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WO2009095264A1 - Procédé de production d'un acier à plasticité induite par maclage, laminé à chaud, et produit en acier à plasticité induite par maclage produit à l'aide du procédé - Google Patents

Procédé de production d'un acier à plasticité induite par maclage, laminé à chaud, et produit en acier à plasticité induite par maclage produit à l'aide du procédé Download PDF

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Publication number
WO2009095264A1
WO2009095264A1 PCT/EP2009/000633 EP2009000633W WO2009095264A1 WO 2009095264 A1 WO2009095264 A1 WO 2009095264A1 EP 2009000633 W EP2009000633 W EP 2009000633W WO 2009095264 A1 WO2009095264 A1 WO 2009095264A1
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WO
WIPO (PCT)
Prior art keywords
hot
strip
rolling
steel
cold
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/EP2009/000633
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English (en)
Inventor
Marcus Cornelis Maria Cornelissen
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Tata Steel Ijmuiden BV
Original Assignee
Corus Staal BV
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Corus Staal BV filed Critical Corus Staal BV
Priority to EP09705515.6A priority Critical patent/EP2257394B1/fr
Priority to ES09705515T priority patent/ES2705203T3/es
Priority to KR1020167007883A priority patent/KR20160039304A/ko
Publication of WO2009095264A1 publication Critical patent/WO2009095264A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling

Definitions

  • This invention relates to a method for producing a hot-rolled TWIP-steel, and a TWIP-steel produced thereby.
  • High manganese austenitic steels combine a capacity to be drawn into very complex parts with a very high strength.
  • TWIP steels derive their exceptional properties from a specific strengthening mechanism: twinning. In addition to the basic mechanism of dislocation gliding, deformation also occurs by twinning.
  • the steels are fully austenitic and nonmagnetic during production at high temperatures and during use at ambient temperatures. The formation of mechanical twins during deformation generates high strain hardening, prevents necking and thus maintains a very high strain capacity. This mechanism is called TWinning Induced Plasticity.
  • TWIP-steels are particularly useful in parts of a car such as the inner parts of the A-pillar, because large deformations of the part prior to mounting in the car are required, whereas significant reduction potential must be present to act as a crash absorber in the event of an accident.
  • the steel components must combine two different characteristics: they should be ductile to absorb most of the collision energy and at the same time have sufficient shape stability to protect the passenger cabin.
  • the TWIP- steel part is able to accommodate further deformation because of its ductility reserve. Each part of the steel elongates, then strengthens and passes on the remaining deformation energy to the surrounding parts, which then also starts to deform. Hence, by dispersing energy over the whole surface, the collision momentum is absorbed more efficiently and the passengers stay safe.
  • TWIP steels are currently being considered.
  • Conventional production routes involve casting of thick slabs of 200 to 400 mm in thickness. These slabs are reheated to temperatures between 1100 and
  • an oxide layer is formed on the surface of the hot-rolled strip.
  • the hot-rolled strip has to be pickled to remove this oxide layer before cold-rolling to the final thickness. After pickling, the strip is cold- rolled to the final thickness. In the cold-rolling process the resulting cold-rolled strip becomes heavily deformed.
  • the strip Prior to coating in a hot-dip coating process, the strip must be annealed to promote recrystallisation of the cold deformed microstructure to restore the formability of the steel.
  • One or more of the objects of the invention is reached by providing a method for the manufacture of a TWIP-steel strip, whereby molten steel is cast in a continuous casting machine with one or more strands to form a slab having a thickness of at least 30 mm and at most 120 mm and, while making use of the casting heat, is conveyed through a furnace apparatus, is hot-rolled in a hot-rolling mill comprising one or more rolling stands into a steel strip of a desired final thickness (h f ), i. in an endless rolling process wherein a.
  • This method allows a large reduction of the cast slab while ensuring a very homogeneous temperature over the width and thickness of the strip.
  • the method does not relate to the so-called strip-casting process, wherein a strip of a thickness between 1 and 20 mm is. These thin strips do not allow a sufficiently large reduction of the cast slab.
  • the material connection it is possible to reach a small finished thickness after hot- rolling, because the head of each new coil is attached to the tail of the preceding coil, and these are only separated immediately before coiling thereby avoiding risks of lift-off of the strip from the run-out table after the hot-rolling mill.
  • the micro-segregation of alloying elements is neutralised in the furnace apparatus by diffusion.
  • the macro-segregation is levelled out by the large deformation of the solidified slab in the hot rolling operation.
  • This hot rolling operation may comprise a roughing operation and a separate finishing operation, but the entire rolling operation may also be performed in a rolling mill in which the roughing and finishing operation are combined.
