. 025%〜0· 075%, Si 2. 5%〜4· 5%， S^ O. 015%, Als 0. 010 〜0· 050% Ν 0· 0010〜0· 0120%， Β: 0· 0005〜0· 0080%， Μη 0· 05〜0· 45%， Sn 0. 01 〜0. 10%， 其余为 Fe及不可避免的夹杂物。 板坯在 120CTC以下加热后进行热轧， 用 1次冷轧或有中间退火两次以上的冷轧方法轧制到最终产品厚度，冷轧压下率 在 80%以上， 接着进行脱碳退火和高温退火， 在脱碳退火和高温退火的二次再结 晶开始阶段渗氮。
脱碳退火后， 钢板的氧含量换算成 12mi l为： [0] ppm=55t ± 50 ( t : 板厚， 单位： mi l ) 用该方法可以生产高磁感取向硅钢。
日本专利特开平 5-112827 中介绍的方法， 其化学成分： [C] 0. 025%〜
0. 075%, Si 2. 9%〜4. 5%， S^ O. 012%, Als 0· 010〜0· 060%， Ν^ Ο. 010%, Μη 0. 08 〜0. 45%， Ρ 0. 015〜0. 045%， 其余为 Fe及不可避免的夹杂物。 板坯 120CTC以下 加热后， 进行热轧。用 1次冷轧或有中间退火两次以上的冷轧方法轧制到最终产 品厚度，脱碳退火后钢板在行进过程中进行连续渗氮，涂隔离剂后进行高温退火， 生产磁性和底层质量倶佳的取向硅钢。 连续渗氮方法： 保护气氛为 和 N2的混 合气体， 其中 NH3含量为 lOOOppm以上， 氧势为 ρΗ20/ρ 0. 04， 渗氮温度为 500 〜900°C。
高温退火时， 在 600〜850°C的温度范围内保持弱氧化性气氛。
阿奇亚斯佩丝阿里特尔尼公司的低温取向硅钢生产技术即中国专利 CN1228817A中介绍的方法，其化学成分： Si 2. 5— 5%, C 0. 002〜0. 075%, Mn 0. 05 〜0· 4%， S (或 S+0. 503Se) < 0. 015%,酸可溶 A1 0. 010〜0· 045%, Ν 0. 003〜0· 013%, Sn^ O. 2%, 其余为 Fe及不可避免的杂质。 上述成分的钢浇铸成薄板坯， 在 1150 〜1300°C的温度加热， 热轧后， 进行常化退火及压下率大于 80%的最终冷轧， 最 终高温退火时， 控制退火气氛， 使钢的吸氮量小于 50ppm。 这种方法主要适合于 薄板坯连铸生产取向硅钢。 没有采用渗氮工艺。
中国专利 CN1231703A公开了一种方法， 其化学成分体系属于低碳且含铜的 成分体系， 生产方法与前述专利也基本一致， 不同的是在脱碳退火后对钢板进行 渗氮， 渗氮温度为 900〜1050°C， 渗氮量低于 50ppm。 适合于薄板坯生产取向硅 钢。
中国专利 CN1242057A也公开了一种方法，其化学成分： Si 2. 5〜4. 5%； C 150
〜750ppm，最好 250〜500ppm; Mn 300〜4000ppm，最好 500〜2000ppm; S< 120ppm， 最好 50〜70ppm; 酸可溶 Al 100〜400ppm， 最好 200〜350ppm; N 30〜130ppm， 最好 60〜100ppm; Ti < 50ppm， 最好小于 30ppm; 其余为 Fe及不可避免的杂质。 板坯加热温度 1200〜1320°C， 渗氮温度 850〜1050°C。其余工艺与上面两个基本 相同。
中国专利 CN1244220A中介绍的方法， 该专利的特点在于渗氮与脱碳同步进 行。
其他专利要点在于热轧板中有弥散析出相， 便于高温渗氮。 渗氮温度为 900 〜1000°C。综合来看， 阿奇亚斯佩丝阿里特尔尼公司的低温技术局限于高温渗氮 及（或）薄板坯连铸方法生产取向硅钢， 要点在于热轧板中有弥散析出相， 便于 应用高温渗氮方法， 渗氮为脱碳与渗氮同时进行或脱碳后渗氮。
韩国 P0SC0 公司， 其低温取向硅钢化学成分为： C 0. 02〜0. 045%， Si 2. 9 〜3· 30%， Μη 0· 05〜0· 3%， 酸可溶 Al 0· 005〜0· 019%， Ν 0· 003〜0· 008%， S < 0. 006%, Cu 0. 30〜0. 70%， Ni 0. 30〜0. 70%， Cr 0. 30〜0. 70%， 其余为 Fe及 不可避免的杂质。 此外， 钢中含 B 0. 001〜0. 012%。 脱碳与渗氮同时进行， 在湿 气氛中渗氮。 该方法的基础是以 BN为主抑制剂。
还有如中国专利号 85100664和 88101506. 7 中所述的方法均是建立在抑制 剂在加热过程中固溶、在轧制过程中控制析出的传统工艺方法， 实际加热温度接 近 1300°C， 与本发明方法有本质区别； 宝钢申请的专利 ZL200410099080. 7所述 方法在于脱碳前渗氮。
通过对国内外基于渗氮工艺的低温板坯加热生产取向硅钢技术的专利、 文 献等的査询与分析， 可以发现：
