WO2019242565A1 - 980MPa以上冷轧或镀锌双相钢板的制造方法 - Google Patents

980MPa以上冷轧或镀锌双相钢板的制造方法 Download PDF

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WO2019242565A1
WO2019242565A1 PCT/CN2019/091202 CN2019091202W WO2019242565A1 WO 2019242565 A1 WO2019242565 A1 WO 2019242565A1 CN 2019091202 W CN2019091202 W CN 2019091202W WO 2019242565 A1 WO2019242565 A1 WO 2019242565A1
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rolled
cold
steel plate
temperature
heat
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French (fr)
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薛鹏
王利
朱晓东
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to US17/252,031 priority Critical patent/US12084751B2/en
Priority to JP2020570147A priority patent/JP7159356B2/ja
Publication of WO2019242565A1 publication Critical patent/WO2019242565A1/zh
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    • 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
    • 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
    • C21D8/0226—Hot rolling
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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
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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
    • C21D8/0247—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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/68—Furnace coilers; Hot coilers
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • 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
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    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/003—Apparatus
    • C23C2/0038—Apparatus characterised by the pre-treatment chambers located immediately upstream of the bath or occurring locally before the dipping process
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/14—Removing excess of molten coatings; Controlling or regulating the coating thickness
    • C23C2/16—Removing excess of molten coatings; Controlling or regulating the coating thickness using fluids under pressure, e.g. air knives
    • C23C2/18—Removing excess of molten coatings from elongated material
    • C23C2/20—Strips; Plates
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the present invention relates to a method for manufacturing an ultra-high-strength steel sheet, and in particular, to a method for manufacturing a cold-rolled or galvanized dual-phase steel sheet with a 980 MPa or more.
  • Cold-rolled or galvanized dual-phase ultra-high-strength steel (more than 980 MPa) mainly based on phase transformation strengthening. Due to the high alloy element content and strong hardenability, the material structure and performance of the hot rolling process after intermediate hot rolling process varies with temperature. The differences are extremely sensitive. Traditionally, the hot-rolling process only accurately controls the temperature before coiling, such as the tapping temperature, the final rolling temperature, and the coiling temperature. There is no fine control on the temperature change after coiling.
  • the uneven cooling rate, structure and performance of different parts during the coil cooling process will have a significant adverse effect on the cold rolling manufacturability of ultra-high strength steel hot coils.
  • the different cooling processes of different parts during the stack cooling process are caused by The root cause of such adverse effects.
  • the purpose of the present invention is to provide a method for manufacturing a cold-rolled or galvanized duplex steel plate of more than 980 MPa, which can solve the edge cracks after cold rolling and the thickness after cold rolling through the design of a heat source with or without a heat source after hot rolling. Manufacturing problems such as sharp fluctuations, and good cold rolling manufacturability.
  • the present invention provides a method for manufacturing a cold-rolled dual-phase steel plate above 980 MPa, in which the slab is directly cold-rolled after hot rolling, coiling, bundling, online insulation, and continuous annealing to obtain cold Duplex steel plates are rolled; the coiling temperature is controlled above 450 ° C; the on-line insulation means that each hot-rolled coil is covered with an independent, closed insulation cover and transferred to cold rolling within 30 minutes; The thermal insulation temperature of the coil in the thermal insulation cover is above 450 ° C, and the thermal insulation time is less than 20 hours.
  • the invention also provides a method for eliminating hot-rolled steel sheet edge cracks after cold rolling and reducing thickness fluctuations after cold rolling.
  • the method includes covering an independent, sealed heat insulation cover within 30 minutes after unrolling a hot rolled coil, and transferring it to cold.
  • the coiling temperature is controlled from 450 ° C to a bainite transformation temperature.
  • each hot rolled coil is covered with an independent and closed heat insulation cover within 10 minutes after uncoiling.
  • a heating device is used to heat and keep the heat in the heat-retaining cover.
  • an electric heating device and a temperature sensor are arranged in the heat insulation cover.
  • the heat insulation cover has a composite structure
  • the outer protection layer is a high-strength steel plate
  • the middle layer is a heat insulation material
  • the inner layer is a high temperature resistant stainless steel plate.
  • the thermal insulation cover is a composite structure, which includes an internal radiation layer, an electric heating wire layer, an intermediate mesh cover, an intermediate thermal insulation layer, and an external protective layer in order from the inside to the outside.
  • a temperature sensor is respectively provided on the surface and the end surface of the steel coil in the heat insulation cover.
