EP4527965A1 - Acier en bande laminé à chaud à haute résistance et haute plasticité à résistance élevée aux intempéries et son procédé de fabrication - Google Patents

Acier en bande laminé à chaud à haute résistance et haute plasticité à résistance élevée aux intempéries et son procédé de fabrication Download PDF

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EP4527965A1
EP4527965A1 EP23823231.8A EP23823231A EP4527965A1 EP 4527965 A1 EP4527965 A1 EP 4527965A1 EP 23823231 A EP23823231 A EP 23823231A EP 4527965 A1 EP4527965 A1 EP 4527965A1
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hot
strip steel
rolled strip
steel
temperature
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EP4527965A4 (fr
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Mingzhuo BAI
Zigang LI
Ana YANG
Fengbin LI
Donghui WEN
Qingjun Zhou
Fengming SONG
Xiaoping Hu
Haiting Liu
Sheng Liu
Hua Zhang
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving particular fabrication steps or treatments of ingots or slabs
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to the technical field of the production of low alloy steel, in particular to a high-strength and high-plasticity hot-rolled strip steel with high weather resistance and manufacturing method therefor.
  • Atmospheric corrosion-resistant steel is widely used in the production of outdoor steel structures with atmospheric corrosion-resistance requirements such as containers, railway vehicles, bridges, etc.
  • atmospheric corrosion-resistant steel With the increasing demand for green, low-carbon and environmentally friendly materials, the application scenarios of atmospheric corrosion-resistant steel are also expanding.
  • These steel structures can be used directly naked, or the surfaces thereof can be lightly coated before use, which can achieve very high weather resistance, and thus some traditional steel surface anticorrosive processes for steel, such as pre galvanizing, pre plating with zinc aluminum magnesium coating, post galvanizing, etc., can be replaced.
  • the use of atmospheric corrosion-resistant steel can not only reduce the energy consumption and pollution caused by the metal coating process, but also improve the service life of steel structures and reduce the cost of anti-corrosion maintenance at a later stage.
  • An objective of the present invention is to provide a high-strength and high-plasticity hot-rolled strip steel with high weather resistance and manufacturing method therefor.
  • the atmospheric corrosion resistance of the material is significantly improved for the hot-rolled strip steel of the present invention, which has a corrosion rate of 30% or less of that of the ordinary structural steel Q355B, i.e., a weather resistance 3 or more times that of the steel Q355B, and its weather resistance is also one or more times higher than that of ordinary weathering steel (such as Q450NQR1 steel).
  • the hot-rolled strip steel of the present invention can replace post-galvanized anti-corrosion protection, and can be used barely for guardrails, mast towers, photovoltaics and other support structural parts without coating on the surface.
  • the present invention realizes the technical objective by optimizing the chemical composition of the hot-rolled strip steel.
  • a high Cr content of 1.5-4.5% is used to promote the formation of a uniform dense rust layer on the surface of hot-rolled strip steel during use, and Cr can be rapidly enriched in the thin rust layer.
  • the Cr concentration at the interface between the rust layer and the substrate can be 12% or more, which significantly improves the corrosion potential and electrochemical impedance, and stops the corrosion from continuing to occur, thereby obtaining super high atmospheric corrosion resistance.
  • a microstructure mainly comprising 70% or more by volume of fine ferrite can be obtained at a high Cr content, and there is a large amount of nanoscale precipitated phase of TiC with a diameter of 10 nm or less in the ferrite, so hot-rolled strip steel with high strength, high plasticity, high weather resistance and excellent formability can be obtained economically.
  • the hot-rolled strip steel of the present invention comprises the following components in mass percentage: C: 0.04-0.09%, Si ⁇ 0.50%, Mn: 0.10-1.50%, P ⁇ 0.03%, S ⁇ 0.01%, Al ⁇ 0.60%, Cr: 1.5-4.5%, Cu: 0.10-0.60%, Ti: 0.05-0.18%, Ni ⁇ 0.30%, Nb ⁇ 0.06%, N ⁇ 0.008%, and the balance being Fe and inevitable impurities, and the hot-rolled strip steel further satisfies: 2Mn+Cr ⁇ 6%, with element symbols being substituted with mass percentages of corresponding chemical elements in the hot-rolled strip steel for calculation. For example, when the content of Mn in steel is 0.10%, the numerical value 0.10% is substituted for calculation.