日本的技术集中在脱碳退火后到二次再结晶过程中， 对钢板渗氮， 渗氮温 度低， 抑制剂在高温退火的前期形成； 欧洲的技术为脱碳退火后进行渗氮， 或者 脱碳退火与渗氮同时进行， 渗氮温度高； P0SC0的技术适用于低碳低 A1成分体 系， 渗氮与脱碳同时进行。
用日本的渗氮工艺生产取向硅钢时， 由于钢板内没有抑制剂， 不能抑制一 次再结晶晶粒的长大，一次再结晶晶粒尺寸主要由温度和时间进行控制， 因而脱 碳退火及渗氮工艺的控制要求高， 工艺窗口窄； 另一方面， 由于渗氮在脱碳退火 后进行， 钢板表面已经形成一层以 Si02为主要成分的氧化层， 渗氮的均匀性和 渗氮行为易受表面氧化层的影响。阿奇亚斯佩丝阿里特尔尼公司技术特点在于高 温渗氮， 为了实现该工艺， 热轧板中必须有弥散析出的第二相质点， 板坯的加热 温度较高， 如 125CTC左右， 因而要控制热轧板中的有利夹杂。 另外， 其渗氮在 脱碳后或者与脱碳退火同时进行。 P0SC0也是采取脱碳、 渗氮同时进行的工艺方 式， 钢板表面氧化层对渗氮的影响不可避免； 此外， 钢中的 A1 含量低， 以 BN 为主抑制剂， B 的不稳定性将导致抑制能力的不稳定， 磁性的稳定性会受到很 大影响。
几种低温板坯加热技术取向硅钢的化学成分体系比较如表 1所示。
表 1 化学成分体系比较 单位 wt. %
Figure imgf000006_0001
发明内容
如前所述， 高温板坯加热方法生产取向硅钢具有能耗高、 加热炉使用效率 低、 热轧板边裂大、 生产性不好、 成本低等固有缺点， 低温板坯加热技术生产取 向硅钢可以较好地解决这些问题， 因而具有强大的开发动力。 目前专利文献中公 开的低温板坯加热技术生产取向硅钢， 几乎都是建立在渗氮工艺的基础上的。
本发明的目的在于提供一种用一次冷轧法生产取向硅钢的方法， 通过控制 热轧板常化冷却工艺， 利用板坯在脱碳退火和高温退火低保温阶段的吸氮， 以形 成足量的 （Al、 Si ) N有利夹杂， 利用其对一次再结晶晶粒的抑制作用， 可以有 效地控制钢板的一次再结晶组织， 对获得稳定、完善的二次再结晶成品组织非常 有利； 同时， 本发明克服了其它专利中使用氨气渗氮对底层的不良影响， 有利于 获得良好的玻璃膜底层。
为达到上述目的， 本发明的技术方案是，
用一次冷轧法生产取向硅钢的方法， 其包括如下步骤：
1)冶炼
用转炉或电炉炼钢， 钢水经二次精炼和连铸后， 获得以下成分的铸坯： C 0. 035〜0· 065%, Si 2. 9〜4· 0%， Μη 0. 08〜0· 18%， S 0. 005〜0· 012%, Als 0. 015 〜0· 035%， Ν 0· 0050〜0· 0130%， Sn 0· 001〜0· 15%， Ρ 0· 010〜 0· 030%， Cu 0. 05 〜0. 60%， Cr < 0. 2%, 其余为 Fe及不可避免的夹杂物， 以质量百分比计；
2)热轧
铸坯在加热炉内加热到 1090〜1200°C， 小于 118CTC开轧， 86CTC以上的温度 终轧， 轧成 1. 5〜3. 5mm厚度的热轧板， 卷取温度 500〜650°C；
3)常化
常化退火， 并进行冷却， 退火温度： 1050〜1180°C ( 1〜20 秒） + ( 850〜 950°C X 30〜200秒） ， 冷却速度： 10°C /s〜6(TC /s ;
4)冷轧
用一次冷轧法轧到成品板厚度， 冷轧压下率 75〜92%；
5)脱碳
对轧到成品厚度的钢板进行脱碳退火，涂布以 MgO为主要成分的高温退火隔 离剂； 脱碳温度控制范围为 780〜880°C ; 保护气氛露点 40〜80°C ; 脱碳时间： 80〜350秒； 保护气氛： 与 N2混合气体， 含量： 15〜85%； 脱碳板表面总氧 [0] : 171/t< [0] < 313/t (t为钢板实际厚度， mm) , 吸氮量 2〜10 ppm;
6)高温退火
控制 1000度以下退火保护气氛： 与 N2混合气体或纯 N2， ， 保护气氛露点 0〜50度； 第一段保温时间： 6〜30hr; 对于≥5 ton的钢卷， 最佳的低保温时间 8〜15h; 高温退火， 吸氮量 10〜40ppm;
7)热平整退火，
按常规的热平整工艺进行。
进一步，取向硅钢在上述基本成分的基础上，钢中还可添加 MoO. 01〜0. 10%， 和 /或 Sb≤ 0. 2%， 以质量百分比计。
又， 常化板厚度方向上， 板厚 1/4〜1/3和板厚 2/3〜3/4两处， 高斯织构 (110) [001]和立方织构（001) [110]的比例控制在： 0·2≤ Ι (110) [001] / 丄 (001) [1 ≤ 8， I (110) [001]和 I (001) [110]分别是高斯织构和立方织构的强度； 优选： 0.5≤ 1 (
Figure imgf000008_0001
如果具有高斯织构的晶粒所占比例过大， 将不利于择优长大， 使二次再结 晶后晶粒取向度下降， 从而影响磁性； 如果具有立方织构的晶粒所占比例过大， 高温退火后钢板内将产生大量同类细晶， 从而影响磁性。 此外， 通过控制冷速， 可以实现抑制剂尺寸的优化。