  • the method further includes the step of performing galvanizing after continuous annealing to obtain a galvanized duplex steel sheet.
  • Figures 1 to 3 show the change trend of the mechanical properties of the three steel types DP-1, DP-2, and DP-3 after 500 ° C, 550 ° C, and 600 ° C heat preservation for different times.
  • Figure 4 shows the effect of decomposition softening and precipitation strengthening during the heat preservation process.
  • Figure 5 is the observation of DP-1 for 8h-precipitates.
  • Figure 6 is the observation of DP-2 for 8h-precipitate.
  • Figure 7 shows the observation of DP-3 for 8h-precipitates.
  • FIG. 8 is a schematic structural diagram of a thermal insulation device according to an embodiment of the present invention.
  • FIG. 9 is a cross-sectional view of a side wall of a heat insulation cover according to an embodiment of the present invention.
  • the invention aims to solve manufacturing problems such as edge cracks after cold rolling, sharp fluctuations in thickness after cold rolling, and the like by using a heat source with or without heat source heat preservation process after hot rolling coiling, and obtain good cold rolling manufacturability.
  • the present invention controls the coiling temperature to be above 450 ° C, and controls the thermal insulation temperature of the hot-rolled coil in the insulation cover to be above 450 ° C, and the thermal insulation time is within 20 hours, such as the thermal insulation time is 1-20 hours.
  • the slab is directly sent to cold rolling + continuous annealing or cold rolling + continuous annealing + galvanizing after hot rolling, coiling, bundling, and on-line insulation to obtain cold rolling or galvanizing.
  • Phase steel where the coiling temperature is controlled above 450 ° C; the online insulation means that each hot rolled coil is covered with an independent, closed insulation cover and transferred to cold rolling within 30 minutes after uncoiling;
  • the heat preservation temperature in the hood is above 450 ° C, and the heat preservation time is less than 20 hours.
  • the method of the invention is particularly suitable for manufacturing cold-rolled dual-phase steel plates with a tensile strength ⁇ 980 MPa.
  • the composition of cold-rolled duplex steel plates with tensile strength ⁇ 980 MPa is not particularly limited, in some embodiments, such steel plates usually contain 0.05-0.2% C, preferably 0.08-0.17%, in terms of weight percentage; 0.1 -1.0% Si, preferably 0.2-0.9%; 1.8-3.0% Mn, preferably 2.1-2.7%; 0.01-0.06% Al, preferably 0.01-0.04%; 0.01-0.08% Ti, preferably 0.01-0.05% ; The rest are Fe and inevitable impurities.
  • any one or more of B, Cr, Mo, and Nb may be contained in such steel plates.
  • the content of B may be 0.0005-0.004%, preferably 0.001-0.003%; the content of Cr may be 0.10-0.80%, preferably 0.20-0.60%; the content of Mo may be 0.05-0.40%, preferably 0.15 -0.30%; the content of Nb may be 0.01-0.06%, preferably 0.02-0.05%.
  • this type of steel sheet contains at least any two of B, Cr, Mo, and Nb.
  • the design of the holding temperature needs to refer to the CCT curve of the component system, that is, the temperature and time at which each phase change starts to occur.
  • the CCT curve of the component system that is, the temperature and time at which each phase change starts to occur.
  • the initial matrix structure of the entire roll will be different, that is, the part quickly cooled below 400 ° C, the structure is bainite + martensite Body; the place where the center is kept above 530 °C for a long time, and the structure is pearlite and ferrite.
  • the tissue difference of the matrix is difficult to completely eliminate through thermal insulation, and the difference in mechanical properties will always be inherited.
  • a coiling temperature and a holding temperature below 530 ° C need to be designed to eliminate the difference in the initial matrix structure of the entire coil and make it completely bainite + martensite.
  • the coiling temperature is set to be equal to or lower than the bainite transformation temperature. Too low coiling temperature will further increase the strength of the matrix structure, resulting in longer holding time required for subsequent softening. Therefore, in the present invention, the winding temperature is controlled to be 450 ° C or higher.
  • the holding temperature is set between the coiling temperature and the bainite transformation temperature.
  • the holding time can be obtained according to laboratory tests of cold-rolled ultra-high-strength dual-phase steel with different composition systems.
  • cold-rolled dual-phase steels of different composition systems can be used to conduct laboratory thermal insulation experiments of hot-rolled steel plates to test the changes in mechanical properties of experimental specimens after thermal insulation.
