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EP3408418B1 - Tôle d'acier haute résistance à deux phases renforcé par dispersion et à affinage de grain laminée à chaud présentant une résistance à la traction minimale de 600 mpa et son procédé - Google Patents

Tôle d'acier haute résistance à deux phases renforcé par dispersion et à affinage de grain laminée à chaud présentant une résistance à la traction minimale de 600 mpa et son procédé Download PDF

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EP3408418B1
EP3408418B1 EP17740800.2A EP17740800A EP3408418B1 EP 3408418 B1 EP3408418 B1 EP 3408418B1 EP 17740800 A EP17740800 A EP 17740800A EP 3408418 B1 EP3408418 B1 EP 3408418B1
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steel sheet
dual phase
phase steel
max
hot rolled
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EP3408418A1 (fr
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Appa Rao Chintha
Saurabh KUNDU
Prashant Pathak
Sushil Kumar GIRI
Soumendu MONIA
Subhankar Das BAKSHI
G Senthil KUMAR
Vinay V. MAHASHABDE
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Tata Steel Ltd
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Tata Steel Ltd
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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D8/0247—Modifying the physical properties 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 by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/34—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tyres; for rims
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • 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
    • 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
    • C21D2211/005—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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling

Definitions

  • the present disclosure relates to a process for producing hot rolled high strength dual phase steel.
  • the disclosure further relates to hot rolled high strength dual phase steel with > 600 MPa tensile strength and 25% total elongation.
  • European patent EP1398392A1 and US patent US8337643 disclose a method of producing a hot rolled dual phase (ferrite + martensite) steel of minimum tensile strength of 590 MPa. Though the proposed steels achieved the strength level, it contains high amount of Si (minimum 0.5 wt.% in European patent and 0.2 wt.% in US patent). Presence of Si will lead to surface scales, generally called as tiger marks.
  • European Patent EP2053139B1 discloses a method in which a hot rolled steel sheet is subjected to heat treatment after forming so as to achieve a tensile strength varying in the range of 440 to 640 MPa.
  • the heat treatment after forming which is an essential part of the disclosure, is likely to add to the processing cost and hence is not suitable for mass production.
  • European Patent EP2578714A1 discloses a method of producing hot-rolled steel sheets with a minimum tensile strength of 590 MPa with excellent bake hardenability and stretch-flangeability. According to the proposed method the steel must contain 1.7 to 2.5 wt% of Mn. When added in such large amounts, Mn tends to segregate in the central portion in the thickness direction, which not only induces cracking during press forming but also leads to Inconsistency in achieving the desired stretch-flangeability.
  • the automotive wheel is composed of a disk and a rim. While the disc is press formed, the rim is flared and then roll formed after flash butt welding. Therefore, the material needed to form the disk needs to have good deep drawability, stretch formability and stretchability, whereas the material needed to form the rim needs to have good formability after welding.
  • the wheel discs and rims are formed by their respective processes, they are assembled by means of spot welding or arc welding. Hence the materials for both rim and disc use need to have good spot weldability. From the point of view of application, the most important functional requirement for autowheels is durability, which can be increased by increasing the fatigue strength of the wheel material.
  • Hot rolled DP steels with a tensile strength of 600 MPa have become a very popular choice for wheel disc applications owing to their superior strength and formability and at the same time good stretchability (high n value) and spot weldability.
  • HR-DP 600 hot rolled DP steels with a tensile strength of 600 MPa
  • many process parameters e.g. the finish rolling temperature, cooling rate etc. are needed to be optimized and fine tuned keeping in mind the mill configuration e.g. the length of the run out table, water volume available etc. in order to obtain the desired microstructural features which in turn will decide the final mechanical properties.
  • All the existing patents and literature have considerable amount of Si to increase ferrite strength
  • Another object of the disclosure is to propose process of producing hot rolled precipitation strengthened high strength dual phase steel sheet, with lower percentage of Si.