  • the constant rolling speed during endless or semi- endless rolling process ensures that each point of a slab has substantially the same thermo-mechanical history and this is a great advantage for these kinds of steels in comparison to the slab-by-slab and coil-by-coil process because the thermally activated processes such as the diffusion process to counteract the micro-segregation, the dynamic and static recrystallisation during rolling, the grain growth of the austenitic grains, the development of the crystallographic texture, precipitation reactions result in a homogeneous product. Also the rolling speed over the length of the slab is substantially constant, which is not the case in the slab-by-slab and coil-by-coil process.
  • the microstructure of the ferrous matrix of the finished sheet has an austenite volume content of at least 75%.
  • the slab After thin slab casting the slab is either directly fed to a soaking furnace to provide the slab with the correct and homogeneous (over length width and thickness of the slab) temperature for the hot-rolling step, or directly fed from the casting to the hot-rolling step with no, or only a very limited temperature correction.
  • the thin slab preferably has a thickness of at most 100 mm, and is at least 30 mm. Preferably, the thin slab thickness is between 30 and 90 mm.
  • the thickness of the strip is mainly produced by hot-rolling because of the very limited or even absent cold-rolling step, it is advantageous if the thin slab thickness is as low as possible.
  • the minimum slab thickness is limited by dimensional limitations of the thin slab casting process. So a thin slab of about 45 to 65 mm may be preferable.
  • Liquid core reduction of the cast slab may be used to reduce the slab in thickness prior to hot-rolling. Due to the difference in metallurgical conditions, liquid core reduction in this context is deemed to be part of the casting process, and not of the hot-rolling process.
  • hot-rolled thickness of the steel strip is between 0.5 and 5 mm.
  • the preferable thickness range is between 0.5 and 3.0 mm. More preferably the maximum thickness is 2.5 or even 2.0 mm. A suitable minimum thickness is 0.8 mm or even 1.0 mm.
  • the molten steel has a composition comprising 0.05-0.78% C, 9 to 30% Mn, at most 5% Al, at most 5% Cr, at most 2.5% Ni, at most 5% Si, at most 0.5% V, the remainder being iron and unavoidable impurities. All compositional percentages are given in weight percent unless indicated otherwise. Steels of this composition were found to exhibit excellent TWIP-related properties.
  • vanadium a preferably minimum vanadium content is at least 0.05%.
  • aluminium a preferable minimum aluminium content of the steel is at least 1 %. The aluminium content of the steel of at least 1 % ensures an increased stability of the austenite.
  • the alloying with vanadium will promote the formation of VC-precipitates which contribute to the strength of the steel and the prevention of delayed cracking by providing sinks for hydrogen at the predominantly semi-coherent interface between the VC-precipitates and the matrix.
  • a minimum vanadium content of 0.1 or even 0.2% is preferable.
  • the chromium content is at most 0.5% and/or at least 0.05%.
  • a suitable minimum chromium content is 0.10 or even 0.15%.
  • the steel sheet comprises a maximum Mn content of 23% or preferably 11 to 18% Mn.
  • a suitable maximum manganese content is 16% or even 15.5%.
  • the Ni and Mn contents are chosen such that (Ni+Mn) is from 11.0 to 23.
  • a preferable maximum for (Ni+Mn) is 18%. More preferably this maximum is chosen to be 17 or even 15.9%.
  • the microstructure of the sheet comprises at least 80%, preferably at least 85%, more preferably at least 90% and even more preferably at least 95% in volume of austenite after hot rolling and cooling. Due to the metastability of the austenite, and the occurrence of transformation induced plasticity, the amount of austenite tends to decrease during subsequent processing steps. In order to ensure good formability and high strength, even during a later or its last processing step, it is desirable to have an austenite content which is as high as possible at any stage of the processing.
  • an oxide layer is formed on the surface of the hot-rolled strip.
  • the hot-rolled strip has to be pickled to remove this oxide layer before cold-rolling to the final thickness. After pickling, the strip is cold- rolled to the final thickness. In the conventional cold-rolling process the resulting cold-rolled strip becomes heavily deformed.
  • the strip Prior to coating in a hot-dip coating process, the strip must be annealed to promote recrystallisation of the cold deformed microstructure to restore the formability of the steel.
  • the strip is subjected to a cold rolling reduction (CCR) or temper rolling reduction (TRR) between hot-rolling and coating and/or after coating.
  • CCR cold rolling reduction
  • TRR temper rolling reduction
  • This CRR or TRR is at most 20% and the cold rolling reduction or temper rolling reduction is the only cold-rolling step between hot-rolling and coating and/or after coating of the strip.
  • TRR will be used to indicate the reduction in the cold rolling or temper-rolling reduction.
  • Temper rolling is a cold rolling process.
  • temper rolling treatment with the express and sole purpose of shape correction only is not considered to be a cold-rolling step in this respect because it does not necessitate the annealing to recrystallise the heavily deformed cold-rolled microstructure.