  • the length of time for holding the heat should be sufficient to make the maximum tensile strength of the steel coil below 1000 MPa after the end of the heat holding.
  • Table 1 Composition of three cold-rolled ultra-high-strength dual-phase steels
  • the DP-1, DP-2, and DP-3 steel grades are kept at 500 ° C, 550 ° C, and 600 ° C for different times, and the changes in mechanical properties are shown in Figures 1-3.
  • the hard phases in the DP-1, DP-2, and DP-3 tissues all decomposed during the heat preservation process, and the strength of the tissues decreased.
  • the addition and proportion of alloying elements will also cause a difference in the tempering resistance of the structure, so the same structure will have different softening effects at the same holding temperature and time.
  • the strength of DP-3 is higher than that of DP-1 and DP-2 under the same conditions.
  • the purpose of covering the heat insulation cover is to prevent heat from being radiated outward, and use the heat inside the steel coil to increase the temperature of the surface of the steel coil to make the overall temperature of the steel coil uniform, thereby achieving the purpose of heat treating the steel coil.
  • the present invention can be implemented using heat shield devices known in the art.
  • An exemplary heat shield device is shown in Figs. 8 and 9 and includes:
  • the steel coil supporting bracket 2 is disposed on the steel coil tray 1;
  • the heat insulation cover 3 is arranged outside the steel coil support bracket 2 and has an internal cavity volume greater than the volume of at least one steel coil 100+ steel coil support bracket 2.
  • the lower end of the heat insulation cover 3 is movably connected to the steel coil tray 1 .
  • the heat shield device may further include:
  • An electric heating device 4 is disposed on an inner wall of the heat insulation cover 3;
  • a temperature sensor 5 provided in the heat insulation cover 3;
  • the electric heating device 4 and the temperature sensor 5 are electrically connected to the information acquisition control module 6.
  • the electric heating device 4 may be an electric heating wire.
  • the temperature sensor 5 may be a thermocouple.
  • the heat insulation cover used in the present invention can not only realize the use of the remaining temperature of the hot-rolled steel coil to realize slow cooling, but also perform secondary heating treatment on some special steel materials, and achieve secondary tempering to improve the coil performance and refine the grain. .
  • temperature sensors are respectively provided on the surface and the end surface of the steel coil 100 in the heat insulation cover 3.
  • the heat insulation cover 3 of the present invention is a composite structure, which includes an internal radiation layer 31, an electric heating wire layer 32, an intermediate mesh cover 33, an intermediate insulation layer 34, and an outer protective layer 35 in order from the inside to the outside;
  • the composite structure of the cover 3 is fixed with anchor nails 36.
  • the heating device is put into use needs to be judged according to the temperature and time of the insulation. For example, if the insulation temperature is required to be higher than 550 ° C without a heat source for a long time, the temperature inside the insulation cover increases with the insulation, which is not conducive to the uniformity of the strength of the coil. Therefore, when the heat preservation temperature of the hot rolled coil in the heat insulation cover is required to be above 550 ° C, a heating device should be used to heat and keep the inside of the heat insulation cover.
  • the hot-rolled coil covered with the heat insulation cover can be transferred to the cold rolling through a coil transportation chain or a moving trolley.
  • the steel coil is heated after being rolled into a heat insulation cover to prevent heat from being radiated outward.
  • the heat inside the steel coil is used to increase the temperature of the surface of the steel coil and make the overall temperature of the steel coil uniform.
  • the roll is heat treated for the purpose.
  • the insulation temperature is reasonably designed to ensure that there is little difference in the initial matrix structure of the entire coil.
  • controlling the tensile strength of hot-rolled steel coils to be less than 1000 MPa is conducive to ensuring the manufacturability of cold rolling and avoiding defects such as edge cracks after cold rolling and sharp fluctuations in thickness after cold rolling.
  • the present invention obtains a cold-rolled or galvanized dual-phase steel sheet with a high cold-rolled manufacturable tensile strength of greater than 980 MPa through a reasonable design of the holding temperature and holding time.
  • the tensile strength is less than 1000 MPa; it has good manufacturability for cold rolling, and can avoid defects such as edge cracking after cold rolling and sharp fluctuations in thickness after cold rolling.
  • Examples and comparative examples of cold-rolled dual-phase steel plates above 980 MPa were prepared according to the ingredients in Table 3. The slabs were hot-rolled, coiled, bundled, and then directly cold-rolled + continuous annealed after online insulation to obtain cold-rolled dual-phase steel plates.