  • Another object of the disclosure to propose hot rolled precipitation strengthened high strength dual phase steel sheet the tensile strength more than 600 MPa with lower percentage of Si.
  • Still another object of the disclosure is to propose hot rolled precipitation strengthened high strength dual phase steel sheet, with lower percentage of Si.
  • Various embodiments of the disclosure provide a process for producing dual phase steel sheet, comprising steps of making a liquid steel having chemical composition in wt% of C: 0.03 - 0.12, Mn: 0.8 - 1.5, Si: ⁇ 0.1, Cr: 0.3 - 0.7 ,S- 0.008 max, P - 0.025 max, Al- 0.01 to 0.1, N- 0.007 max, Nb: 0.005 - 0.035, and V- 0.06 max; continuous casting the liquid steel into a slab; hot rolling the slab into a hot rolled sheet at finish rolling temperature (FRT) 840 ⁇ 30 deg.
  • FRT finish rolling temperature
  • a dual phase steel sheet comprising a chemical composition in wt% C: 0.03 - 0.12 , Mn: 0.8 - 1.5, Si: ⁇ 0.1, Cr: 0.3 - 0.7, S- 0.008 max, P - 0.025 max, Al- 0.01 to 0.1, N- 0.007 max, Nb: 0.005 - 0.035, and V- 0.06 max.
  • FIG. 1 Shown in FIG. 1 is a process (100) for producing dual phase steel sheet
  • Step (104) a liquid steel is made. Following is the composition of the liquid steel (in wt.%) C: 0.03 - 0.12, Mn: 0.8 - 1.5, Si: ⁇ 0.1, Cr: 0.3 - 0.7 ,S- 0.008 max, P- 0.025 max, Al- 0.01 to 0.1, N- 0.007 max, Nb: 0.005 - 0.035, and V-0.06 max.
  • the liquid steel in wt.% C: 0.03 - 0.12, Mn: 0.8 - 1.5, Si: ⁇ 0.1, Cr: 0.3 - 0.7 ,S- 0.008 max, P- 0.025 max, Al- 0.01 to 0.1, N- 0.007 max, Nb: 0.005 - 0.035, and V-0.06 max.
  • each alloying element and the limitations imposed on each element are essential for achieving the target microstructure and properties.
  • Carbon is one of the most effective and economical strengthening elements. Carbon combines with Nb or V to form carbides or carbonitrides which bring about precipitation strengthening. This requires a minimum of 0.03%C in the steel. However, in order to have good weld-ability, the carbon content has to be restricted to less than 0.12%.
  • Mn 0.8-1.5%: Manganese not only imparts solid solution strengthening to the ferrite but it also lowers the austenite to ferrite transformation temperature thereby refining the ferrite grain size. However, the Mn level cannot be increased to beyond 1.5% as at such high levels it enhances centerline segregation during continuous casting.
  • Si ⁇ 0.1 wt. % Silicon like Mn is a very efficient solid solution strengthening element
  • Si leads surface scale problems in hot rolling and hence it should be restricted to less than 0.1% in order to prevent the formation of surface scales.
  • Nb 0.035% maximum: Niobium is the most potent microalloying element for grain refinement even when it is added in very small amounts. When in solid solution it lowers the austenite to ferrite transformation temperature which not only refines the ferrite grain size but also promotes the formation of lower transformation products like bainite. However, to ensure the effectiveness of Nb, it should not be allowed to precipitate before the transformation temperature is reached. To ensure that the entire Nb content remains in solution before rolling commences and it is alone added, the maximum Nb content Is restricted to 0.035%.
  • V 0.06% maximum: Microalloying by Vanadium also leads to precipitation strengthening as well as grain refinement.
  • the solubility of Vanadium in austenite is more than that of other microalloying elements and so it is more likely to remain in solution prior to transformation.
  • vanadium precipitates as carbides and/or nitrides, depending on the relative carbon and nitrogen contents, at grain boundaries resulting in precipitation strengthening as well as grain refinement
  • Nb or V Both can also be added. If V alone is added, it is required up to 0.06 wt.%.
