WO2024169741A1 - Acier au silicium orienté à induction magnétique élevée et son procédé de fabrication - Google Patents

Acier au silicium orienté à induction magnétique élevée et son procédé de fabrication Download PDF

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WO2024169741A1
WO2024169741A1 PCT/CN2024/076060 CN2024076060W WO2024169741A1 WO 2024169741 A1 WO2024169741 A1 WO 2024169741A1 CN 2024076060 W CN2024076060 W CN 2024076060W WO 2024169741 A1 WO2024169741 A1 WO 2024169741A1
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oriented silicon
silicon steel
temperature
decarburization annealing
annealing
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PCT/CN2024/076060
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English (en)
Chinese (zh)
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孙焕德
李国保
杨勇杰
章华兵
吴美洪
刘德胜
赵自鹏
徐琪
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宝山钢铁股份有限公司
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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • 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
    • C22C38/04—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/24—Nitriding
    • C23C8/26—Nitriding of ferrous surfaces

Definitions

  • the present disclosure relates to a steel plate and a method for manufacturing the same, and in particular to an oriented silicon steel and a method for manufacturing the same.
  • the high-temperature process uses MnS+AIN as an inhibitor and adopts normalization + one-time cold rolling process to produce high-temperature HiB steel.
  • the obvious feature of this production process is that the slab heating temperature of up to 1400°C is required during the hot rolling process, so that the MnS and AlN in the steel plate are fully dissolved, and precipitated as fine dispersed second-phase particles in the subsequent normalization process, which acts as an inhibitor of primary grain growth, prompting the formation of larger Gaussian grains during the high-temperature annealing and secondary recrystallization process, so as to obtain high-magnetic induction oriented silicon steel products with high orientation and low iron loss.
  • high-temperature slab heating has the disadvantages of low yield, serious slag accumulation at the bottom of the furnace, low output, high energy consumption, shortened furnace life, high manufacturing cost, many surface defects of the product, and unstable magnetic properties.
  • the low-temperature HiB production process can reduce the slab heating temperature to 1150°C, add only a trace amount of Al elements during steelmaking, and perform nitriding treatment after decarburization annealing.
  • the main feature of this process is that when low-temperature heating is performed for decarburization annealing, coarse sulfides and nitrides cannot be dissolved in solid, and inhibitors cannot be formed during hot rolling and normalizing. Instead, the inhibitor AlN is formed in a nitridable atmosphere after decarburization annealing.
  • the low-temperature slab heating process since AlN cannot be completely dissolved in solid during the heating stage, the number of inhibitors will be insufficient, and secondary recrystallization cannot fully occur. For this reason, many manufacturers have studied various methods to strengthen inhibitors, improve secondary recrystallization and/or increase the magnetic induction strength of oriented silicon steel.
  • the thin slab continuous casting and rolling process can also be used to produce oriented silicon steel.
  • the cast slab is directly hot-rolled, which shortens the production process and saves energy.
  • the thin slab continuous casting and rolling process for producing oriented silicon steel has the advantages of fast solidification of the slab, low segregation, small size and dispersed distribution of inhibitors (MnS, AlN, etc.).
  • the edges of hot-rolled silicon steel sheets often have defects, such as hard slag inclusions and tiny cracks of non-metallic materials at the edges; and in the subsequent cold rolling process, the steel plate not only bears tensile force and bending force, but also large plastic deformation. The defects will expand under such complex stress and deformation conditions, causing more serious cold rolling edge cracks and even broken strips.
  • the traditional hot rolling process often adopts the method of controlling the oxygen in the protective atmosphere during the slab reheating. Measures such as adjusting the mass fraction and holding time as well as adjusting the rough rolling reduction rate and rolling temperature can reduce grain boundary oxidation, refine the steel plate grains, and achieve the purpose of reducing edge cracks.
  • one of the objectives of the present disclosure is to provide a high magnetic induction oriented silicon steel, which has excellent magnetic induction performance and a low hot-rolled coil cracking rate, thereby greatly improving the yield rate.