  • the winding temperature is shown in Table 4.
  • Each hot-rolled coil is covered with an independent, sealed thermal insulation cover within 30 minutes after uncoiling, and the hot-rolled coil covered with the thermal insulation cover is transferred to cold rolling through a steel coil transport chain or a moving cart.
  • the thermal insulation temperature and thermal insulation time of the hot rolled coil in the thermal insulation cover are shown in Table 4.
  • a heating device is used to heat and keep the heat in the heat insulation cover.
  • Table 3 Compositions of the examples and comparative examples (unit: weight percent)
  • Example 1 0.088 0.30 2.25 0.02 Zh 0.55 0.22 Zh 0.02
  • Example 2 0.120 0.25 2.50 0.03 0.0025 0.60 Zh 0.025 0.025
  • Example 3 0.085 0.45 2.20 0.03 0.0020 Zh 0.20 0.040 0.05
  • Example 4 0.088 0.30 2.25 0.02 Zh 0.55 0.22 Zh 0.02
  • Example 5 0.120 0.25 2.50 0.03 0.0025 0.60 Zh 0.025 0.025
  • Example 6 0.085 0.45 2.20 0.03 0.0020 Zh 0.20 0.040 0.05 Comparative Example 7 0.088 0.30 2.25 0.02 Zh 0.55 0.22 Zh 0.02
  • Example 1 no 20 ⁇ m 1034
  • Example 2 no 25 ⁇ m 1234
  • Example 3 no 18 ⁇ m 1021
  • Example 4 no 19 ⁇ m 998
  • Example 5 no 21 ⁇ m 1254
  • Example 6 no 15 ⁇ m 1003 Comparative Example 7 no 70 ⁇ m 1002 Comparative Example 8 Yes 70 ⁇ m 1198 Comparative Example 9 no 90 ⁇ m 997
  • Controlling the tensile strength of the hot-rolled steel coil is less than 1000 MPa, which is beneficial to ensure the cold-rolling manufacturability and avoid defects such as edge cracks after cold-rolling and sharp fluctuations in thickness after cold-rolling, as in Examples 3 and 6.
  • Comparative Example 9 did not guarantee that the total tensile strength was reduced uniformly to less than 1000 MPa, and the thickness fluctuated severely after cold rolling.

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Abstract