  • P 0.025% maximum: Phosphorus content should be restricted to 0.025% maximum as higher phosphorus levels can lead to reduction in toughness and weldability due to segregation of P into grain boundaries.
  • N ⁇ 0.007 Too high N content raises the dissolution temperature of Nb(C, N) and hence reduces the effectiveness of Nb. Reducing nitrogen levels also positively affects ageing stability and toughness in the heat-affected zone of the weld seam, as well as resistance to inter-crystalline stress-corrosion cracking. Thus N levels should be preferably kept below 0.007.
  • Al 0.01 to 0.1 Al is used to remove undesirable oxygen from molten steel and hence steel contains same amount of Al, may be upto 0.05 wt.%. Excess (high) Al in steel making is a major problem as it decreases hot deformation of cast slab besides nozzle dogging during casting. Therefore, Al needs to be restricted to 0.1 wt.%.
  • step (108) the liquid steel is continuously casted into a slab.
  • the liquid steel of the specified composition is first continuously casted either in a conventional continuous caster or a thin slab caster.
  • the temperature of the cast slab is not allowed to drop to a temperature below 950 °C. This is because if the thin slab temperature falls below 950 °C, Nb precipitation occurs. Then it becomes difficult to completely dissolve the precipitates in the subsequent reheating process rendering them ineffective for precipitation strengthening.
  • the slab After casting the slab with the specified composition, the slab is reheated to a temperature of 1100 to 1200 °C for a duration of 20 minutes to 2 hours.
  • the reheating temperature should be above 1100 °C, to ensure complete dissolution of any precipitates of Nb or/and V that may have formed in the preceding processing steps.
  • a reheating temperature greater than 1200 °C is also not desirable because it leads to grain coarsening of austenite and/or excessive scale loss.
  • Step (112) the slab is hot rolled into a hot rolled sheet at finish rolling temperature (FRT) 840 ⁇ 30°C.
  • the hot rolling constitute of a roughing step above the recrystallization temperature and a finishing step below the recrystallization temperature, when rolling is done in a conventional hot strip mill.
  • the deformation schedule is designed in such a manner that the cast structure is destroyed in the Initial stands and finishing is done below the recrystallization temperature. More specifically the finish rolling in either set up should be done at a temperature, T FRT given by 840 +/- 30 °C.
  • Laminar cooling on the Run-Out-Table (ROT): At step (116) the hot rolled sheet is cooled on a Run Out Table at cooling rate 40 - 70°C/s. The said cooling rate is maintained to achieve intermediate temperature (T INT ) 720 ⁇ T INT ⁇ 650.
  • the cooling rate should be higher than 40°C/s to prevent formation of pearlite. Any pearlite, or degenerate pearlite If formed leads to deterioration of both, tensile strength as well as stretch flangeability. High cooling rate also results in lowering the ferrite start temperature which leads to refinement of the ferrite grain size. It also prevents the growth of the ferrite. By increasing the cooling rate and controlling rolling schedule, the desired grain size of 2-6 ⁇ m can be achieved. The cooling rate may not be more than 70°C/s because then the desired amount of ferrite will not form. This fast cooling is continued up to an intermediate temperature.
  • the intermediate temperature (T INT ) should be 650 ⁇ T INT ⁇ 720° C.
  • the strip is allowed to naturally cool while being transferred on RoT.
  • the duration of air cooling is critical and is 5 to 7 seconds. If the strip is allowed to cool for less than 5 seconds, then sufficient amount of ferrite will not be formed. On the other hand, if the strip is allowed to air cool more than 7 seconds then it will results in insufficient amount of martensite.
  • austenite transforms to ferrite.
  • entire austenite will not transform to ferrite as time is not sufficient for complete transformation.
  • remaining austenite at the end of natural cooling will be enriched with carbon because ferrite cannot accommodate average carbon content in the steel.
