EP2684975A1 - Produit plat en acier laminé à froid et son procédé de fabrication - Google Patents

Produit plat en acier laminé à froid et son procédé de fabrication Download PDF

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Publication number
EP2684975A1
EP2684975A1 EP12175756.1A EP12175756A EP2684975A1 EP 2684975 A1 EP2684975 A1 EP 2684975A1 EP 12175756 A EP12175756 A EP 12175756A EP 2684975 A1 EP2684975 A1 EP 2684975A1
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EP
European Patent Office
Prior art keywords
temperature
flat
product
cooling
flat steel
Prior art date
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EP12175756.1A
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German (de)
English (en)
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EP2684975B1 (fr
Inventor
Roland Sebald
Dorothea Mattissen
Sigrun EBEST
Stefan Follner
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Priority to PL12175756T priority Critical patent/PL2684975T3/pl
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to ES12175756.1T priority patent/ES2614465T3/es
Priority to EP12175756.1A priority patent/EP2684975B1/fr
Priority to CN201380036484.9A priority patent/CN104471096B/zh
Priority to PCT/EP2013/064551 priority patent/WO2014009404A1/fr
Priority to BR112014021543-0A priority patent/BR112014021543B1/pt
Priority to KR1020147021943A priority patent/KR102128563B1/ko
Priority to US14/377,398 priority patent/US10344344B2/en
Priority to JP2015520969A priority patent/JP6236078B2/ja
Publication of EP2684975A1 publication Critical patent/EP2684975A1/fr
Application granted granted Critical
Publication of EP2684975B1 publication Critical patent/EP2684975B1/fr
Not-in-force legal-status Critical Current
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C21D8/0284—Application of a separating or insulating coating
    • 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
    • C22C38/002—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • 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
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to a cold rolled flat steel product and a process for its production.
  • flat steel products this refers to steel strips and sheets or blanks derived therefrom.
  • a dual-phase steel is known, which in addition to a strength of at least 950 MPa and good ductility also has a surface texture that allows using a simple manufacturing process, the flat product produced from this steel in the uncoated or provided with a corrosion protective coating state to a deforming a complex shaped component, such as a part of an automobile body.
  • This is achieved according to this prior art by the fact that the known dual-phase steel consists of 20-70% of martensite, up to 8% of retained austenite and the remainder of ferrite and / or bainite.
  • the known steel in wt .-%): C: 0.10 - 0.20%, Si: 0.10 - 0.60%, Mn: 1.50 - 2.50%, Cr: 0, 20 - 0.80%, Ti: 0.02-0.08%, B: ⁇ 0.0020%, Mo: ⁇ 0.25%, Al: ⁇ 0.10%, P: ⁇ 0.2%, S: ⁇ 0.01%, N: ⁇ 0.012% and the remainder iron and unavoidable impurities.
  • a flat steel product made from such a steel can be used as a hot strip or cold strip.
  • Si is used in the known steel to increase the strength by hardening the ferrite or bainite.
  • a minimum content of Si of 0.10 wt .-% is provided.
  • the Si content is limited to 0.6 wt%, with lower upper limits for the Si content be particularly preferred to minimize the risk of grain boundary oxidation.
  • the cutting gap is 8% to 14% of the sheet thickness.
  • the board is clamped in the test tool so that the degree of cutting of the hole is on the bottom.
  • the hold-down force is a maximum of 400 kN.
  • Below the tool then becomes a round 100 mm diameter punch against the sample and the board is arched until the hole edge fails.
  • the maximum hole diameter d M reached when a first crack of the hole edge occurs is detected, and the hole expansion ratio ⁇ M is determined as the ratio d 0 / d M expressed in "%".
  • the object of the invention was to provide a flat steel product which can be produced by simple means and, despite high strength values, has optimum deformability characterized by a high elongation at break and a good hole expansion ratio ⁇ M.
  • a method should be given which allows the production of such a flat steel product in a simple manner.
  • the solution according to the invention of the abovementioned object is that during the production of a cold-rolled flat steel product according to the invention, the working steps specified in claim 4 are run through.
  • a flat steel product according to the invention is accordingly produced from a steel which consists of (in% by weight) C: 0.12 - 0.19%, Mn: 1.5-2.5%, Si: > 0, 60 - 1,0%, Al: ⁇ 0.1%, Cr: 0.2 - 0.6%, Ti: 0.05-0.15%, and the remainder is iron and production-related unavoidable impurities.
  • the structure of the flat steel product according to the invention is characterized in that it has 2-15% by volume, in particular at least 5% by volume, better still more than 8% by volume retained austenite.
  • the microstructure of a steel according to the invention is free in the technical sense of bainite and perlite.
  • the presence of effective bainite or pearlite content in the microstructure of a flat steel product according to the invention would impair its elongation at break and, consequently, its deformability, in particular the desired good hole widening properties. Due to the inventively specified contents of retained austenite, however, the required elongation at break of at least 15% is achieved, which has a flat steel product according to the invention.