本发明提供980MPa以上冷轧或镀锌双相钢板的制造方法，板坯经热轧、卷取、打捆、在线保温后直送冷轧+连续退火或冷轧+连续退火+镀锌，获得冷轧或镀锌双相钢板；其中，卷取温度控制在450℃以上；所述在线保温是指每个热轧卷卸卷后30分钟内盖上独立、密闭的保温罩，通过钢卷运输链或移动小车将盖上保温罩的热轧卷移送至冷轧；热轧卷在保温罩内的保温温度在450℃以上，保温时间小于20小时。本发明通过热轧卷取后带热源或不带热源保温工艺的设计，解决冷轧轧后边裂、冷轧轧后厚度剧烈波动等制造问题，获得良好的冷轧可制造性。

Description

980MPa以上冷轧或镀锌双相钢板的制造方法 技术领域
本发明涉及超高强钢板的制造方法，特别涉及一种980MPa以上冷轧或镀锌双相钢板的制造方法。
背景问题
以相变强化为主的冷轧或镀锌双相超高强钢(980MPa以上)由于合金元素含量高、淬透性强，中间热轧工序后材料组织性能对热轧卷取后的温度变化过程差异极为敏感。热轧过程传统上只精确控制卷取前的温度，例如出炉温度、终轧温度、卷取温度，对卷取后的温度变化无精细控制。
钢卷冷却过程中产生的不同部位冷速-组织-性能不均匀会对超高强钢热卷的冷轧可制造性产生显著不良影响，钢卷在堆放冷却过程中不同部位的不同冷却历程是造成此类不良影响的根本原因。
以一种980MPa以上冷轧超高强双相钢为例：其热轧卷取后，贝氏体区域较宽，马氏体临界冷速高，卷取后高冷速区域进入贝氏体甚至马氏体相变区；其他低冷速区域组织以珠光体为主，导致卷取后组织和强度不均，并由此带来冷轧后厚度剧烈波动、冷轧后边裂等生产问题。
发明内容
本发明的目的在于提供一种980MPa以上冷轧或镀锌双相钢板的制造方法，通过热轧卷取后带热源或不带热源保温工艺的设计解决冷轧轧后边裂、冷轧轧后厚度剧烈波动等制造问题，获得良好的冷轧可制造性。
为达到所示目的，本发明提供一种980MPa以上冷轧双相钢板的制造方法，其中，板坯经热轧、卷取、打捆、在线保温后直送冷轧，并进行连续退火，获得冷轧双相钢板；其中，卷取温度控制在450℃以上；所述在线保温是指每个热轧卷卸卷后30分钟内盖上独立、密闭的保温罩，移送至冷轧；其中，热轧卷在保温罩内的 保温温度在450℃以上，保温时间小于20小时。
本发明还提供一种消除热轧钢板冷轧轧后边裂并减少冷轧轧后厚度波动的方法，该方法包括热轧卷卸卷后30分钟内盖上独立、密闭的保温罩，移送去冷轧的步骤；其中，热轧卷在保温罩内的保温温度在卷取温度到贝氏体相变温度。
优选的，所述卷取温度控制在450℃到贝氏体相变温度。
优选的，所述每个热轧卷卸卷后10分钟内盖上独立、密闭的保温罩。
优选的，当热轧卷在保温罩内的保温温度要求在550℃以上时，采用加热装置对保温罩内加热保温。
进一步，所述保温罩内设电加热装置及温度传感器。
优选的，所述保温罩为复合结构，外保护层为高强钢板，中间层为保温材料，内层为耐高温不锈钢板。
优选的，所述保温罩为复合结构，其自内向外依次包括内部辐射层、电加热丝层、中间网罩、中间保温层、外保护层。
优选的，所述保温罩内对应钢卷的表面和端面分别设置温度传感器。
进一步，所述方法还包括连续退火后进行镀锌，从而获得镀锌双相钢板的步骤。
附图说明
图1～图3为DP-1、DP-2、DP-3三种钢种在500℃、550℃和600℃保温不同时间后机械性能变化趋势图。
图4为保温过程分解软化和析出强化效果示意。
图5为DP-1保温8h-析出物观察。
图6为DP-2保温8h-析出物观察。
图7为DP-3保温8h-析出物观察。
图8为本发明实施例保温装置的结构示意图。
图9为本发明实施例保温罩的侧壁剖视图。
具体实施方式
本发明旨在通过热轧卷取后的带热源或不带热源保温工艺解决冷轧轧后边裂、冷轧轧后厚度剧烈波动等制造问题，获得良好的冷轧可制造性。为此，本发明控制 卷取温度在450℃以上，且控制热轧卷在保温罩内的保温温度在450℃以上，保温时间在20小时以内，如保温时间为1-20小时。在一些实施方案中，本发明制造方法中，板坯经热轧、卷取、打捆、在线保温后直送冷轧+连续退火或冷轧+连续退火+镀锌，获得冷轧或镀锌双相钢板；其中，卷取温度控制在450℃以上；所述在线保温是指每个热轧卷卸卷后30分钟内盖上独立、密闭的保温罩，移送至冷轧；热轧卷在保温罩内的保温温度在450℃以上，保温时间小于20小时。