  • the present disclosure provides a grain-oriented silicon steel, which, in addition to Fe and unavoidable impurities, further contains the following chemical elements in the following mass percentages:
  • the present disclosure also provides a oriented silicon steel, the mass percentage content of each chemical element of which is as follows:
  • the oriented silicon steel disclosed herein further contains at least one of the following chemical elements in the following mass percentages: 0 ⁇ Cr ⁇ 0.30%; 0 ⁇ Cu ⁇ 0.3%; 0 ⁇ Nb ⁇ 0.01%; 0 ⁇ Bi ⁇ 0.05%.
  • the unavoidable impurities include V element and Ti element, and V ⁇ 0.01%, and Ti ⁇ 0.01%.
  • the mass percentage content of each chemical element satisfies at least one of the following items: One less: C: 0.04 ⁇ 0.08%, Si: 3.0-4.0%, Mn: 0.08 ⁇ 0.18%, P: 0.005 ⁇ 0.04%, S: 0.006 ⁇ 0.01%, Als: 0.02 ⁇ 0.04%, N: 0.004 ⁇ 0.009%, Sn: 0.03 ⁇ 0.20%, Mo: 0.015 ⁇ 0.025%.
  • the average secondary recrystallization grain size (average secondary recrystallization grain diameter D) of the grain-oriented silicon steel disclosed in the present invention is greater than 20 mm.
  • the magnetic induction B 8 of the oriented silicon steel disclosed in the present invention is ⁇ 1.95T.
  • the ratio of the magnetic induction B8 to the saturation magnetic induction value Bs ( B8 /Bs) of the oriented silicon steel disclosed in the present invention is greater than 0.98.
  • the iron loss P 17/50 of the grain-oriented silicon steel disclosed in the present invention is less than 1.00 W/kg.
  • the cold-rolling burr reduction ratio ⁇ of the grain-oriented silicon steel disclosed in the present invention is ⁇ 90%.
  • the present disclosure also provides a method for manufacturing the above-mentioned oriented silicon steel, comprising the following steps:
  • the slab thickness is 60-70 mm
  • the slab soaking temperature is 1100-1200°C
  • the soaking time in the furnace is 20-40 min;
  • An insulating coating is applied to the surface of the annealed sheet, and hot-stretching and flattening annealing is performed to obtain oriented silicon steel.
  • the superheat of the molten steel is 20-40° C. and the casting speed is 3-5 mpm.
  • the hot rolling start temperature is 1000-1150°C
  • the hot rolling finish temperature is 850-1050°C.
  • step (2) laminar cooling is performed after rolling, and then coiling is performed, and the coiling temperature is below 650° C.
  • the coiling temperature is below 650° C., it can be further ensured that no coarse precipitates are formed.
  • the cold rolling in step (4) also includes intermediate annealing.
  • the oriented silicon steel disclosed in the present invention is obtained based on a thin slab continuous casting and rolling process, which effectively avoids the problem of hot rolled coil cracking.
  • the inventors have found through research that the thickness of the slab has a significant effect on the size of the precipitates after continuous casting and rolling.
  • the slab thickness is 60-70 mm, the equivalent diameter of the precipitates is small.
  • the slab of the oriented silicon steel prepared by the method disclosed in the present invention is thin, the casting cooling speed is fast, and the precipitates are small.
  • the method disclosed in the present invention can effectively reduce the cracking of hot-rolled coils and improve the yield rate.
  • the specific normalizing annealing process disclosed in the present invention can precipitate fine inhibitors such as AlN, increase the number of recrystallized grains in the hot-rolled plate, and make the texture distribution more reasonable.
  • the two-stage decarburization annealing process disclosed in the present invention decarburization is sufficient, the glass film quality is improved, the secondary recrystallization is stable, and the secondary recrystallization grains are small, thereby improving the magnetic properties.
  • nitriding treatment is performed during or after the decarburization annealing process to form favorable inclusions.
  • nitriding temperature is 750-900°C
  • nitriding time is 5-50s
  • nitriding atmosphere is NH3 + H2 + N2
  • the volume percentage of NH3 in the nitriding atmosphere is 0.1-15%)
  • the nitrogen infiltrated into the surface of the steel plate will diffuse and form favorable inclusions mainly composed of (Al, Si)N, which will inhibit the growth of primary grains and prepare for secondary recrystallization, so that the molar ratio of acid-soluble aluminum to nitrogen content of the steel plate before secondary recrystallization Als/[N] meets the following requirements: 1 ⁇ Als/[N] ⁇ 1.8, thereby obtaining an ultra-high magnetic induction oriented silicon steel product with B8 ⁇ 1.95T.