另外， 常化板板厚 1/4〜1/3和板厚 2/3〜3/4两处， 具有高斯织构的晶粒数 占总晶粒数的比例≥ 5%。
本发明方法的显著优点在于：
(1)完全解决了高温取向硅钢生产方法的固有矛盾， 能耗低、 生产成本低， 此外， 由于不需要专用的高温板坯加热炉， 生产的灵活性大大提高， 不构成热轧 机的产能限制， 潜在效益大；
(2) 在化学成分上， 明确了 S和 Cu含量控制范围， 保证了抑制剂弥散、 细小和稳定地析出；
(3) 通过常化工艺的调整， 使织构和部分抑制剂析出最优化；
(4) 不需要使用氨气或其它渗氮介质对钢板进行特殊的渗氮处理， 因而降 低了成本， 保护了环境；
(5) 由于未使用氨气渗氮， 可以避免渗氮对底层的影响， 有利于形成良好 的玻璃膜底层。
传统的取向钢生产工艺中， 为在热轧或热轧板的退火过程中形成细小、 均 匀的 MnS、AlN等抑制剂，必须先将铸坯加热到 1350〜1400°C使铸坯中粗大的 MnS、 A1N析出物固溶， 因此是一种板坯高温加热技术。 为克服高温加热技术带来的氧 化、边裂等严重问题， 开发了采用渗氮形成获得性抑制剂等取向硅钢板坯低温加 热技术， 主要有如下几类： 一是在高温退火隔离剂中添加渗氮化学成分， 然后在 高温退火阶段使钢带渗氮形成 (Al， Si)N等抑制剂， 如日本专利特许公报平 1一 230721、平 1一 283324等； 另一类是利用高温退火升温阶段的渗氮气氛进行渗氮 。 这两类均因渗氮不均匀等原因而没能获得磁性稳定的产品。 在此基础上， 出现 的又一种技术是在中间退火、脱碳退火以后、或在脱碳退火的同时在气氛中通入 活性较强的氨。 本发明未使用氨气作为渗氮介质。 高温退火升温阶段前， 钢板中 氮含量的增加主要来自脱碳退火和高温退火低保温阶段保护气氛中氮气的分解， 与上述专利均不相同。
此外， 本发明由于采用传统的连铸过程， 因此与专利 US6273964B1 和 US6296719B1揭示的采用薄板坯连铸连轧的取向钢生产工艺有较大区别。
阿奇亚斯佩丝阿里特尔尼公司的技术， 属于高温渗氮专利， 渗氮方式也是 采用脱碳后渗氮或脱碳与渗氮同时进行的办法， 与本发明方法不同； 中国专利号 85100664和 88101506. 7中所述的方法均是建立在抑制剂在加热过程中固溶、在 轧制过程中控制析出的传统工艺方法， 实际加热温度接近 1300°C， 与本发明方 法有本质区别。
本发明通过对热轧板常化工艺的调整， 实现对常化后钢板织构和有利夹杂 量的优化； 在脱碳退火过程中，通过控制保护气氛中氮氢比、温度、 时间和露点， 实现脱碳和对钢板表面氧含量的精确控制， 确保获得良好的底层； 同时控制保护 气氛中氮氢比， 使钢板吸氮； 通过对高温退火工序低保温阶段保护气氛中氮氢比 的控制， 获得适量的抑制剂， 确保二次再结晶的完善。 附图概述
图 1为本发明常化板板厚 1/4〜1/3和板厚 2/3〜3/4处示意图；
图 2为本发明可能获得良好底层的脱碳工艺的控制范围图；
图 3为本发明吸氮量大于等于 l Oppm的控制示意图。 本发明的最佳实施方案
实施例 1
用 500kg真空炉炼钢， 化学成分和热轧条件如表 2和表 3所示。 常化条件 1 13CTC X 5s+930°C X 70s+50°C /s 的冷却， 带钢冷轧到 0. 30mm， 脱碳及涂布 MgO 隔离剂后进行高温退火和平整退火， 涂绝缘层， 测量磁性能。 交叉实验结果如表 4所示。
表 2 实验钢化学成分 单位： ％
Figure imgf000009_0001
表 3 实验钢热轧条件 单位 °C 加热温度 终轧温度 卷取温度 厚度 (mm) c 1160 900 500 2.5
D 1240 930 520 2.5
表 4 实验结果
Figure imgf000010_0001
实施例 2
用表 2中 A成分和表 3中 C热轧条件钢进行常化条件实验， 常化工艺条件 1120°CX6s + 910°CXX s+ Y °C/s对织构的影响如表 5所示， 常化工艺条件与 磁性的关系如表 6所示。
表 5 常化工艺条件与织构比例的关系
Figure imgf000010_0002
*在此处具有高斯织构的晶粒数占总晶粒数的比例≥ 5 % 表 6 常化工艺条件与磁性的关系 说明 B8 (T) Pl7 (W/kg) 比较例 1. 50 2. 12
发明例 1. 84 1. 34
发明例 1. 85 1. 25
比较例 1. 80 1. 46
比较例 1. 77 1. 87
发明例 1. 87 1. 17
发明例 1. 90 1. 06
比较例 1. 81 1. 44
实施例 3
用表 2中 A成分和表 3中 C热轧条件钢进行常化条件实验， 常化工艺条件 1120°C X 5s+910°C X 70 + 20°C /s， 脱碳时间、 温度、 露点对磁性和底层的影响 如表 7和表 8所示。
Figure imgf000011_0001