本发明方法特别适合用于制造抗拉强度≥980MPa的冷轧双相钢板。虽然对抗拉强度≥980MPa的冷轧双相钢板的组成并无特殊限制，但在一些实施方案中，以重量百分比计，这类钢板通常含有0.05-0.2％的C，优选0.08-0.17％；0.1-1.0％的Si，优选0.2-0.9％；1.8-3.0％的Mn，优选2.1-2.7％；0.01-0.06％的Al，优选0.01-0.04％；0.01-0.08％的Ti，优选0.01-0.05％；其余为Fe和不可避免的杂质。任选地，这类钢板中还可含有B、Cr、Mo和Nb中的任意一种或任意多种。当含有时，B的含量可为0.0005-0.004％，优选为0.001-0.003％；Cr的含量可为0.10-0.80％，优选为0.20-0.60％；Mo的含量可为0.05-0.40％，优选0.15-0.30％；Nb的含量可为0.01-0.06％，优选0.02-0.05％。在一些实施方案中，该类钢板至少含有B、Cr、Mo和Nb中任意两种。
本发明中，保温温度的设计需要参考该成分体系的CCT曲线，即参考各相变开始发生的温度和时间。以主要成分为C 0.12％，Si 0.25％，Mn 2.5％，Cr 0.6％，B 0.0025％，Al 0.03％，Nb 0.025％和Ti 0.025％的980MPa以上冷轧超高强双相钢为例，从其CCT曲线可以看出，该成分体系热轧后在不同冷却速度下冷却，分别会进入软相区(铁素体相区、珠光体相区)和硬相区(贝氏体相区、马氏体相区)。若在该双相钢的贝氏体相变温度(530℃)以上卷取及保温，整卷初始基体组织会有差别，即快速冷却到400℃以下的部分，组织为贝氏体+马氏体；中心在530℃以上长时间保持的部位，组织则为珠光体和铁素体。而基体的组织区别很难通过保温完全消除，机械性能的差异将一直遗传。
所以，对于该冷轧超高强双相钢，需要设计530℃以下的卷取温度和保温温度，以消除整卷初始基体组织差异，使其完全为贝氏体+马氏体。
因此，本发明中，卷取温度设为贝氏体相变温度以下。而太低的卷取温度将会使基体组织强度进一步提高，导致后续软化需要的保温时间变长。因此，本发明中， 将卷取温度控制为450℃以上。保温温度则设为卷取温度到贝氏体相变温度之间。
本发明中，保温时间可根据不同成分体系的冷轧超高强双相钢实验室试验获得。例如，可对不同成分体系的冷轧双相钢种进行热轧钢板的实验室保温实验，测试保温后实验样板的力学性能变化。通常，在选定的保温温度下，保温的时间长度应足以使得保温结束后钢卷的最大抗拉强度低于1000MPa。
本发明以DP-1、DP-2、DP-3三种钢种为例进行说明。三钢种成分体系如表1所示。
表1：三种冷轧超高强双相钢成分
钢种 C Si Mn Cr B Al Mo Nb Ti
DP-1 0.088 0.30 2.25 0.55   0.02 0.22   0.020
DP-2 0.120 0.25 2.50 0.60 0.0025 0.03   0.025 0.025
DP-3 0.085 0.45 2.20   0.0020 0.03 0.20 0.040 0.050
DP-1、DP-2、DP-3三种钢种分别在500℃、550℃和600℃保温不同时间，机械性能变化趋势如图1～图3所示。
保温效果区别的原因归结如下：保温时基体组织发生硬相(马氏体、贝氏体)分解软化和Nb、Ti的C、N化物析出强化的竞争。不同合金成分体系在同样的保温条件下，呈现不同的分解软化和析出强化效果，两种机制的组合结果决定了钢种的保温效果。如图4所示。
DP-1、DP-2、DP-3组织中的硬相均在保温过程中分解，组织强度均存在降低趋势。另外，合金元素的添加和配比也会使组织存在抗回火性的差异，所以同样的组织，在同样的保温温度和时间下，软化效果不同。
另一方面，由于成分中的合金元素添加，回火过程中Nb、Ti的C、N化物析出，而Nb、Ti、Mo、Cr的添加量与配比会影响Nb、Ti的C、N化物尺寸，造成强化效果的差异。
DP-1、DP-2、DP-3在550℃保温8h扫描照片如图5-7所示。从20000倍的扫 描照片看，DP-3组织中Nb、Ti的C、N化物尺寸极其细小，达到纳米级，这会产生远大于DP-1、DP-2的强化效果。
综上所述，硬相分解软化和析出强化的叠加作用下，DP-3在同样条件下保温回火后的强度高于DP-1、DP-2。
所以，依据实验室结果，三种钢种的合理保温时间(在合理设计的保温温度之下)如下表2：
表2
钢种 保温工艺
DP-1 500℃，5h保温
DP-2 500℃，5h保温
DP-3 600℃，10h保温