  • a cold rolled flat steel product according to the invention has distinct differences.
  • Complex phase steels generally have a higher yield ratio, compared to the flat steel product according to the invention, with a lower "quality" calculated as the product of tensile strength Rm and elongation at break A80. This is due to the relatively high yield strength and thereby lower elongation of the known steels
  • the deformation behavior of the flat steel product according to the invention is similar to that of a dual-phase steel. However, a big difference can be found in the structures. While a flat steel product according to the invention has a residual austenite content of up to 15% Dual-phase steels no or only very low retained austenite contents.
  • TRIP steels in contrast to the flat steel product according to the invention, have significantly higher elongations at break. This results in grades (Rm * A80) of 20,000 MPa *% and more.
  • TRIP steels must be alloyed with increased contents of carbon, silicon and / or aluminum in order to achieve the so-called TRIP effect by means of sufficient stabilization of the retained austenite and secondly to achieve the corresponding strength.
  • such an alloy concept leads to a weldability that is significantly worse than that of a flat steel product according to the invention, in which high strength and, on the other hand, good weldability are attained by setting the contents of the alloying elements in an optimized manner, in particular with regard to the Si content.
  • the hole expansion ratio ⁇ M determined according to Marciniak is at least 6% for a flat steel product according to the invention, with hole expansion ratios ⁇ M of 7% and more regularly being achieved.
  • a flat steel product according to the invention has a high elongation at break of at least 15% and, associated therewith, a quality (Rm * A80) which is at least 14000 MPa *% at a minimum tensile strength Rm of 880 MPa.
  • the tensile strengths Rm Steel flat products according to the invention in the range of 880-1150 MPa.
  • the yield strength of a flat steel product according to the invention is at least 550 MPa, yielding yield strengths of 580 MPa and more on a regular basis. Typically, the yield strengths of flat steel products according to the invention are in the range of 580 - 720 MPa. For a flat steel product according to the invention, the yield ratio (ReL / Rm) is accordingly also 0.55-0.75.
  • the elongation at break A80 of a flat steel product according to the invention is at least 15%, with regular elongation at break A80 of up to 25% being achieved.
  • Carbon is present in a flat steel product of the invention at levels of 0.12-0.19% by weight to provide strength enhancement by interstitial solid solution formation and precipitation hardening to form cementite (Fe 3 C).
  • the minimum level of 0.12 wt% is necessary to achieve the desired strength.
  • the maximum content of 0.19% by weight should not be exceeded in order to meet in practice the weldability of Flat steel products of the type according to the invention requirements to meet.
  • Manganese is present in a flat steel product of the invention at levels of 1.5-2.5% by weight.
  • the addition of manganese increases yield strength and tensile strength.
  • a tensile strength Rm of at least 880 MPa and a yield strength ReL of at least 550 MPa, in particular at least 580 MPa possible.
  • More than 2.5% by weight of Mn should not be present in a steel according to the invention, since at higher Mn contents the risk of formation of manganese segregations increases, which can adversely affect the material behavior.
  • the content of silicon which is present in a steel flat product according to the invention in contents of> 0.60-1.0% by weight, is of particular importance with regard to the formation of the microstructure.
  • Si content By making the Si content more than 0.60% by weight, the formation of pearlite is suppressed, enabling carbonization of the austenite with carbon and concomitantly increasing the retained austenite stability.
  • the retained austenite transforms into martensite during forming, which provides additional strengthening.
  • Silicon also forms mixed crystals with iron, which increase the strength in the steel.
  • the positive effects of the presence of silicon in a flat steel product according to the invention can be used particularly reliably if the Si content is at least 0.65% by weight, in particular at least 0.7% by weight.
  • the Si content is limited to at most 1.0% by weight, such scale formation being limited in particular when the Si content is limited to not more than 0.95% by weight.
  • the steel constituting the flat steel product according to the invention is aluminum-killed. Accordingly, flat steel products according to the invention regularly contain more than 0.01% by weight and up to 0.1% by weight of aluminum.
  • Chromium is present in a flat steel product of the invention at levels of 0.2-0.6 wt%. Chromium strengthens the steel flat product according to the invention. In addition, in the course of the production of a flat steel product according to the invention, hot processing of the steel is delayed by the presence of Cr, the formation of bainite. A content of 0.2% by weight is required to achieve the necessary strength. The content is limited to 0.6 wt .-%, since tests have shown that too high a chromium content has an unfavorable effect on the elongation and concomitantly on the quality (Rm * A80) of the flat steel product according to the invention.