  • FIG. 1 shows the effect of slab thickness on precipitate size in the grain-oriented silicon steel of the present disclosure.
  • FIG. 2 shows the effect of the molar ratio of acid-soluble aluminum to nitrogen content (Als/[N]) on the magnetic induction B8 of the oriented silicon steel of the present invention before secondary recrystallization.
  • the average grain size of secondary recrystallization is measured as described in the embodiment part, specifically: a single magnetic test sample is pickled to remove the surface coating and show the macro grains, and the sample is photographed to obtain an image; the image of the secondary recrystallization grain is then processed by image processing software, and the equivalent circular diameter of the secondary recrystallization grains in the image is obtained by the area method, and the average value of the equivalent circular diameter of the secondary recrystallization grains is obtained as the average grain size of the secondary recrystallization.
  • the magnetic induction B8 and B25 are measured according to GB/T 13789-2008 “Method for measuring magnetic properties of electrical steel sheets (strips) using a single-piece tester”; and B25 is defined as the saturation magnetic induction value Bs.
  • the iron loss P 17/50 is measured using a 0.3 mm thick sample in accordance with GB/T 13789-2008 “Method for measuring the magnetic properties of electrical steel sheets (strips) using a single-piece tester”.
  • the cold rolling burr reduction ratio ⁇ refers to the ratio of the number of hot-rolled coils directly used without trimming during cold rolling to the total number of hot-rolled coils.
  • pH 2 O/pH 2 refers to the partial pressure ratio of water to hydrogen in the atmosphere, which is obtained by measuring the dew point in the atmosphere, determining the water content, and calculating based on the hydrogen content.
  • the nitrogen content is represented by [N] because the nitrogen content of the steel plate has changed compared with the smelting composition at this time.
  • the main function of the C element is to make the steel contain 20% to 30% of the ⁇ phase during the hot rolling process.
  • Phase transformation can refine the hot-rolled steel plate structure and make the hot-rolled steel plate structure present a specific structure gradient along the thickness direction of the steel plate. That is, the C content in the center of the steel plate is high and the grain structure is fine, while the C content near the surface of the steel plate is low and the ferrite grains are coarse due to decarburization, which makes it easy to form coarse and accurately oriented Gaussian grains along the rolling direction.
  • the C content in the steel should not be too high.
  • the mass percentage of the C element is controlled between 0.035 and 0.120%.
  • the mass percentage of the C element is controlled between 0.04 and 0.08%.
  • the Si element can effectively reduce the iron loss of the finished steel plate.
  • the Si content in the steel should not be too high. If the Si content in the steel is too high, the ⁇ phase content will decrease sharply, making the material processing difficult, the structure of the hot-rolled steel plate coarse, the precipitated inhibitors coarse, the number reduced, the inhibitory force reduced, the primary recrystallization grains coarse, the ⁇ 110 ⁇ pole density in the primary recrystallization structure reduced, and the secondary recrystallization difficult.
  • the Si content in the steel is too high, the carbide particles precipitated after the normalizing step will be coarse, affecting the cold rolling aging and decarburization annealing. Therefore, in the oriented silicon steel disclosed in the present invention, the mass percentage of the Si element is controlled to be between 2.5 and 4.5%.
  • the mass percentage of Si element is controlled between 3.0 and 4.0%.
  • the Mn element can prevent the hot-rolled plate from being hot brittle, and can also combine with the S element to form MnS precipitates, thereby making the grains of the primary recrystallization small and uniform, and promoting the development of secondary recrystallization.
  • the Mn element can also expand the ⁇ phase region in the steel, which can effectively reduce the amount of C element added in the steel, thereby reducing the burden of decarburization in the subsequent process.
  • the Mn element content in the steel should not be too high. If the Mn element content in the steel is too high, the ⁇ phase will appear in the subsequent process, interfering with the secondary recrystallization process. Therefore, in the oriented silicon steel disclosed in the present invention, the mass percentage of the Mn element is controlled between 0.05 and 0.20%.