本发明中，加盖保温罩的目的是阻止热量向外散发，利用钢卷内部的热量来提高钢卷表面的温度，使钢卷整体温度均匀，从而达到对钢卷进行热处理的目的。可使用本领域周知的保温罩装置来实施本发明。示例性的保温罩装置如图8和图9所示，包括：
钢卷托盘1；
钢卷承托支架2，设置于所述钢卷托盘1上；
保温罩3，罩设于所述钢卷承托支架2外，其内腔体积大于至少一个钢卷100+钢卷承托支架2的体积，保温罩3下端活动连接于所述钢卷托盘1。
保温罩装置还可包括：
电加热装置4，设置于所述保温罩3内侧壁；
温度传感器5，设置于所述保温罩3内；和
信息采集控制模块6；
所述电加热装置4和温度传感器5电性连接于该信息采集控制模块6。
电加热装置4可以是电加热丝。温度传感器5可以是热电偶。优选地，本发明使用的保温罩不但能实现对热轧钢卷余温的利用实现缓冷，同时对于某些特殊钢材能够进行二次加热处理，实现二次回火改善钢卷性能细化晶粒。
优选的，保温罩3内对应钢卷100的表面和端面分别设置温度传感器。
参见图9，本发明所述保温罩3为复合结构，其自内向外依次包括内部辐射层31、电加热丝层32、中间网罩33、中间保温层34、外保护层35；所述保温罩3复合结构采用锚固钉36固定。
是否投入加热装置需要根据保温温度和时间需要具体判断，如要求保温温度高于550℃而长时间无热源加热保温，保温罩内温度随保温进行不均匀度提高，不利于钢卷强度均匀性。因此，当热轧卷在保温罩内的保温温度要求在550℃以上时，应采用加热装置对保温罩内进行加热保温。
通常，可通过钢卷运输链或移动小车将盖上保温罩的热轧卷移送至冷轧。
本发明方法中，钢卷热轧后进保温罩保温，阻止热量向外散发，利用钢卷内部的热量来提高钢卷表面的温度，使钢卷整体温度均匀，从而达到环保节能便捷高效的对钢卷进行热处理的目的。
根据热轧卷取后不同冷速下的相变温度和相变时间合理设计保温温度，保证整卷初始基体组织差异小。
不同成分体系在某特定保温温度和保温时间下软化效果不同，实验室实验的性能结果将作为保温时间设计的合理依据。
根据实验室保温实验结果，控制热轧钢卷抗拉强度小于1000MPa，有利于保证冷轧可制造性，避免冷轧轧后边裂及冷轧轧后厚度剧烈波动等缺陷。
相较于现有技术，本发明通过保温温度和保温时间的合理设计，获得高冷轧可制造性的抗拉强度大于980MPa的冷轧或镀锌双相钢板，其中间工序热轧卷保温后抗拉强度小于1000MPa；具有良好的冷轧可制造性，可以避免冷轧轧后边裂及冷轧轧后厚度剧烈波动等缺陷。
具体实施方式
按表3成分制备实施例和对比例980MPa级以上冷轧双相钢板，板坯经热轧、卷取、打捆、在线保温后直送冷轧+连续退火，获得冷轧双相钢板。
卷取温度如表4所示。每个热轧卷卸卷后30分钟内盖上独立、密闭的保温罩，通过钢卷运输链或移动小车将盖上保温罩的热轧卷移送至冷轧。热轧卷在保温罩内的保温温度和保温时间如表4所示。当热轧卷在保温罩内的保温温度要求在550℃以上时，采用加热装置对保温罩内加热保温。 表3：实施例与比较例成分(单位：重量百分比)
序号 C Si Mn Al B Cr Mo Nb Ti
实施例1 0.088 0.30 2.25 0.02   0.55 0.22   0.02
实施例2 0.120 0.25 2.50 0.03 0.0025 0.60   0.025 0.025
实施例3 0.085 0.45 2.20 0.03 0.0020   0.20 0.040 0.05
实施例4 0.088 0.30 2.25 0.02   0.55 0.22   0.02
实施例5 0.120 0.25 2.50 0.03 0.0025 0.60   0.025 0.025
实施例6 0.085 0.45 2.20 0.03 0.0020   0.20 0.040 0.05
比较例7 0.088 0.30 2.25 0.02   0.55 0.22   0.02
比较例8 0.120 0.25 2.50 0.03 0.0025 0.60   0.025 0.025
比较例9 0.085 0.45 2.20 0.03 0.0020   0.20 0.040 0.05
表4：实施例与比较例热轧后保温工艺
Figure PCTCN2019091202-appb-000001
表5：实施例与比较例冷轧可制造性指标
钢种 轧后边裂 冷轧轧后厚度波动 最终连退钢板抗拉强度(MPa)
实施例1 否 20μm 1034
实施例2 否 25μm 1234
实施例3 否 18μm 1021
实施例4 否 19μm 998
实施例5 否 21μm 1254