表 8 脱碳温度、 时间和露点与底层的关系 脱碳时间 （S 脱碳温度 露点 保护气氛 增氮量 附着性 * 说 明
) ( °C ) ( °C ) 中 N2比例 ppm (级） 比较例 200 770 +18 10% 1 F 发明例 200 790 +40 55% 5 C 发明例 150 830 +70 18% 3 B 发明例 250 850 +60 50% 7 A 发明例 345 850 +50 25% 7 A 发明例 90 870 +77 80% 8 B 比较例 370 890 +85 14% 9 D 比较例 150 900 +19 88% 7 F
*参考国标 GB/T2522-2007 , 0级〉 A级〉 B级〉 C级〉 D级〉 E级〉 F级， E级以上 为合格品
参见图 2， 从中看出， 能够获得良好底层质量的脱碳温度和脱碳氧化能（露 点、 氢气比例） 。 实施例 4
用表 2中 A成分和表 3中 C热轧条件钢进行常化条件实验， 常化工艺条件 1120°C X 5s+910°C X 70 + 20°C /s , 脱碳 850°C X 200s， 露点 +60°C， 高温退火升 温阶段 1000度以下的保护气氛中氮气比例、 露点和时间对磁性的影响如表 9所 示。
表 9 气氛、 时间和露点与磁性的关系
Figure imgf000012_0001
发明例 12 24% -10 34 1.85 1.20 比较例 3 10% 40 7 1.81 1.51 图 3显示了保护气氛中氮气比例与低保温时间对吸氮量的影响，图中给出了 吸氮量 ^lppm的有利的高温退火条件， 可以获得良好的磁性。 实施例 5
用 500kg真空炉炼钢， 化学成分如表 10， 按照表 3中 C所示的热轧条件进 行热轧； 此后按 1150°CX5s+93(TCX70s + 35°C/s冷却的工艺进行热轧板常化， 带钢冷轧到 0.30mm, 850°CX200s脱碳， 涂布 MgO隔离剂后进行高温退火和平整 退火， 涂绝缘层， 测量磁性， 结果也列于表 10。
表 10 实施例和比较例化学成分 单位： wt%
Figure imgf000013_0001
0. 01 0. 007 0. 008
9 0. 046 2. 94 0. 16 0. 018 0. 11 0. 09 1. 87 1. 15
1 5 5
0. 02 0. 003 0. 006
10 0. 044 3. 10 0. 20 0. 018 0. 13 0. 16 1. 63 2. 00
3 5 7
0. 02 0. 004 0. 007
11 0. 048 3. 11 0. 19 0. 019 0. 11 0. 008 1. 77 1. 55
2 3 2
0. 00 0. 019 0. 007
12 0. 051 3. 32 0. 18 0. 022 0. 61 0. 12 1. 75 1. 64
8 0 7
0. 02 0. 014 0. 004
13 0. 043 3. 09 0. 09 0. 018 0. 28 0. 008 1. 78 1. 62
4 0 7
0. 02 0. 007
14 0. 046 3. 05 0. 15 0. 004 0. 020 0. 66 0. 13 1. 70 2. 03
1 0
0. 02 0. 015 0. 008
15 0. 033 4. 11 0. 19 0. 022 0. 45 0. 13 1. 74 1. 65
5 0 1
0. 02 0. 029 0. 008
16 0. 045 2. 87 0. 19 0. 020 0. 48 0. 14 1. 67 1. 88
1 0 6
*实施例 1〜9， 对比例 10 长期以来取向硅钢生产方法都是采用板坯高温加热的方式， 板坯加热温度 高达 1400°C， 使有利夹杂充分固溶， 并在加热后进行高温轧制， 获得有利的夹 杂物分布与尺寸， 在高温退火时， 抑制初次再结晶晶粒， 获得良好的二次再结晶 组织。 该生产方法的缺点在于：
(1) 必须专用的高温加热炉；
(2) 由于高温加热， 板坯表面融渣严重， 导致加热炉必须频繁修补， 维护 费用高， 炉子的作业率低下；
(3) 板坯的厚度一般为 200〜250mm， 为了加热均匀， 必须长时间加热， 能 耗商；
(4) 板坯内的柱状晶发达， 晶界氧化， 导致边裂严重， 后工序生产性差， 成材率低， 生产成本高。
本发明的方法有效地解决了上述问题， 而且与日本、 韩国 P0SC0 及阿奇亚 斯佩丝阿里特尔尼公司等方法相比，本发明方法通过常化优化了抑制剂尺寸及织 构， 并在脱碳退火和高温退火阶段， 钢板吸氮形成附加的（Al、 Si ) N有利夹杂， 可以有效地控制钢板的一次再结晶组织， 对获得稳定、完善的二次再结晶成品组 织非常有利。 同时本方法不采用特殊渗氮处理， 不需要渗氮装置， 对良好底层的 形成极为有利。
低温板坯加热技术生产取向硅钢代表了取向硅钢发展的前沿技术， 本发明 方法的实施设备均为生产取向硅钢的常规设备， 实现技术简单易行， 因而具有良 好的推广应用前景。

