WO2018110867A1 - Tôle d'acier laminée à froid à haute résistance présentant une excellente limite d'élasticité, une excellente ductilité et une excellente capacité d'expansion de trou, tôle d'acier galvanisée par immersion à chaud et procédé de production associé - Google Patents

Tôle d'acier laminée à froid à haute résistance présentant une excellente limite d'élasticité, une excellente ductilité et une excellente capacité d'expansion de trou, tôle d'acier galvanisée par immersion à chaud et procédé de production associé Download PDF

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WO2018110867A1
WO2018110867A1 PCT/KR2017/013762 KR2017013762W WO2018110867A1 WO 2018110867 A1 WO2018110867 A1 WO 2018110867A1 KR 2017013762 W KR2017013762 W KR 2017013762W WO 2018110867 A1 WO2018110867 A1 WO 2018110867A1
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steel sheet
less
rolled steel
hot
ductility
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PCT/KR2017/013762
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Korean (ko)
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WO2018110867A8 (fr
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곽재현
조항식
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주식회사 포스코
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Priority to EP17881067.7A priority Critical patent/EP3556896B1/fr
Priority to JP2019531765A priority patent/JP6846522B2/ja
Priority to US16/468,162 priority patent/US20200190612A1/en
Priority to CN201780077454.0A priority patent/CN110073026B/zh
Publication of WO2018110867A1 publication Critical patent/WO2018110867A1/fr
Publication of WO2018110867A8 publication Critical patent/WO2018110867A8/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—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
    • 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
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • C22C38/50—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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C23C2/34—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
    • C21D2211/001—Austenite
    • 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