  • the strip Is further cooled rapidly after naturally being cooled at step (120). This ensures the transformation of remaining carbon enriched austenite to martensite.
  • the cooling rate during this period is 40 - 70 °C/s to achieve coiling temperature below 406 0 C.
  • the coiling temperature can be as low as 100 deg.C
  • the microstructure obtained comprises martensite pupe/phase in the ferrite matrix.
  • the microstructure is uniform or in other words martensite phase is distributed uniformly throughout the ferrite matrix. Furthermore, bainite or degenerate pearlite/ pearlite and grain boundary cementite is avoided and high strength dual phase steel sheet achieves good work hardening rate, low yield point and continuous yielding. The contribution of each of the microstructural components is described below:
  • the high strength dual phase steel sheet has got improved fatigue life due to the presence of fine precipitate in the ferrite matrix coupled with martensite as second phase.
  • the yield stress of the high strength dual phase steel sheet obtained is 350 - 500 MPa.
  • the tensile strength obtained is min. 600 MPa.
  • the min. uniform elongation is 16% and 22% minimum total elongation.
  • strain hardening exponent ("n") of the high strength dual phase steel sheet is 0.15 - 0.16.
  • Yield to Tensile strength (ratio) of the dual phase steel is 0.6 - 0.8 and the hole expansion ratio in punched condition is about 40%.
  • a slab of the composition (given in Table 1) according to the process 100 (Strip 1) was continuously cast in a CSP mill. Slab was hot rolled. The ROT cooling was done in accordance with the present disclosure and the cooling profile is given in FIG. 2 .
  • the mechanical properties steels sheet are listed in Table 2, 3 & 4.
  • the microstructures of the steels are shown in FIGS. 4 , 5 , 6 & 7 . It is dear from the mechanical properties and the microstructures achieved, that the target properties can be achieved when the chemistry and ROT cooling parameters do conform to the requirements of the disclosure.
  • FIGS. 4 , 5 , 6 & 7 consist of ferrite and martensite.
  • Tensile test samples with 50 mm gauge length were prepared in accordance to ASTM E8 standard. Typical tensile test plot is given in FIG. 3 . It is evident from the figure and table that newly developed steel has minimum 600 MPa tensile strength, 16 % uniform elongation and minimum 22 % total elongation, the strip has high strain hardening co-efficient 0.15, yield ratio (Yield strength to Tensile strength) between 0.6 & 0.8. The steel has dispersion of fine precipitates in ferrite matrix.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Claims (11)

  1. Un procédé (100) pour produire une tôle d'acier biphasée, comprenant les étapes consistant à :
    a) fabriquer un acier liquide ayant une composition chimique d'alliage constituée en % en poids de C : 0,03 à 0,12, Mn : 0,8 à 1,5, Si : < 0,1, Cr: 0,3 à 0,7, S : 0,008 max., P : 0,025 max., Al : 0,01 à 0,1, N : 0,007 max., Nb : 0,005 à 0,035, et V : 0,06 max. (104) ;
    b) couler en continu l'acier liquide en une brame (108) ;
    c) laminer à chaud la brame en une tôle laminée à chaud à une température de finition de laminage (FRT) de 840 ± 30 °C (112) ;
    d) refroidir la tôle laminée à chaud sur une table de sortie à une vitesse de refroidissement de 40 à 70 °C/s obtenant une température intermédiaire (TINT) de 720 ≤ TINT ≤ 650 (116) ;
    e) refroidir naturellement la tôle laminée à chaud sur une durée de 5 à 7 secondes (120) ; et
    f) refroidir rapidement la tôle laminée à chaud afin de transformer l'austénite restante enrichie en carbone en martensite, à une vitesse de refroidissement de 40 à 70 °C/s afin d'obtenir une température d'enroulement en deçà de 400 °C (124).
  2. Un procédé tel que revendiqué dans la revendication 1, dans lequel la tôle d'acier biphasée est réchauffée jusqu'à une plage de températures de 1 100 à 1 200 °C afin de dissoudre des précipités.