Claims

权 利 要 求
1.用一次冷轧法生产取向硅钢的方法， 其包括如下步骤：
1)冶炼
用转炉或电炉炼钢， 钢水经二次精炼和连铸后， 获得以下成分的铸坯： c
0.035〜0· 065%, Si 2.9〜4· 0%， Μη 0.08〜0· 18%， S 0.005〜0· 012%, Als 0.015 〜0·035%， Ν 0· 0050〜0· 0130%， Sn 0· 001〜0· 15%， Ρ 0· 010〜 0· 030%， Cu 0.05 〜0.60%， Cr < 0.2%, 其余为 Fe及不可避免的夹杂物， 以质量百分比计；
2)热轧
铸坯在加热炉内加热到 1090〜1200°C， 小于 118CTC开轧， 86CTC以上的温度 终轧， 轧成 1.5〜3.5mm厚度的热轧板， 卷取温度 500〜650°C；
3)常化
常化退火， 并进行冷却， 退火温度： 1050〜1180°C (1〜20 秒） + (850〜 950°C X30〜200秒） ， 冷却速度： 10°C/s〜6(TC/s;
4)冷轧
用一次冷轧法轧到成品板厚度， 冷轧压下率 75〜92%；
5)脱碳
对轧到成品厚度的钢板进行脱碳退火，涂布高温退火隔离剂； 脱碳温度控制 范围为 780〜880°C; 保护气氛露点 40〜80°C; 脱碳时间： 80〜350秒； 保护气 氛： 与 N2混合气体， 含量: 15〜85%； 脱碳板表面总氧 [0] :171/t≤ [0]<313/t (t为钢板实际厚度， mm)， 吸氮量 2 〜10 ppm;
6)高温退火
在 1000度以下的退火保护气氛： 与 N2混合气体或 N2， 保护气氛露点 0 〜50度； 第一段保温时间 6〜30hr; 高温退火吸氮量 10〜40ppm;
7)热平整退火，
按常规的热平整工艺进行。
2.如权利要求 1 所述的用一次冷轧法生产取向硅钢的方法， 其特征是， 取 向硅钢在上述基本成分的基础上，钢中还可添加 MoO.01〜0.10%，和 /或 Sb≤ 0.2%, 以质量百分比计。
3.如权利要求 1 所述的用一次冷轧法生产取向硅钢的方法， 其特征是， 常 化板板厚 1/4〜1/3和板厚 2/3〜3/4两处，高斯织构（110)[001]和立方织构（001 ) [110]的比例控制在： 0.2 ≤ I (110) [001]/ 丄（001) [110] ≤ 8， I (110) [001]和 I (001) [110]分 别是高斯织构和立方织构的强度。
4.如权利要求 1 所述的用一次冷轧法生产取向硅钢的方法， 其特征是， 高 斯织构 (110) [001]和立方织构 (001) [110]的比例控制优选: 0.5 < I (no) toon/
I (001) [110] ≤ 2。
5.如权利要求 1 所述的用一次冷轧法生产取向硅钢的方法， 其特征是， 常 化板板厚 1/4〜1/3和板厚 2/3〜3/4两处，具有高斯织构的晶粒数占总晶粒数的 比例≥ 5%。
6.如权利要求 1 所述的用一次冷轧法生产取向硅钢的方法， 其特征是， 对 于≥5^11的钢卷， 第一段保温时间 8〜15h。
PCT/CN2009/076317 2008-12-31 2009-12-31 用一次冷轧法生产取向硅钢的方法 WO2010075797A1 (zh)

Priority Applications (5)

Application Number Priority Date Filing Date Title
JP2011502219A JP5939797B2 (ja) 2008-12-31 2009-12-31 一回冷間圧延法による方向性珪素鋼の製造方法
KR1020117013268A KR101462044B1 (ko) 2008-12-31 2009-12-31 1차 냉간 압연 공정을 포함하고 있는 규소 강철의 제조방법
RU2011132006/02A RU2469104C1 (ru) 2008-12-31 2009-12-31 Способ производства текстурированной кремнистой стали с использованием единственной холодной прокатки
US13/142,955 US9038429B2 (en) 2008-12-31 2009-12-31 Method for manufacturing grain-oriented silicon steel with single cold rolling
EP09836084.5A EP2390373B1 (en) 2008-12-31 2009-12-31 Method for manufacturing grain oriented silicon steel with single cold rolling

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN200810205181.6 2008-12-31
CN200810205181A CN101768697B (zh) 2008-12-31 2008-12-31 用一次冷轧法生产取向硅钢的方法

Publications (1)

Publication Number Publication Date
WO2010075797A1 true WO2010075797A1 (zh) 2010-07-08

Family

ID=42309829

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2009/076317 WO2010075797A1 (zh) 2008-12-31 2009-12-31 用一次冷轧法生产取向硅钢的方法

Country Status (7)

Country Link
US (1) US9038429B2 (zh)
EP (1) EP2390373B1 (zh)
JP (1) JP5939797B2 (zh)
KR (1) KR101462044B1 (zh)
CN (1) CN101768697B (zh)
RU (1) RU2469104C1 (zh)
WO (1) WO2010075797A1 (zh)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2552562C2 (ru) * 2010-09-30 2015-06-10 Баошан Айрон Энд Стил Ко., Лтд. Способ производства листа из текстурированной электротехнической стали с высокой плотностью магнитного потока
CN114645202A (zh) * 2022-03-14 2022-06-21 安阳钢铁集团有限责任公司 一种高取向度GOSS织构Fe-3%Si材料的获得方法