  • the composition of the hot-rolled strip steel satisfies Ti-3N ⁇ 0.04%, with element symbols being substituted with mass percentages of corresponding chemical elements in the hot-rolled strip steel for calculation, in which case the strengthening effect of Ti can be fully exerted.
  • the composition of the hot-rolled strip steel satisfies Si+2Ni ⁇ 0.10%, with element symbols being substituted with mass percentages of corresponding chemical elements in the hot-rolled strip steel for calculation, in which case the effect of copper brittleness can be reduced.
  • the hot-rolled strip steel of the present invention further comprises at least one selected from the following: Ca ⁇ 0.015%, Mg ⁇ 0.015%, B ⁇ 0.003%, Mo ⁇ 0.30%, V ⁇ 0.15%, and Re ⁇ 0.015%.
  • the hot-rolled strip steel of the present invention has a microstructure of polygonal ferrite + a small amount of pearlite + bainite mainly in the form of MA, and the ferrite has a grain size of grade 8 or more, preferably grade 9 or more.
  • the content of polygonal ferrite is 70-90%, and the content of pearlite is 5-30%.
  • the content of pearlite is more preferably 15% or more and 25% or less.
  • the content of bainite is 5-15%, wherein the MA structure accounts for about 20-70% of bainite, preferably 30-70%.
  • the ferrite contains a large amount of nanoscale precipitated phase of TiC with a diameter of 10 nm or less, and the content of nanoscale precipitated phase of TiC in ferrite is about 0.005%-0.03%.
  • the content of the steel microstructure in the present invention refers to the volume fraction.
  • the hot-rolled strip steel of the present invention has very high weather resistance, and the corrosion rate of the hot-rolled strip steel is 30% or less of that of the Q355B steel, that is, its weather resistance is 3 or more times that of Q355B steel and 2 or more times that of ordinary weathering steel (such as Q450NQR1 steel).
  • the corrosion rate of the hot-rolled strip steel of the invention decreases rapidly with the increase of corrosion depth, and the simulation corrosion test results show that the corrosion depth of the hot-rolled strip steel is ⁇ 0.1 mm during a simulated service cycle of 25 years.
  • C is an effective strengthening element in steel.
  • C can also form nanoscale second-phase precipitated particles with Ti, Nb and other microalloying elements to play the role of precipitation strengthening and refining the structure.
  • the C content of the present invention is ⁇ 0.04%; However, too much C will form too much carbide or bainite hard phase structure in the steel, which will not only reduce the toughness and formability of the material, but also generate a galvanic cell effect to reduce the corrosion resistance of the steel, and reduce the welding performance of the steel. Therefore, the C content is ⁇ 0.09%.
  • the content of elements in the hot-rolled strip steel of the present invention refers to the mass fraction.
  • Si is a commonly used deoxidizing element in steel and also has a solid solution strengthening effect on the steel. It can also improve the corrosion resistance of the material, and has a certain effect on reducing the copper brittleness.
  • a high content of Si will lead to scale defects on the surface of hot-rolled strip steel, seriously affect the surface quality of the strip steel, and deteriorate the welding performance of the material, resulting in the deterioration of the toughness in the welding heat affected zone. Therefore, the content of Si of the present invention is ⁇ 0.50%s, preferably 0.06% ⁇ Si ⁇ 0.50%.
  • Cr is an important element in improving the weather resistance of steel sheet.
  • the main mechanism of improving the weather-resistance of weathering resistant steel is as follows: on one hand, the corrosion potential of the substrate is increased by adding corrosion-resistant elements, to reduce the corrosion rate by increasing the electrochemical impedance.
  • Cr enables a physical barrier to the corrosive medium by promoting the formation of a dense rust layer on the surface and changing the corrosion environment at the substrate, and the corrosion gradually slows down as the corrosion depth increases.