Definitions

  • the present invention relates to a high strength steel sheet used in an automobile body, and more particularly, to a high strength cold rolled steel sheet, a hot dip galvanized steel sheet, and a method of manufacturing the same, which have high strength and excellent yield strength and formability. .
  • the metamorphic steel is classified into so-called DP (Dual Phase) steel, Transformation Induced Plasticity (TRIP) steel, and Complex Phase (CP) steel.
  • DP Dual Phase
  • TRIP Transformation Induced Plasticity
  • CP Complex Phase
  • Each of these steels has mechanical properties, that is, according to the type and fraction of the parent phase and the second phase.
  • the level of tensile strength and elongation is different, especially in the case of TRIP steel containing residual austenite, the balance of tensile strength and elongation (TS x El) shows the highest value.
  • CP steel of the metamorphic structure steel as described above is lower than the other steels, and is limited to simple processing such as roll forming, and high ductility DP steel and TRIP steel are applied to cold press forming.
  • Patent Document 2 discloses a method of forming residual austenite and martensite as a main structure (Quenching and Partitioning Process (Q & P)). According to a report using this (non-patent document 1), the carbon level is 0.2%. In the case of low, the yield strength has a disadvantage of low around 400MPa, and it can be confirmed that the elongation obtained in the final product is only similar to the existing TRIP steel.
  • the essence of the Q & P method is to secure ductility by quenching between the martensite transformation start temperature (Ms) and the finish temperature (Mf) and then reheating to stabilize the austenite by carbon diffusion at the martensite and austenite interface.
  • Ms martensite transformation start temperature
  • Mf finish temperature
  • fresh martensite (FM) is formed in the final cooling step, and the fresh martensite has a high carbon content and inhibits pore expansion (Patent Document 3).
  • Patent Document 4 there is a method of securing the ductility and hole expandability by heat-treating the martensite structure again in an abnormal region, but this is not economical by performing two heat treatments.
  • Patent Document 1 Korean Unexamined Patent Publication No. 1994-0002370
  • Patent Document 2 US Publication No. 2006-0011274
  • Patent Document 3 Japanese Patent Application JP2002-177278
  • Patent Document 4 Japanese Patent Publication JP2001-300503
  • Patent Document 5 Japanese Patent Publication JP2014-018431
  • Non-Patent Document 1 ISIJ International, Vol. 51, 2011, p. 137-144
  • the present invention has been made to solve the above-mentioned limitations of the prior art, and implements a lower alloy cost compared to the existing TWIP steel, compared to the case of applying the conventional TBF (Trip aided Bainitic Ferrite) Q & P (Quenching and Partitioning) heat treatment process. It is an object of the present invention to provide a cold rolled steel sheet of bainite columnar having better ductility and hole expandability, a hot-dip galvanized steel sheet produced using the same, an alloyed hot-dip galvanized steel sheet, and a method of manufacturing the same.
  • the microstructure yields 50% or more of bainite, 10% or more of tempered martensite (TM), 10% or less of fresh martensite (FM), 20% or less of residual austenite and 5% or less of ferrite. It relates to a high strength cold rolled steel sheet excellent in strength, ductility and hole expansion properties.
  • the TM / FM ratio is greater than two.
  • the present invention also relates to a hot-dip galvanized steel sheet hot-dip galvanized on the surface of the cold-rolled steel sheet, and an alloyed hot-dip galvanized steel sheet which has been alloyed hot-dip galvanized.
  • the steel sheet after the continuous Q & P continuous annealing has a microstructure of 50% or more of bainite, 10% or more of tempered martensite (TM), 10% or less of fresh martensite (FM), and 20% or less of residual austenite. And 5% or less of ferrite.
  • the TM / FM ratio is greater than two.
  • the present invention compared with the conventional high-ductile transformation tissue steel such as DP steel or TRIP steel and Q & P steel subjected to conventional Q & P (Quenching & Partitioning) heat treatment, it is possible to ensure accurate TM amount and bainite It can effectively provide high strength cold rolled steel sheet, hot dip galvanized steel sheet and alloyed hot dip galvanized steel sheet with yield strength and ductility and hole extension property excellent in tensile strength of 980MPa or more.
  • Figure 2 shows the low temperature transformation behavior of the TBF method and the present invention method.
  • Figure 3 is a photograph observing the microstructure of the inventive example (F) steel produced by the present invention.
  • nitrogen reduces the alloying efficiency of alloying elements by forming BN and TiN, it is preferable to limit it to 0.01% or less, which is usually in a controllable range.
  • the remaining component of the present invention is iron (Fe).
  • Fe iron
  • other conventional steelmaking processes undesired impurities from raw materials or the surrounding environment can be inevitably incorporated. Since these impurities are known to those skilled in the art of ordinary steel manufacturing, not all of them are specifically mentioned herein.
  • the cold rolled steel sheet of the present invention that satisfies the above-described microstructure has a tensile strength of 980 MPa or more, and has high yield strength and press formability, ductility, and hole expansion properties compared to steel sheets manufactured through conventional Q & P heat treatment. High strength steel sheet can be provided.
  • the reheating step is preferably carried out at 1000 ⁇ 1300 °C.
  • the reheated steel slab is hot rolled to produce a hot rolled steel sheet, wherein hot finish rolling is preferably performed at 800 to 950 ° C.
  • cold rolling is carried out to secure the thickness required by the customer, and there is no limitation on the reduction ratio, but cold rolling reduction is performed at 30% or more to suppress the formation of coarse ferrite grains during recrystallization in a subsequent annealing process. It is preferable.
  • the produced cold-rolled steel sheet is cracked for more than 30 seconds at a temperature of Ac3 or more, and then cooled to a quenching temperature (QT) ⁇ 10 ° C defined by the following relation 1 at a cooling rate of 5 to 20 ° C / sec. (See Figure 1).
  • QT quenching temperature
  • the ferrite unformed cooling rate of the present invention was designed to be 5 ⁇ 20 °C. There is no problem even if the cooling rate is higher than this, but the slower the cooling rate, the better the plate shape without distortion, and does not need to be increased.
  • the elements such as carbon and manganese are concentrated in the austenite remaining in the bainite transformation process, so that the FM does not remain austenite and is transformed during final cooling. This is because the strength is very high, and the interfacial separation occurs during the hole expansion, so that the cracks are easily broken, thereby greatly reducing the hole expandability.
  • the temperature at which bainite is formed fastest in the reheating and constant temperature holding at bainite temperature PT was determined by experiment. If the temperature is higher than this, the amount of bainite formation is small, the stabilization of residual austenite is insufficient and the FM formation is rather increased. Therefore, PT must be heated to PT ⁇ 10 °C.
  • Constant temperature maintenance has the advantage that it is easy to apply to a facility having a constant temperature furnace without a heating maintenance device because it only needs to cool after maintaining for more than 100 seconds within the temperature range of QT ⁇ or ⁇ QT-100 °C.
  • Q & P heat treatment produces steel containing 50% or more of bainite, 10% or more of tempered martensite (TM), 10% or less of fresh martensite (FM), 20% or less of residual austenite and 5% or less of ferrite.
  • TM tempered martensite
  • FM fresh martensite
  • the first and second annealing heat-treated cold rolled steel plate may be plated to produce a plated steel sheet.
  • the plating treatment is preferably carried out by a hot dip plating method or an alloyed hot dip plating method, and the plating layer formed from them is preferably zinc-based.
  • the hot dip galvanizing bath may be manufactured as a hot dip galvanized steel sheet, and in the case of the hot dip galvanizing method, an alloy may be manufactured by performing a conventional alloy hot dip plating process.
  • the molten metal having the composition shown in Table 1 was prepared in a 90 mm thick, 175 mm wide ingot through vacuum melting. Subsequently, it was reheated for 1 hour at 1200 ° C. for homogenization treatment, and hot-rolled and rolled at 900 ° C. or higher, which is a temperature of Ar 3 or higher, to prepare a hot rolled steel sheet. Thereafter, the hot rolled steel sheet was cooled, charged into a furnace preheated to 600 ° C., held for 1 hour, and then cold rolled to simulate hot rolled winding. The hot rolled sheet material as described above was cold rolled at a cold reduction rate of 50 to 60%, and then subjected to annealing heat treatment under the conditions of Table 2 to produce a final cold rolled steel sheet.
  • FIG. 3 is a photograph observing the microstructure of the inventive example (F) steel produced by the present invention.
  • inventive steel (F) steel has a bainite of 75%, a TM, FM of 14%, and 5% of TM / FM of more than 2, and F of less than 5% of bays. It can be seen that the night steel can be produced.
  • This is a technical feature of the present invention, but conventionally focused on making ferritic TRIP steel or tempered martensitic steel through Q & P heat treatment, but if the steel composition and QT, PT are specified, the bainite matrix structure Can be made easier than the TBF heat treatment method.
  • FIG. 4 is an APT observation of TM in the tissue of FIG. 3.
  • the transition carbide and coarse cementite are mixed to show tempered martensite.
  • Figure 5 is the same component as the structure of the steel (E), but the ferrite and FM are formed due to the annealing annealing and TBF heat treatment can be confirmed that the strength and HER is low.
  • the cold rolled steel sheet produced according to the present invention can secure a yield strength and excellent elongation and HER of 980MPa or more, the cold forming for applying to the structural member compared to the steel produced through the conventional Q & P heat treatment process There is an advantage that can be easily performed.