Families Citing this family (39)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102041368A (zh) * 2011-01-16 2011-05-04 首钢总公司 一种表面质量优异的取向电工钢生产方法
CN102127709A (zh) * 2011-01-16 2011-07-20 首钢总公司 一种低温板坯加热高磁感取向硅钢及制造方法
CN102618783B (zh) * 2011-01-30 2014-08-20 宝山钢铁股份有限公司 一种高磁感取向硅钢的生产方法
CN102758127B (zh) * 2011-04-28 2014-10-01 宝山钢铁股份有限公司 具有优异磁性能和良好底层的高磁感取向硅钢生产方法
CN103031420B (zh) * 2011-09-30 2014-12-03 宝山钢铁股份有限公司 一种磁性能优良的取向硅钢生产方法
EP2876173B9 (en) * 2012-07-20 2019-06-19 Nippon Steel & Sumitomo Metal Corporation Manufacturing method of grain-oriented electrical steel sheet
WO2014020369A1 (en) * 2012-07-31 2014-02-06 Arcelormittal Investigación Y Desarrollo Sl Method of production of grain-oriented silicon steel sheet grain oriented electrical steel sheet and use thereof
CN103255274B (zh) * 2012-08-10 2015-06-03 新万鑫（福建）精密薄板有限公司 一般取向硅钢由两次冷轧改为一次冷轧的生产方法
CN103695619B (zh) 2012-09-27 2016-02-24 宝山钢铁股份有限公司 一种高磁感普通取向硅钢的制造方法
CN102899467A (zh) * 2012-10-23 2013-01-30 鞍钢股份有限公司 促进电工钢薄带有利织构生成的方法
CN103834856B (zh) * 2012-11-26 2016-06-29 宝山钢铁股份有限公司 取向硅钢及其制造方法
CN103074476B (zh) * 2012-12-07 2014-02-26 武汉钢铁(集团)公司 一种分三段常化生产高磁感取向硅钢带的方法
KR101480498B1 (ko) * 2012-12-28 2015-01-08 주식회사 포스코 방향성 전기강판 및 그 제조방법
CN103667874A (zh) * 2013-05-20 2014-03-26 新万鑫（福建）精密薄板有限公司 取向硅钢在高温退火期间缩短在炉时间的生产方法
CN103952629B (zh) * 2014-05-13 2016-01-20 北京科技大学 一种中硅冷轧无取向硅钢及制造方法
CN104120233A (zh) * 2014-07-02 2014-10-29 东北大学 一次轧制制备取向高硅钢板的方法
KR101642281B1 (ko) 2014-11-27 2016-07-25 주식회사 포스코 방향성 전기강판 및 이의 제조방법
CN104928567A (zh) * 2015-06-25 2015-09-23 宝山钢铁股份有限公司 具有良好加工性能的晶粒取向硅钢及其制造方法
CN104962816B (zh) * 2015-07-15 2017-10-24 东北大学 一种极薄取向硅钢板及其短流程制造方法
DE102016100648B4 (de) * 2015-12-23 2018-04-12 Benteler Automobiltechnik Gmbh Wärmebehandlungsofen sowie Verfahren zur Wärmebehandlung einer vorbeschichteten Stahlblechplatine und Verfahren zur Herstellung eines Kraftfahrzeugbauteils
WO2017145907A1 (ja) * 2016-02-22 2017-08-31 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
WO2017155057A1 (ja) * 2016-03-09 2017-09-14 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
CN106282779B (zh) * 2016-09-29 2018-03-13 武汉科技大学 一种取向高硅钢薄带及其制备方法
DE102017220714B3 (de) * 2017-11-20 2019-01-24 Thyssenkrupp Ag Optimierung des Stickstofflevels während der Haubenglühung
DE102017220721A1 (de) * 2017-11-20 2019-05-23 Thyssenkrupp Ag Optimierung des Stickstofflevels während der Haubenglühung III
CN108480587B (zh) * 2018-02-13 2020-02-18 鞍钢股份有限公司 一种低夹杂缺陷率高磁感取向硅钢的生产方法
CN109112395B (zh) * 2018-08-10 2020-02-07 全球能源互联网研究院有限公司 一种无底层取向超薄带母材及其制备方法
CN110257700A (zh) * 2019-06-02 2019-09-20 郭慧敏 一种取向硅钢钢带或钢板的制造方法
CN113308647B (zh) * 2020-02-27 2022-06-28 宝山钢铁股份有限公司 一种搪瓷用冷轧钢板及其制造方法
CN112593053A (zh) * 2020-12-14 2021-04-02 海安华诚新材料有限公司 一种气耗优化成本较低的取向硅钢高温退火工艺
CN113211325B (zh) * 2021-05-07 2022-07-12 包头市威丰稀土电磁材料股份有限公司 一种物理喷砂方式制备取向硅钢薄带无底层原料的方法
CN113198866B (zh) * 2021-05-07 2023-03-17 新余钢铁股份有限公司 一种薄规格中高牌号无取向硅钢酸轧生产工艺
CN116463545A (zh) * 2022-01-12 2023-07-21 宝山钢铁股份有限公司 一种含铜低温取向硅钢及其制造方法
CN114622076A (zh) * 2022-03-11 2022-06-14 安阳钢铁股份有限公司 一种低温高磁感取向硅钢的制备方法
CN114622070A (zh) * 2022-03-11 2022-06-14 安阳钢铁股份有限公司 一种改善取向硅钢涂层附着性的生产方法
CN115161453B (zh) * 2022-07-08 2023-11-03 江苏沙钢集团有限公司 一种防止冷轧高牌号硅钢边损边裂的制备方法
WO2024043063A1 (ja) * 2022-08-22 2024-02-29 Ｊｆｅスチール株式会社 焼鈍設備および方向性電磁鋼板の製造方法
CN116004961A (zh) * 2022-12-12 2023-04-25 湖南华菱涟钢特种新材料有限公司 取向硅钢的制备方法及取向硅钢
CN116200661A (zh) * 2023-01-04 2023-06-02 广东电网有限责任公司 一种立方双取向硅钢及其制备方法和应用