  • the hot-rolled strip steel of the present invention will produce an effect similar to stainless steel, that is, the corrosion potential at the interface between the corrosion front rust layer and the substrate is very high, as well as the blocking effect of the low corrosive medium of the dense rust layer, which makes the electrochemical impedance of the strip surface very high, and the corrosion reaction is basically interrupted.
  • the content of Cr in the substrate should not be too high. With the increase of the content of Cr in the substrate, the corrosion potential of the substrate will increase.
  • the content of Cr in the present invention is 1.5%-4.5%, preferably 2.27%-3.68%.
  • Figure 1 shows the influence of the content of Cr in steel on the relative corrosion rate of hot-rolled strip steel in alternate immersion tests; and Figure 2 shows the effect of the content of Cr in steel on the long-period corrosion depth of hot-rolled strip steel.
  • the corrosion rate of the hot-rolled strip steel of the present invention decreases rapidly with time, for example, when the content of Cr in the steel is 2%, the estimated value of the corrosion depth may be 0.1 mm or less during a simulated cycle of 25 years. However, when the content of Cr in steel is 5%, the estimated value of corrosion depth is about 0.12 mm during a simulated cycle of 25 years, indicating a decrease in corrosion resistance.
  • Cr is also an element that increases the hardenability of steel, and a higher content of Cr can make the steel form air-cooled bainite or air-cooled martensite at a lower air-cooling rate, thus significantly improving the tensile strength of the material and reducing the yield-to-tensile ratio of the material, which is conducive to reducing the forming rebound and improving the stability of the forming size.
  • the present invention further improves the strength of steel by adopting the design of a high content of Cr, making full use of this function of Cr, and combining the strengthening effect of C, Mn and other elements.
  • Cu is also one of the important corrosion-resistant elements, and the effect is more obvious when it is added with Cr.
  • Cu can promote the formation of a dense rust layer on the steel surface. Adding 0.10% or more of Cu can significantly improve the atmospheric corrosion resistance of steel.
  • Cu is a metal with a low melting point, and the strip steel containing more Cu is prone to copper brittle mesh cracks and warping defects on the surface during the hot rolling process, which deteriorates the surface quality of the steel.
  • Cu is also an expensive element.
  • the content of Cu in the present invention is 0.10-0.60%, preferably 0.2-0.5%, more preferably 0.25-0.38%.
  • P is often added as a corrosion-resistant element in traditional atmospheric corrosion-resistant steel, which can promote the formation of a protective rust layer on the surface, so as to effectively improve the atmospheric corrosion resistance of steel.
  • P is also a harmful impurity element in steel, which tends to segregate in the center of thickness during continuous casting of slab.
  • P is easy to produce segregation at the grain boundary, reducing the grain boundary binding energy, thus reducing the toughness and plasticity of steel.
  • P is also very unfavorable to the welding performance of steel. Therefore, the present invention does not adopt atmospheric corrosion-resistant steel with a high content of P, but minimizes the content of P in the steel, requiring the content of P to be 0.03% or less.
  • S is a common harmful impurity element in steel, which has adverse effects on low temperature toughness, welding performance, cold forming performance, etc.
  • the content of S in the steel of the present invention is 0.01% or less.
  • Al is a very effective deoxidizing element, and Al is conducive to refining grain and improving the strength and toughness of the steel. At the same time, Al can also promote the formation of the ferrite, inhibit the pearlite transition, and facilitate the transition of ferrite bainite dual phase structure.
  • a high content of Al is not conducive to smooth pouring, which tends to block the water outlet, so the present invention requires that the content of Al in the steel is ⁇ 0.60%, preferably 0.011-0.56%, more preferably 0.02-0.30%.
  • Ti is a strong carbonitride forming element, which can be precipitated in the form of extremely fine TiC or Ti(C, N) as second phase particles, thus significantly improving the strength of the material, and it is a very effective strengthening element.
  • the content of Ti is 0.05% or more, it will play a strong precipitation-strengthening role.
  • the precipitation of TiC significantly reduces the free C to form larger carbides or pearlite, thereby reducing the galvanic effect of heterogeneous phases in the corrosion process, improving the ability of the material to resist intergranular corrosion, so as to improve the strength of the material, and at the same time to improve the corrosion resistance of the material.