Abstract

L'invention concerne une tôle d'acier laminée à froid à haute résistance présentant une excellente limite d'élasticité, une excellente ductilité et une excellente capacité d'expansion de trou, une tôle d'acier galvanisée par immersion à chaud et un procédé de production associé. La tôle d'acier laminée à froid de la présente invention comprend 0,06 à 0,2 % en poids de carbone (C), 1,5 à 3,0 % en poids de manganèse (Mn), 0,3 à 2,5 % en poids de silicium (Si), 0,01 à 0,2 % en poids d'aluminium (Al), 0,01 à 3,0 % en poids de nickel (Ni), 0,2 % en poids ou moins de molybdène (Mo), 0,01 à 0,05 % en poids de titane (Ti), 0,02 à 0,05 % en poids d'antimoine (Sb), 0,0005 à 0,003 % en poids de bore (B), 0,01 % en poids ou moins (0 % étant exclu) d'azote (N), le reste comprenant du Fe et des impuretés inévitables, et sa microstructure comprenant, en termes de fraction de surface, 50 % ou plus de bainite, 10 % ou plus de martensite revenue (TM), 10 % ou moins de martensite fraîche (FM), 20 % ou moins d'austénite résiduelle, et 5 % ou moins de ferrite.
PCT/KR2017/013762 2016-12-16 2017-11-29 Tôle d'acier laminée à froid à haute résistance présentant une excellente limite d'élasticité, une excellente ductilité et une excellente capacité d'expansion de trou, tôle d'acier galvanisée par immersion à chaud et procédé de production associé WO2018110867A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
EP17881067.7A EP3556896B1 (fr) 2016-12-16 2017-11-29 Tôle d'acier laminée à froid à haute résistance présentant une excellente limite d'élasticité, une excellente ductilité et une excellente capacité d'expansion de trou, et tôle d'acier galvanisée par immersion à chaud
JP2019531765A JP6846522B2 (ja) 2016-12-16 2017-11-29 降伏強度、延性、及び穴拡げ性に優れた高強度冷延鋼板、溶融亜鉛めっき鋼板、及びこれらの製造方法
US16/468,162 US20200190612A1 (en) 2016-12-16 2017-11-29 High strength cold-rolled steel sheet having excellent yield strength, ductility, and hole expandability, hot-dip galvanized steel sheet, and method for producing same
CN201780077454.0A CN110073026B (zh) 2016-12-16 2017-11-29 屈服强度、延展性和扩孔性优异的高强度冷轧钢板、热浸镀锌钢板及其制造方法

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CN115181895A (zh) * 2021-04-02 2022-10-14 宝山钢铁股份有限公司 1180MPa级别低碳低合金热镀锌Q&P钢及快速热处理热镀锌制造方法
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EP3988679A4 (fr) * 2019-08-20 2022-11-02 JFE Steel Corporation Tôle d'acier haute résistance laminée à froid et son procédé de fabrication
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CN114746562A (zh) * 2019-12-17 2022-07-12 安赛乐米塔尔公司 经热轧的钢板及其制造方法
CN114746562B (zh) * 2019-12-17 2023-12-29 安赛乐米塔尔公司 经热轧的钢板及其制造方法
CN115181895A (zh) * 2021-04-02 2022-10-14 宝山钢铁股份有限公司 1180MPa级别低碳低合金热镀锌Q&P钢及快速热处理热镀锌制造方法
CN115181895B (zh) * 2021-04-02 2023-09-12 宝山钢铁股份有限公司 1180MPa级别低碳低合金热镀锌Q&P钢及快速热处理热镀锌制造方法

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EP3556896B1 (fr) 2021-11-10
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