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN85100664A (zh) 1985-04-01 1986-09-24 冶金工业部钢铁研究总院 降低普通取向硅钢板坯加热温度的方法
JPH01230721A (ja) 1987-11-20 1989-09-14 Nippon Steel Corp 磁束密度の高い一方向性珪素鋼板の製造方法
JPH01283324A (ja) 1988-05-11 1989-11-14 Nippon Steel Corp 磁束密度の高い一方向性電磁鋼板の製造方法
EP0420238A2 (en) * 1989-09-28 1991-04-03 Nippon Steel Corporation Process for preparing unidirectional silicon steel sheet having high magnetic flux density
JPH05112827A (ja) 1988-04-25 1993-05-07 Nippon Steel Corp 磁気特性、皮膜特性ともに優れた一方向性電磁鋼板の製造方法
CN1228817A (zh) 1996-08-30 1999-09-15 阿奇亚斯佩丝阿里特尔尼公司 用薄钢坯生产具有高的磁性能的晶粒取向电工钢带的工艺
CN1231703A (zh) 1996-09-05 1999-10-13 阿奇亚斯佩丝阿里特尔尼公司 由薄板坯生产晶粒取向电工钢带的方法
CN1242057A (zh) 1996-12-24 2000-01-19 阿奇亚斯佩丝阿里特尔尼公司 具有高磁性能的晶粒取向电工钢片的制造工艺
CN1244220A (zh) 1996-12-24 2000-02-09 阿奇亚斯佩丝阿里特尔尼公司 晶粒取向硅钢的处理工艺

Family Cites Families (17)

* 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
JPS53129116A (en) * 1977-04-18 1978-11-10 Nippon Steel Corp Oriented electromagnetic steel sheet with excellent magnetic characteristic s
US4115161A (en) * 1977-10-12 1978-09-19 Allegheny Ludlum Industries, Inc. Processing for cube-on-edge oriented silicon steel
JPS60145318A (ja) * 1984-01-09 1985-07-31 Kawasaki Steel Corp 方向性けい素鋼スラブの加熱方法
US4997493A (en) * 1987-11-27 1991-03-05 Nippon Steel Corporation Process for production of double-oriented electrical steel sheet having high flux density
DE69032461T2 (de) * 1989-04-14 1998-12-03 Nippon Steel Corp., Tokio/Tokyo Verfahren zur Herstellung von kornorientierten Elektrostahlblechen mit hervorragenden magnetischen Eigenschaften
JPH04341518A (ja) * 1991-01-29 1992-11-27 Nippon Steel Corp 極薄手高磁束密度低鉄損一方向性電磁鋼板の製造方法
RU2000341C1 (ru) * 1992-02-07 1993-09-07 Новолипецкий металлургический комбинат им.Ю.В.Андропова Способ производства изотропной электротехнической стали
JP2000119817A (ja) * 1998-10-14 2000-04-25 Sumitomo Metal Ind Ltd マルテンサイト系ステンレス鋼管
JP3659041B2 (ja) * 1998-12-25 2005-06-15 Ｊｆｅスチール株式会社 強度変動の極めて小さい高強度冷延鋼板の製造方法
RU2223334C2 (ru) * 2002-03-26 2004-02-10 Открытое акционерное общество "Щелковский металлургический завод" Способ производства стальных полос для магнитных экранов
FR2850671B1 (fr) * 2003-02-05 2006-05-19 Usinor Procede de fabrication d'une bande d'acier dual-phase a structure ferrito-martensitique, laminee a froid et bande obtenue
JP4747564B2 (ja) * 2004-11-30 2011-08-17 Ｊｆｅスチール株式会社 方向性電磁鋼板
CN100381598C (zh) 2004-12-27 2008-04-16 宝山钢铁股份有限公司 一种取向硅钢及其生产方法和装置
CN1743128A (zh) * 2005-09-29 2006-03-08 东北大学 连铸板坯直接轧制生产取向硅钢带的方法
CN1743127A (zh) * 2005-09-29 2006-03-08 东北大学 薄板坯连铸连轧生产取向硅钢带的方法
JP5320690B2 (ja) * 2006-05-24 2013-10-23 新日鐵住金株式会社 磁束密度の高い方向性電磁鋼板の製造方法