  • the mass percentage of the Mn element is controlled between 0.08 and 0.18%.
  • the P element in the oriented silicon steel disclosed in the present invention, can effectively promote the primary recrystallization grains to be finer and more uniform, while increasing the proportion of ⁇ 111 ⁇ texture in the primary recrystallization grains, making the secondary recrystallization perfect.
  • the mass percentage of the P element is controlled to be between 0.005% and 0.05%.
  • the mass percentage of P element is controlled between 0.005 and 0.04%.
  • the S content in the steel should not be too high.
  • the mass percentage of the S element is controlled to be between 0.005 and 0.012%.
  • the mass percentage of S element is controlled between 0.006 and 0.01%.
  • Als and N In the oriented silicon steel disclosed in the present invention, Als (acid-soluble aluminum) in the steel can be combined with N element to form AlN.
  • AlN is the main inhibitor in oriented silicon steel. From the perspective of ensuring sufficient magnetic properties, the content of acid-soluble aluminum needs to be between 0.015 and 0.045%, and the content of nitrogen needs to be above 0.003%. In addition, when the N content is greater than 0.01%, the casting is prone to swelling. The product will have peeling and blistering defects.
  • the mass percentage of Als is controlled between 0.02% and 0.04%, and the N content is controlled between 0.004% and 0.009%.
  • the Mo element is the core element for controlling the edge cracking of the hot-rolled plate.
  • the addition of Mo can reduce the cracking of the hot-rolled plate.
  • the enrichment of Mo on the surface of the hot-rolled plate can inhibit the oxidation of the grain boundaries, form Mo 3 S 3 near the surface and prevent the formation of FeS, promote the refinement of the primary grains and prevent the cracking of the grain boundaries.
  • the addition of Mo can also increase the secondary crystal nuclei, improve the accuracy of the orientation, and improve the magnetic induction intensity.
  • the mass percentage of Mo element is controlled within the range of 0.015-0.025%.
  • Sn is a grain boundary segregation element.
  • An appropriate amount of Sn element added to the steel can enhance the inhibitory effect on grain growth, prevent premature denitrification and nitrogenation during high-temperature annealing, promote the perfection of secondary recrystallization, and improve the magnetic properties of the steel.
  • the Sn element occupies the grain boundaries, it hinders the diffusion of the O element in the steel and affects the formation of the underlying embedded structure, which may cause the quality of the underlying layer to deteriorate. Therefore, the quality of the underlying layer can be compensated by adding Cr and Cu elements. Based on this, in the oriented silicon steel disclosed in the present invention, the mass percentage of the Sn element is controlled to be between 0.03 and 0.30%.
  • the mass percentage of Sn element is controlled between 0.03 and 0.20%.
  • the oriented silicon steel disclosed herein further contains at least one of the following chemical elements in the following mass percentages: 0 ⁇ Cr ⁇ 0.30%; 0 ⁇ Cu ⁇ 0.3%; 0 ⁇ Nb ⁇ 0.01%; 0 ⁇ Bi ⁇ 0.05%.
  • the mass percentage of Cr is controlled between 0.05 and 0.30%.
  • the mass percentage of Cr element is controlled to be 0.08-0.28%.
  • the addition of Cu can increase the ⁇ phase content, appropriately reduce the C content, and reduce the slab heating temperature.
  • the addition of Cu can precipitate (Cu, Mn)xS or CuxS particles.
  • the precipitation temperature of (Cu, Mn)xS or CuxS is 80°C to 100°C lower than that of MnS, so it helps to reduce the slab heating temperature.
  • the precipitated (Cu, Mn)xS or CuxS is finer and more dispersed than MnS, and the precipitation amount is also significantly increased, so the inhibition of grain growth is enhanced, and the secondary cold rolling reduction rate and the magnetic properties of the finished product are improved.
  • the addition of Cu can improve the hot-rolled plate and decarburization annealing.
  • the ⁇ 110 ⁇ 001> oriented grains are increased, the ⁇ 100 ⁇ 001> oriented grains are reduced, and the secondary recrystallization is promoted; the addition of Cu can also improve the effect of glass film deterioration caused by the addition of Sn or Sb.
  • the mass percentage of Cu element is controlled between 0 ⁇ Cu ⁇ 0.3%.