  3. Une tôle d'acier biphasée comprenant des phases de ferrite et de martensite produite conformément au procédé de la revendication 1, constituée en tant qu'éléments d'alliage en % en poids, de :
    C : 0,03 à 0,12, Mn : 0,8 à 1,5, Si : < 0,1, Cr :0,3 à 0,7, S : 0,008 max., P : 0,025 max.,
    Al : 0,01 à 0,1, N- 0,007 max., Nb : 0,005 à 0,035, et V- 0,06 max. ; restant de fer et impuretés inévitables,
    la tôle d'acier biphasée ayant une résistance à la traction de 600 MPa min.
  4. Une tôle d'acier biphasée telle que revendiquée dans la revendication 3, dans laquelle une limite d'élasticité de la tôle d'acier biphasée est de 350 à 500 MPa.
  5. Une tôle d'acier biphasée telle que revendiquée dans la revendication 3, la tôle d'acier biphasée ayant un allongement uniforme de 16 % min.
  6. Une tôle d'acier biphasée telle que revendiquée dans la revendication 3, la tôle d'acier biphasée ayant un allongement total de 22 % min.
  7. Une tôle d'acier biphasée telle que revendiquée dans la revendication 3, dans laquelle un coefficient d'écrouissage (« n ») de la tôle d'acier biphasée est de 0,15 à 0,16.
  8. Une tôle d'acier biphasée telle que revendiquée dans la revendication 3, dans laquelle l'élasticité à la résistance à la traction (rapport) est de 0,6 à 0,8.
  9. Une tôle d'acier biphasée telle que revendiquée dans la revendication 3, dans laquelle le rapport d'expansion de trou dans un état perforé est d'environ 40 %.
  10. Une tôle d'acier biphasée telle que revendiquée dans la revendication 3, la tôle d'acier biphasée comprenant de 75 à 90 % de ferrite, de 10 à 25 % de martensite et < 5 % de bainite en volume.
  11. Une tôle d'acier biphasée telle que revendiquée dans la revendication 3, dans laquelle la grosseur de grain de la tôle d'acier biphasée est de 2 à 5 µm.
EP17740800.2A 2017-02-10 2017-05-10 Tôle d'acier haute résistance à deux phases renforcé par dispersion et à affinage de grain laminée à chaud présentant une résistance à la traction minimale de 600 mpa et son procédé Active EP3408418B1 (fr)

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CN111020096B (zh) * 2019-11-22 2021-05-28 辽宁科技大学 一种双相汽车钢dp590的单lf工艺低氮控制方法
CN113926892B (zh) * 2020-06-29 2024-07-12 宝山钢铁股份有限公司 抗拉强度≥980MPa级热轧超高强度双相钢零件冲压成形工艺及应用
CN112430772A (zh) * 2020-09-28 2021-03-02 甘肃酒钢集团宏兴钢铁股份有限公司 基于csp流程的中温卷取型热轧dp600生产方法
JP2024512668A (ja) * 2021-04-02 2024-03-19 宝山鋼鉄股▲分▼有限公司 引張強度≧９８０ＭＰａの二相鋼と溶融亜鉛メッキ二相鋼およびそれらの急速熱処理製造方法
CN115029622B (zh) * 2022-04-29 2023-05-23 武汉钢铁有限公司 一种高表面质量热轧双相钢及其生产工艺
CN115491601A (zh) * 2022-09-20 2022-12-20 武汉钢铁有限公司 采用CSP产线生产屈服强度350MPa级经济型磁轭钢及生产方法

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WO2018146695A1 (fr) 2018-08-16
ES2951778T3 (es) 2023-10-24
KR20190131408A (ko) 2019-11-26
JP7063810B2 (ja) 2022-05-09
JP2020509151A (ja) 2020-03-26
US20200123630A1 (en) 2020-04-23
EP3408418A1 (fr) 2018-12-05

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