Patent Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN85100664A (zh) 1985-04-01 1986-09-24 冶金工业部钢铁研究总院 降低普通取向硅钢板坯加热温度的方法
JPH01230721A (ja) 1987-11-20 1989-09-14 Nippon Steel Corp 磁束密度の高い一方向性珪素鋼板の製造方法
JPH05112827A (ja) 1988-04-25 1993-05-07 Nippon Steel Corp 磁気特性、皮膜特性ともに優れた一方向性電磁鋼板の製造方法
JPH01283324A (ja) 1988-05-11 1989-11-14 Nippon Steel Corp 磁束密度の高い一方向性電磁鋼板の製造方法
EP0420238A2 (en) * 1989-09-28 1991-04-03 Nippon Steel Corporation Process for preparing unidirectional silicon steel sheet having high magnetic flux density
JPH03211232A (ja) 1989-09-28 1991-09-17 Nippon Steel Corp 磁束密度の高い一方向性珪素鋼板の製造方法
CN1228817A (zh) 1996-08-30 1999-09-15 阿奇亚斯佩丝阿里特尔尼公司 用薄钢坯生产具有高的磁性能的晶粒取向电工钢带的工艺
US6296719B1 (en) 1996-08-30 2001-10-02 Acciai Speciali Terni S.P.A. Process for the production of grain oriented electrical steel strip having high magnetic characteristics, starting from thin slabs
CN1231703A (zh) 1996-09-05 1999-10-13 阿奇亚斯佩丝阿里特尔尼公司 由薄板坯生产晶粒取向电工钢带的方法
US6273964B1 (en) 1996-09-05 2001-08-14 Acciali Speciali Terni S.P.A. Process for the production of grain oriented electrical steel strip starting from thin slabs
CN1242057A (zh) 1996-12-24 2000-01-19 阿奇亚斯佩丝阿里特尔尼公司 具有高磁性能的晶粒取向电工钢片的制造工艺
CN1244220A (zh) 1996-12-24 2000-02-09 阿奇亚斯佩丝阿里特尔尼公司 晶粒取向硅钢的处理工艺

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP2390373A4

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2552562C2 (ru) * 2010-09-30 2015-06-10 Баошан Айрон Энд Стил Ко., Лтд. Способ производства листа из текстурированной электротехнической стали с высокой плотностью магнитного потока
CN114645202A (zh) * 2022-03-14 2022-06-21 安阳钢铁集团有限责任公司 一种高取向度GOSS织构Fe-3%Si材料的获得方法

Also Published As

Publication number Publication date
EP2390373B1 (en) 2020-11-25
CN101768697A (zh) 2010-07-07
JP2011518947A (ja) 2011-06-30
KR101462044B1 (ko) 2014-11-14
CN101768697B (zh) 2012-09-19
KR20110093883A (ko) 2011-08-18
US20120000262A1 (en) 2012-01-05
US9038429B2 (en) 2015-05-26
EP2390373A4 (en) 2016-12-21
EP2390373A1 (en) 2011-11-30
JP5939797B2 (ja) 2016-06-22
RU2469104C1 (ru) 2012-12-10

Similar Documents

Publication Publication Date Title
WO2010075797A1 (zh) 用一次冷轧法生产取向硅钢的方法
JP2782086B2 (ja) 磁気特性、皮膜特性ともに優れた一方向性電磁鋼板の製造方法
JP5479448B2 (ja) 高電磁気性能の方向性珪素鋼の製造方法
CN102758127B (zh) 具有优异磁性能和良好底层的高磁感取向硅钢生产方法
US10236105B2 (en) High magnetic induction oriented silicon steel and manufacturing method thereof
CN100381598C (zh) 一种取向硅钢及其生产方法和装置
WO2021027797A1 (zh) 一种高磁感取向硅钢及其制造方法
CN103695619B (zh) 一种高磁感普通取向硅钢的制造方法
JP2011518947A5 (zh)
WO2006132095A1 (ja) 磁気特性が極めて優れた方向性電磁鋼板及びその製造方法
CN101845582A (zh) 一种高磁感取向硅钢产品的生产方法
CN103534366B (zh) 具有低铁损和高磁通密度的取向电工钢板及其制造方法
EP3561103A1 (en) Grain-oriented electrical steel sheet and manufacturing method therefor
WO2016098917A1 (ko) 방향성 전기강판 및 그 제조방법
CN101824582B (zh) 采用多元抑制剂的取向电工钢板带及其生产方法
KR20200076517A (ko) 방향성의 전기강판 및 그 제조 방법
KR20150073802A (ko) 방향성 전기강판 및 그 제조방법
KR102319831B1 (ko) 방향성 전기강판의 제조방법
WO2024169741A1 (zh) 一种高磁感取向硅钢及其制造方法
WO2023131223A1 (zh) 一种磁性能优良的无取向电工钢板及其制造方法
JPH0730395B2 (ja) 表面脹れ欠陥の無い一方向性電磁鋼板の製造法
JPS6148761B2 (zh)
JPH07110974B2 (ja) 方向性珪素鉄合金薄帯の製造法
JP2002129236A (ja) 一方向性電磁鋼板の安定製造方法
CN115747650A (zh) 一种低温高磁感取向硅钢及提高其磁性能稳定性的方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 09836084

Country of ref document: EP

Kind code of ref document: A1

WWE Wipo information: entry into national phase

Ref document number: 2011502219

Country of ref document: JP

ENP Entry into the national phase

Ref document number: 20117013268

Country of ref document: KR

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

WWE Wipo information: entry into national phase

Ref document number: 2009836084

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 2011132006

Country of ref document: RU

WWE Wipo information: entry into national phase

Ref document number: 13142955

Country of ref document: US