  • Titanium is added to a flat steel product according to the invention as a micro-alloying element in amounts of 0.05-0.15% by weight. Due to the presence of Ti, the steel has the finest precipitates of Ti (C, N) contributing to increase in strength and grain refining.
  • the grain size of the structure according to ASTM is less than or equal to 15, ie less than or equal to 1.9 ⁇ m.
  • a Ti content of at least 0.05 wt .-% is required, with the positive effect of Ti is particularly safe when the Ti content of the steel at least 0.07 wt .-%, in particular at least 0.09 wt .-%, is. From a content of 0.15 wt .-%, no further improvements of the effect of Ti occur.
  • a flat steel product according to the invention is suitable for applications in which higher degrees of deformation in combination with high strength values are necessary.
  • Typical examples of these applications are crash-relevant components such as side members and permanently loaded chassis parts during operation.
  • the steel flat product is cooled at a cooling rate of 8-100 K / s to an intermediate temperature of 450-550 ° C.
  • the cooling rate of at least 8 K / s is needed here in order to avoid the formation of perlite and bainite and nevertheless to generate sufficient amount of ferrite.
  • In the temperature range of 450 ° C to 550 ° C also finds the first enrichment of austenite with carbon instead.
  • the cooling in the first stage of the two-stage cooling can be carried out with any suitable, ensuring a sufficient cooling rate medium.
  • available cooling devices are used in practice. So the cooling can be done in moving air.
  • the cooling in the second stage of the two-stage cooling can be carried out according to a practical embodiment of the invention in that the flat steel product is cooled by contact with the cooled rollers.
  • the steel flat product can be cooled in the second stage of the two-stage cooling by a moving air flow.
  • the overaging treatment can be done, for example, by the steel flat product undergoing an environmentally shielded space in the overaging treatment.
  • the temperature of the flat steel product is set to 100-400 ° C. Based on the temperature with which the Steel flat product enters the overaging treatment, this adjustment of the temperature can be carried out as heating, cooling or holding.
  • the coating of the flat steel product with the metallic protective layer can be carried out particularly effectively electrolytically.
  • the figure shows a diagram in which the typical for an inventive annealing spans the temperature profile are shown over time.
  • the slabs were then thoroughly heated at an austenitizing temperature of 1100-1300 ° C., so that the slabs had a completely austenitic microstructure on entry into the subsequently passed hot rolling mill.
  • the slabs are then hot-rolled at the hot-rolling end temperatures WET given in Table 1b to hot-rolled strip with a thickness DKW of 1.8-4.6 mm, then air, to the respective values also given in Table 1b Reel temperature HT cooled and reeled at the rewinding temperature HT respectively achieved. Pickling was then optionally performed to remove any scale present on the hot strip prior to cold rolling to allow for optimum surface finish during subsequent cold rolling.
  • samples of the cold-rolled steel flat products thus obtained were subjected to various heat treatments A - J, in which they are heated in each case to an annealing temperature GT, then held at the annealing temperature GT over an annealing time tG, then in a first cooling stage with a first cooling rate r1 a first target temperature ZT1 and immediately thereafter in a second cooling stage with a second cooling rate r2 have been brought to a second target temperature ZT2.
  • the respectively obtained samples of cold rolled steel flat products are over an aging period of 250-710 s for a period of time tUeA at an over-aging temperature TUeA at 400-100 ° C at the end of the treatment, in an overburdened space of an overaging treatment been subjected.
  • the parameters set during heat treatment A - J respectively GT, tG, r1, ZT1, r2, ZT2 and tUeA are listed in Table 2.
  • the steel flat product samples produced from the non-composite steel melts 6 and 7 do not reach the lower limits of 880 MPa or 550 MPa, in particular 580 MPa, given their tensile strength Rm or their yield strength ReL, even if they have a lower limit Subjected to heat treatment, which is carried out in accordance with the invention.
  • the flat product samples assembled and heat-treated according to the invention regularly exceed these limits.
  • Table 1a stolen C Mn Si al Cr Ti P N S 1 0.17 1.9 0.72 0, 04 0.37 0, 114 0,012 0.0048 0.001 2 0.13 2.3 0.65 0.06 0.23 0.07 0,007 0.009 0,007 3 0.16 1.7 0.75 0.03 0.57 0.108 0,013 0,007 0,006 4 0.18 2.1 0.94 0.02 0.34 0.143 0.009 0,007 0.009 5 0.14 1.5 0.83 0.08 0.48 0.135 0,018 0,006 0,002 6 0.15 1.8 0.53 0.05 0.43 0.15 0,014 0,003 0,003 7 0.14 2.4 0.73 0.06 0.05 0.09 0.009 0,004 0.005 Content in wt .-%, balance iron and unavoidable impurities stole WET [° C] HT [° C] dW [mm] KWG [%] dKB [mm] D ° [%] According to the invention?