  • the content of Ti of the present invention is 0.05-0.18%, preferably 0.072-0.160%.
  • Ni can improve the corrosion resistance of the steel and improve the surface copper brittleness caused by Cu.
  • the price of Ni is very expensive, and too much addition will greatly increase the alloy cost of the material. Therefore, the content of the Ni in the present invention is ⁇ 0.30%, preferably 0.1% or more and 0.25% or less, more preferably 0.20% or less.
  • Nb is also a strong nitrogen carbide forming element, and it can also be precipitated in the form of NbC and Nb(CN) carbide particles as second phase, resulting in precipitation strengthening.
  • the cost of Nb is much higher than Ti, so it is not economical to increase strength by adding Nb compared to Ti.
  • the content of Nb being too high will also affect the quality of the slab during the cooling process for casting of strip steel, resulting in surface cracks, angle cracks and other defects. Therefore, the content of the Nb in the present invention is ⁇ 0.06%.
  • N is an impurity element in steel.
  • N is easy to combine with Ti and precipitate to form coarse TiN inclusion during smelting.
  • TiN inclusion will damage the toughness of the steel; on the other hand, it also reduces the effective content of Ti in the steel. Therefore, the content of N in the present invention is ⁇ 0.008%.
  • the compositional design of the hot-rolled strip steel of the present invention also needs to meet: 2Mn+Cr ⁇ 6%.
  • Mn and Cr can shift the C curve of ferrite transition to the right, significantly inhibit the ferrite transition and make the transition time longer.
  • the thermal simulation and CCT calculation it is difficult for the strip steel to have sufficient ferritic transformation during laminar flow cooling and post-coiling cooling when 2Mn+Cr>6%, and sufficient ferritic transformation is very important for the properties of the steel.
  • the amount of ferrite transformation will directly affect the elongation of the steel of the present invention, that is, the plasticity of the material. Insufficient elongation makes it difficult for the material to meet the molding requirements for parts of complex cross sections.
  • the transformation of ferrite also has an important impact on the precipitation of nanoscale phase of TiC.
  • the diffusion coefficient of Ti in the ⁇ -ferrite phase is high, while the solubility of C in the ⁇ -ferrite phase is very low, so with the occurrence of ⁇ phase ⁇ ⁇ phase transition, TiC can be precipitated rapidly in the form of interphase precipitation or dispersion precipitation, forming a nanoscale precipitated phase, thus significantly improving the strength.
  • the ferritic phase does not undergo transformation, TiC is difficult to precipitate quickly; as the temperature decreases, a large number of structures are transformed into bainite, and the free C element in the steel will be precipitated in the form of carbide, which will no longer have a chance to combine with Ti to form TiC, and cannot produce enough strengthening effect. Therefore, the full transformation of ferrite has an important effect on the strength and plasticity of the steel. Therefore, in the present invention, it is required to satisfy 2Mn+Cr ⁇ 6%, with element symbols being substituted with mass percentages of corresponding chemical elements in the hot-rolled strip steel for calculation. Preferably, 3% ⁇ 2Mn+Cr ⁇ 5%.
  • the composition of the hot-rolled strip steel of the present invention satisfies Ti-3N ⁇ 0.04%, with element symbols being substituted with mass percentages of corresponding chemical elements in the hot-rolled strip steel for calculation. If N in the steel preferentially combines with Ti to form TiN inclusion, the contribution of Ti to the strength of the steel will be weakened.
  • Ti-3N is defined as the effective content of Ti. When Ti-3N ⁇ 0.04%, it can be ensured that there is sufficient Ti to combine with C to form TiC precipitated particles for precipitation strengthening.
  • the composition of the hot-rolled strip steel of the present invention satisfies Si+2Ni ⁇ 0.10%, with element symbols being substituted with mass percentages of corresponding chemical elements in the hot-rolled strip steel for calculation.
  • Cu is easy to form copper brittleness defects on the surface of strip steel, while Si and Ni have the effect of improving copper brittleness defects, and they can complement each other. Compared with Si, Ni has a better effect on copper brittleness improvement, but the cost is also higher.