  • the unavoidable impurities include V and Ti, and V ⁇ 0.01%, and Ti ⁇ 0.01%.
  • the inevitable impurities are mainly V and Ti.
  • V and Ti are strong carbide or oxide forming elements. When the content of V and Ti is high, it will affect the decarburization annealing process, so it must be controlled. Therefore, in the oriented silicon steel disclosed in the present invention, V ⁇ 0.01% and Ti ⁇ 0.01%.
  • the number of coarse MnS+AlN composite precipitates in the slab with TiN, TiC, and VN as the core can be greatly reduced.
  • the average grain size of the oriented silicon steel after secondary recrystallization is greater than 20 mm.
  • the finished magnetic properties of the oriented silicon steel are obtained by relying on the principle of secondary recrystallization and forming a single Gaussian texture ⁇ 110 ⁇ 001>.
  • Secondary recrystallization refers to the phenomenon that most of the grains of the deformed metal cannot grow normally during heating and recrystallization due to restrictions of certain conditions (such as inhibitors, textures, etc.), and only a few grains (Gaussian grains) swallow up grains in other orientations and grow abnormally. Only those Gaussian nuclei with more accurate orientations can grow and obtain size effects to swallow up grains in other orientations. The number of secondary recrystallized grains is reduced and the size of secondary recrystallized grains is increased, which can ultimately enable the steel to obtain better magnetic properties.
  • the oriented silicon steel disclosed in the present invention optimizes the chemical composition design of the steel, especially adds a proper amount of Mo element, effectively reduces the cracking of hot-rolled coils, makes the cold-rolled burr rolling rate above 90%, and improves the yield rate.
  • the present invention adjusts the normalizing annealing, decarburization and nitriding processes so that the molar ratio of acid-soluble aluminum to nitrogen content in oriented silicon steel before secondary recrystallization meets the condition of 1 ⁇ Als/[N] ⁇ 1.8, thereby enhancing the ability to suppress primary grains, making the average grain diameter D of secondary recrystallization of the finished product ⁇ 20 mm, and finally obtaining a stable ultra-high magnetic induction product, wherein the magnetic induction B 8 ⁇ 1.95 T, the ratio of the magnetic induction B 8 to the saturation magnetic induction value Bs ⁇ 8 /Bs ⁇ 0.98, and the iron loss P 17/50 of the finished product with a thickness of 0.3 mm ⁇ 1.00 W/kg.
  • Table 1 lists the mass percentage of each chemical element in the oriented silicon steels of Examples 1-18 and the comparative steels of Comparative Examples 1-8.
  • Example 1-18 and the comparative steel of Comparative Example 1-8 were prepared by the following steps (specific process parameters are shown in Tables 2-1, 2-2 and 2-3):
  • An insulating coating is applied to the surface of the annealed sheet, and hot-stretching and flattening annealing is performed to obtain an oriented silicon steel coil.
  • Tables 2-1, 2-2 and 2-3 list the specific process parameters of the oriented silicon steels of Examples 1-18 and the comparative steels of Comparative Examples 1-8.
  • the average grain size of secondary recrystallization is obtained by pickling a single magnetic test sample to remove the surface coating and display the macro grains, photographing the sample and obtaining an image.
  • the image of the secondary recrystallization grains is then processed using image processing software, and the equivalent circular diameter of the secondary recrystallization grains in the image is obtained using the area method.
  • the average value of the equivalent circular diameters of the secondary recrystallization grains is obtained as the average grain size of the secondary recrystallization.
  • the magnetic parameters are measured according to GB/T 13789-2008 "Method for measuring magnetic properties of electrical steel sheets (strips) using a single-piece tester”. Line measurement.
  • Cold rolling burr reduction ratio ⁇ the ratio of the number of hot-rolled coils directly used without trimming during cold rolling to the total number of hot-rolled coils.
  • Table 3 lists the observation and performance test results of the oriented silicon steels of Examples 1-9 and the comparative steels of Comparative Examples 1-6.
  • the magnetic induction B8 of the oriented silicon steel of Examples 1-18 is significantly higher than that of the comparative steel of Comparative Examples 1-8, and the iron loss P17 /50 is significantly lower than that of the comparative steel of Comparative Examples 1-8.