实施例6 否 15μm 1003
比较例7 否 70μm 1002
比较例8 是 70μm 1198
比较例9 否 90μm 997
参见表4和表5，实施例1、2、4、5合理设计保温温度，整卷初始基体组织消除差异，完全为贝氏体+马氏体，冷轧可制造性良好。比较例7、8保温温度偏高，整卷初始基体组织会有差别，快速冷却到400℃以下的部分，组织为贝氏体+马氏体；中心在550℃以上长时间保持的部位，其组织为珠光体和铁素体，冷轧可制造性变差，出现严重冷轧轧后边裂和厚度波动。控制热轧钢卷抗拉强度小于1000MPa，有利于保证冷轧可制造性，避免冷轧轧后边裂及冷轧轧后厚度剧烈波动等缺陷，如实施例3、6。比较例9不能保证抗拉强度全长均匀的降低到1000MPa以下，冷轧后厚度波动严重。

Claims (15)

  1. 一种980MPa以上冷轧双相钢板的制造方法，其特征是，板坯经热轧、卷取、打捆、在线保温后直送冷轧，然后进行连续退火，获得冷轧双相钢板；其中，卷取温度控制在450℃以上；所述在线保温是指每个热轧卷卸卷后30分钟内盖上独立、密闭的保温罩，移送至冷轧；热轧卷在保温罩内的保温温度在450℃以上，保温时间在20小时以内。
  2. 如权利要求1所述的980MPa以上冷轧双相钢板的制造方法，其特征是，所述卷取温度控制在450℃到贝氏体相变温度。
  3. 如权利要求1所述的980MPa以上冷轧双相钢板的制造方法，其特征是，所述每个热轧卷卸卷后10分钟内盖上独立、密闭的保温罩。
  4. 如权利要求1或3所述的980MPa以上冷轧双相钢板的制造方法，其特征是，当热轧卷在保温罩内的保温温度要求在550℃以上时，采用加热装置对保温罩内加热保温。
  5. 如权利要求1或3所述的980MPa以上冷轧双相钢板的制造方法，其特征是，所述保温罩内设电加热装置及温度传感器。
  6. 如权利要求4所述的980MPa以上冷轧双相钢板的制造方法，其特征是，所述保温罩内设电加热装置及温度传感器。
  7. 如权利要求1或3或4或5所述的980MPa以上冷轧双相钢板的制造方法，其特征是，所述保温罩内对应钢卷的表面和端面分别设置温度传感器。
  8. 如权利要求1或3或4或5或6所述的980MPa以上冷轧双相钢板的制造方法，其特征是，所述保温罩为复合结构，外保护层为高强钢板，中间层为保温材料，内层为耐高温不锈钢板。
  9. 如权利要求1或3或4或5或6所述的980MPa以上冷轧双相钢板的制造方法，其特征是，所述保温罩为复合结构，其自内向外依次包括内部辐射层、电加热丝层、中间网罩、中间保温层和外保护层。
  10. 如权利要求1所述的980MPa以上冷轧双相钢板的制造方法，其特征是，所述钢板含有0.05-0.2％的C，0.1-1.0％的Si，1.8-3.0％的Mn，0.01-0.06％的Al，0.01-0.08％的Ti，任选的0.0005-0.004％的B、0.10-0.80％的Cr、0.05-0.40％的Mo 和0.01-0.06％的Nb中的至少一种或至少两种，其余为Fe和不可避免的杂质。
  11. 一种980MPa以上冷轧镀锌双相钢板的制造方法，其特征是，所述方法包括采用权利要求1-10中任一项所述的方法制造得到冷轧双相钢板后进行镀锌的步骤。
  12. 一种消除热轧钢板冷轧轧后边裂并减少冷轧轧后厚度波动的方法，该方法包括热轧卷卸卷后30分钟内、优选10分钟内盖上独立、密闭的保温罩，移送去冷轧的步骤；其中，热轧卷在保温罩内的保温温度在卷取温度到该钢板的贝氏体相变温度；其中，当热轧卷在保温罩内的保温温度要求在550℃以上时，采用加热装置对保温罩内加热保温。
  13. 如权利要求12所述的方法，其特征是，卷取温度设在450℃到贝氏体相变温度之间。
  14. 如权利要求12所述的方法，其特征是，所述保温罩内设电加热装置及温度传感器；优选地，在对应钢卷的表面和端面分别设置温度传感器。
  15. 如权利要求12所述的方法，其特征是，所述保温罩为复合结构，外保护层为高强钢板，中间层为保温材料，内层为耐高温不锈钢板；优选地，所述保温罩自内向外依次包括内部辐射层、电加热丝层、中间网罩、中间保温层和外保护层。
PCT/CN2019/091202 2018-06-19 2019-06-14 980MPa以上冷轧或镀锌双相钢板的制造方法 Ceased WO2019242565A1 (zh)

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