  • the hot-rolled strip steel of the present invention can contain one or two elements of Si and Ni.
  • Si ⁇ 0.50%, Ni ⁇ 0.30% and Si+2Ni ⁇ 0.10% in the steel the balance among material design economy, material surface quality and copper brittleness can be adjusted by taking advantage of the complementary relationship between the two elements, which makes the problem of copper brittleness can be controlled economically.
  • Si+2Ni ⁇ 0.30% the Si+2Ni ⁇ 0.30%.
  • Another aspect of the present invention provides a method for manufacturing the above hot-rolled strip steel, comprising the following steps:
  • the temperature at the outlet of rough rolling is 1040 to 1080 °C.
  • the final rolling temperature is 860 to 880 °C; if the thickness of the finished hot-rolled strip steel is 3 to 5 mm, the final rolling temperature is 840 to 860 °C; and if the thickness of the finished hot-rolled strip steel is 5 mm or more, the final rolling temperature is 820 to 840 °C.
  • the hot-rolled strip steel of the present invention In the method for manufacturing the hot-rolled strip steel of the present invention: For Cu-containing steel, low temperature heating is usually used to avoid copper embrittlement. However, for Ti-containing steel, high temperature heating is usually required to fully dissolve Ti in solid solution and provide conditions for the precipitation strengthening of TiC. Due to the hot-rolled strip steel of the present invention containing both Cu and Ti, there is a contradiction in the heating system.
  • the manufacturing process of the present invention optimizes the heating curve of the slab during the heating process.
  • the surface temperature of the slab can quickly cross the sensitive temperature range of 1050-1150 °C for producing copper brittleness, and the heating time is controlled within 15 minutes, so that the molten Cu can be absorbed by the newly formed oxide skin on the surface of the substrate, and it can avoid the Cu penetration into the slab substrate, thus it can inhibit the generation of copper brittleness.
  • the temperature is kept at 1230 to 1290 °C, and the soaking time is controlled to 30 to 90 min to ensure sufficient solid solution of Ti.
  • the tapping temperature is also controlled to 1230 to 1290 °C.
  • the slab is taken out of the heating furnace and sized, rough rolling is carried out.
  • the rough rolling stage should ensure a high enough descaling pressure to obtain a good descaling effect. It is demonstrated by practical production that high pressure water of 15 MPa or more, preferably 20 MPa or more, has a better crushing and removal effect on the dense primary oxide skin on the surface of the slab with a high Cr content. The removal of oxide skin has a significant improvement effect on reducing the copper embrittlement caused by surface Cu enrichment. Therefore, in the manufacturing process of the present invention, the high-pressure water used for descaling is required to be 15 MPa or more.
  • the temperature at the roughing rolling outlet should be 1080 °C or less, preferably 1040 to 1080 °C.
  • the strip steel is subjected to finish rolling, which adopts a process of multi-stand continuous rolling.
  • the final rolling temperature is controlled to 820 to 880 °C.
  • the steel of the present invention needs to adopt a lower final rolling temperature, for example, when the thickness of the finished hot-rolled strip steel is 3 mm or less, the final rolling temperature is 860 to 880 °C; when the thickness of the finished hot rolled strip is 3 to 5 mm , the final rolling temperature is 840 to 860 °C; and when the thickness of the finished hot rolled strip is 5 mm or more, the final rolling temperature is 820 to 840 °C.
  • the hot-rolled strip steel of the present invention has a structure mainly composed of polygonal ferrite, in which the ferrite has a grain size of grade 8 or more or even up to grade 11.
  • the polygonal ferrite content in the microstructure of hot-rolled strip steel is 70-90%, and a large amount of precipitated phase of TiC with a diameter of 10 nm or less is dispersed in the ferrite, which has a significant contribution to the high strength of the material.
  • Figure 5 shows the dark field morphology observed by transmission electron microscopy (TEM) of the hot-rolled strip steel of Example 2.
  • TEM transmission electron microscopy

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EP23823231.8A 2022-06-15 2023-06-15 Acier en bande laminé à chaud à haute résistance et haute plasticité à résistance élevée aux intempéries et son procédé de fabrication Pending EP4527965A4 (fr)

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