  • the average grain size of the secondary recrystallization in the oriented silicon steel of Examples 1-18 is above 20 mm, and the magnetic induction B8 is ⁇ 1.95 T, the ratio of the magnetic induction B8 to the saturation magnetic induction value Bs is ⁇ 8 /Bs ⁇ 0.98, and the iron loss P17 /50 of the finished product with a thickness of 0.3 mm is ⁇ 1.00 W/kg.
  • the cold rolling burr reduction ratio ⁇ of the oriented silicon steel of Examples 1-18 is ⁇ 90%, while the cold rolling burr reduction ratio ⁇ of Comparative Examples 1-8 is less than 90%.
  • the oriented silicon steel of Examples 1-18 can not only obtain excellent magnetic properties but also avoid the edge crack problem.
  • FIG2 shows the effect of the molar ratio of acid-soluble aluminum to nitrogen content (Als/[N]) on the magnetic induction B8 of the oriented silicon steel of the present invention before secondary recrystallization.

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Abstract

La présente divulgation concerne un acier au silicium orienté. L'acier au silicium orienté contient les éléments chimiques suivants, en pourcentage en masse, en plus du Fe et des impuretés inévitables : C : de 0,035 à 0,120 %, Si : de 2,5 à 4,5 %, Mn : de 0,05 à 0,20 %, P : de 0,005 à 0,05 %, S : de 0,005 à 0,012 %, Al : de 0,015 à 0,045 %, N : de 0,003 à 0,010 %, Sn : de 0,03 à 0,30 % et Mo : de 0,01 à 0,03 %. L'acier au silicium orienté de la présente divulgation présente d'excellentes performances d'induction magnétique. De plus, la présente divulgation concerne également un procédé de fabrication de l'acier au silicium orienté. Le procédé de la présente divulgation, grâce à l'adoption de proportions appropriées des constituants d'acier et de traitements spécifiques de recuit de normalisation, de décarburation et de nitruration, permet d'obtenir un produit fini en acier au silicium orienté stable présentant une induction magnétique ultra-élevée et empêche la fissuration de bord, ce qui augmente considérablement le rendement du produit.
PCT/CN2024/076060 2023-02-17 2024-02-05 Acier au silicium orienté à induction magnétique élevée et son procédé de fabrication WO2024169741A1 (fr)

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Citations (6)

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Publication number Priority date Publication date Assignee Title
RU2192484C2 (ru) * 1996-12-24 2002-11-10 Аччаи Спечьяли Терни С.п.А. Способ изготовления полос из кремнистой стали с ориентированной зернистой структурой
CN108546814A (zh) * 2018-04-11 2018-09-18 北京科技大学 一种基于esp无头轧制技术生产高磁感取向硅钢的方法
CN110318005A (zh) * 2018-03-30 2019-10-11 宝山钢铁股份有限公司 一种高磁感取向硅钢及其制造方法
CN113272456A (zh) * 2019-01-16 2021-08-17 日本制铁株式会社 方向性电磁钢板的制造方法
CN114277309A (zh) * 2020-09-27 2022-04-05 宝山钢铁股份有限公司 一种高磁感取向硅钢及其制造方法
CN114277308A (zh) * 2020-09-27 2022-04-05 宝山钢铁股份有限公司 一种高磁感取向硅钢及其制造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2192484C2 (ru) * 1996-12-24 2002-11-10 Аччаи Спечьяли Терни С.п.А. Способ изготовления полос из кремнистой стали с ориентированной зернистой структурой
CN110318005A (zh) * 2018-03-30 2019-10-11 宝山钢铁股份有限公司 一种高磁感取向硅钢及其制造方法
CN108546814A (zh) * 2018-04-11 2018-09-18 北京科技大学 一种基于esp无头轧制技术生产高磁感取向硅钢的方法
CN113272456A (zh) * 2019-01-16 2021-08-17 日本制铁株式会社 方向性电磁钢板的制造方法
CN114277309A (zh) * 2020-09-27 2022-04-05 宝山钢铁股份有限公司 一种高磁感取向硅钢及其制造方法
CN114277308A (zh) * 2020-09-27 2022-04-05 宝山钢铁股份有限公司 一种高磁感取向硅钢及其制造方法

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