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP12175756.1A 2012-07-10 2012-07-10 Produit plat en acier laminé à froid et son procédé de fabrication Not-in-force EP2684975B1 (fr)

Priority Applications (9)

Application Number Priority Date Filing Date Title
ES12175756.1T ES2614465T3 (es) 2012-07-10 2012-07-10 Producto plano de acero laminado en frío y procedimiento para su fabricación
EP12175756.1A EP2684975B1 (fr) 2012-07-10 2012-07-10 Produit plat en acier laminé à froid et son procédé de fabrication
PL12175756T PL2684975T3 (pl) 2012-07-10 2012-07-10 Produkt stalowy płaski, walcowany na zimno i sposób jego wytwarzania
PCT/EP2013/064551 WO2014009404A1 (fr) 2012-07-10 2013-07-10 Produit d'acier plat laminé à froid et son procédé de fabrication
CN201380036484.9A CN104471096B (zh) 2012-07-10 2013-07-10 冷轧扁钢产品及其制造方法
BR112014021543-0A BR112014021543B1 (pt) 2012-07-10 2013-07-10 Produto de aço plano laminado a frio e processo para sua produção
KR1020147021943A KR102128563B1 (ko) 2012-07-10 2013-07-10 냉간-압연 평탄형 강 제품 및 그 제조 방법
US14/377,398 US10344344B2 (en) 2012-07-10 2013-07-10 Cold-rolled flat steel product and method for its production
JP2015520969A JP6236078B2 (ja) 2012-07-10 2013-07-10 冷間圧延鋼板製品およびその製造方法

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Application Number Priority Date Filing Date Title
EP12175756.1A EP2684975B1 (fr) 2012-07-10 2012-07-10 Produit plat en acier laminé à froid et son procédé de fabrication

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EP2684975A1 true EP2684975A1 (fr) 2014-01-15
EP2684975B1 EP2684975B1 (fr) 2016-11-09

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US10697040B2 (en) * 2015-09-28 2020-06-30 Baoshan Iron & Steel Co., Ltd. Continuous annealing method for low coercive force cold-rolled electromagnetic pure iron plate and strip
EP3872206A1 (fr) * 2020-02-28 2021-09-01 ThyssenKrupp Steel Europe AG Procédé de fabrication d'un produit plan en acier laminé à froid, traité ultérieurement et produit plan en acier laminé à froid, traité ultérieurement
WO2023126506A1 (fr) * 2021-12-29 2023-07-06 Voestalpine Grobblech Gmbh Plaque lourde et procédé de manipulation thermomécanique de matériau de départ de production de plaque lourde

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EP3555337A1 (fr) * 2016-12-14 2019-10-23 ThyssenKrupp Steel Europe AG Produit plat en acier laminé à chaud et son procédé de fabrication
WO2018115936A1 (fr) * 2016-12-21 2018-06-28 Arcelormittal Tôle d'acier revêtue et revenue présentant une excellente formabilité et son procédé de fabrication
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CN112789358B (zh) * 2018-09-26 2022-03-25 蒂森克虏伯钢铁欧洲股份公司 制造经涂覆的扁钢产品的方法和经涂覆的扁钢产品
WO2020245627A1 (fr) * 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
CN113403544B (zh) * 2021-05-21 2022-07-22 鞍钢股份有限公司 汽车超高成形性980MPa级冷轧连退钢板及制备方法
CN115198206B (zh) * 2022-06-21 2023-09-15 首钢集团有限公司 一种高力学性能热轧复相钢及其制备方法
CN115491598B (zh) * 2022-09-15 2023-07-11 首钢集团有限公司 一种1180MPa级相变诱发塑性钢及其制备方法

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WO2015185956A1 (fr) * 2014-06-06 2015-12-10 ArcelorMittal Investigación y Desarrollo, S.L. Tôle d'acier galvanisée polyphasique à résistance élevée, procédé de production et utilisation
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CN108115105A (zh) * 2017-12-22 2018-06-05 中钢集团邢台机械轧辊有限公司 一种高合金离心轧辊的制备方法
CN108115105B (zh) * 2017-12-22 2021-05-14 中钢集团邢台机械轧辊有限公司 一种高合金离心轧辊的制备方法
EP3872206A1 (fr) * 2020-02-28 2021-09-01 ThyssenKrupp Steel Europe AG Procédé de fabrication d'un produit plan en acier laminé à froid, traité ultérieurement et produit plan en acier laminé à froid, traité ultérieurement
WO2023126506A1 (fr) * 2021-12-29 2023-07-06 Voestalpine Grobblech Gmbh Plaque lourde et procédé de manipulation thermomécanique de matériau de départ de production de plaque lourde

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KR102128563B1 (ko) 2020-07-08
KR20150031407A (ko) 2015-03-24
US10344344B2 (en) 2019-07-09
US20150000797A1 (en) 2015-01-01
EP2684975B1 (fr) 2016-11-09
JP2015528058A (ja) 2015-09-24
WO2014009404A1 (fr) 2014-01-16
JP6236078B2 (ja) 2017-11-22
CN104471096B (zh) 2017-08-15
CN104471096A (zh) 2015-03-25
BR112014021543B1 (pt) 2020-03-17
ES2614465T3 (es) 2017-05-31
PL2684975T3 (pl) 2017-08-31

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