  • Temper rolling treatments with the sole purpose of removing the yield point elongation are not used for these types of steel.
  • the term temper rolling is used as an equivalent to cold rolling to a degree of reduction that does not require an annealing treatment afterwards prior to the use of the steel in a forming operation and that is not used with the express and sole purpose of shape correction only.
  • the strip may be cold reduced after coating when the steel is pressed, press-formed, deep-drawn or formed into a part for application in e.g. a car.
  • the deformation induced by these forming presses are not to be regarded as a TRR.
  • the temper rolling reduction of 20% is considered to be the aggregate cold rolling reduction between the end of the hot-rolling step and the use of the steel strip in a subsequent production process such as pressing or stamping a part from a blank cut from the steel strip.
  • the deformation of the steel by the use is not considered part of said aggregate cold rolling reduction.
  • the metallic coating may be provided by means of a hot-dip coating step, an electro-coating step, a physical vapour deposition step or a chemical vapour deposition step, optionally followed by a heat treatment such as galvannealing after a hot-dip galvanising step.
  • the metallic coating layer has a thickness of at least 1 ⁇ m.
  • the coating step is performed after the cold rolling reduction and there is no annealing step and/or no pickling step between the cold rolling step and the coating step.
  • the strip is not cold-rolled to a degree that it is necessary to anneal the strip because an adequate deformation potential is still available as a result of the TW IP-properties. Consequently, because of the absence of the annealing step the formation of the manganese-oxide particles on the surface of the strip is prevented. A second pickling prior to hot dip coating to remove these particles is thus avoided, thereby significantly reducing the production costs of the coated steel and the risk of rejection.
  • the hot-rolled strip is coiled after rolling and uncoiled before pickling, but the invention also relates to a direct link between hot-rolling and pickling immediately followed by coating, thus saving a coiling and uncoiling step and potentially a cooling and reheating step e.g. in case of a hot-dip coating step.
  • the maximum aggregate cold rolling reduction (or temper-rolling reduction) to be used in accordance with this invention is 20%.
  • the aggregate cold rolling reduction is defined as the total cold rolling reduction between the end of the hot-rolling step and the use of the steel strip in a subsequent process such as blanking, forming, joining, etc. At this reduction the yield strength and to a lesser extent the tensile strength have increased considerably, but the ductility of the cold rolled product is still adequate for many forming purposes.
  • the maximum TRR is at most 10%, more preferably 8% or even 6%.
  • a suitable minimum value for the TRR is 0.5%, preferably 1 % or even 2%.
  • the TRR is between 1 and 4%.
  • This level of TRR also allows correction of the shape of the hot-rolled strip, and is preferably performed after the coating step, although it is also possible to perform the TR after pickling and prior to coating.
  • a minimum TRR of at least 5% is desirable.
  • a suitable minimum value in that case is 8% or even 10%.
  • Cold-rolling in the context of this invention is defined as rolling while the material to be rolled has an absolute temperature T(K) of at most half the absolute solidus temperature of the steel.
  • T(K) the absolute temperature of TWIP steels
  • a suitable maximum temperature of the material to be rolled is at most 400 0 C, and preferably at most 200 0 C.
  • Starting the cold rolling process with a material at ambient temperature causes a temperature increase of the material during cold rolling due to the deformation of the material. As said, this temperature increase should not result in a temperature of the material over 400 0 C or preferably not over 200 0 C.
  • the coated TWIP-steel sheet is used as a replacement for cold-rolled, annealed and coated steel sheet.
  • the thickness of the hot-rolled product needs to be small enough.
  • the method as described hereinabove is particularly suitable to provide these thin hot-rolled strips with homogeneous properties without the enlarged risk of rejection due to lift-off of the heads of these strips.
  • Said strip may be subjected to an uniform cold rolling reduction wherein the aggregate cold rolling reduction between the end of the hot-rolling step and the use of the steel strip is at most 20%.
  • At least one part of the hot-rolled TWIP steel is subjected to a cold reduction which is different from the other parts of the hot rolled TWIP steel so as to achieve a different local thickness and/or different local mechanical properties.
  • the cold reduced microstructure brought about by an aggregate cold rolling reduction of at most 20% between the end of the hot-rolling step and the use of the steel strip.
  • the cold reduction may be performed by a cold rolling step which is able to impose different cold reductions over length and/or width of the rolled product.
  • the rolled product may be a strip, plate or sheet of steel. From this product blanks may be produced which can e.g. be used for a stamping or pressing operation.
  • the cold reduction is a step in the production of a tailor- rolled blank, and wherein the cold reduction of the various parts of the TRB is chosen such that in the cold-reduced part or parts of the TRB the desired values of mechanical properties are obtained.
  • a steel product having an initial set of mechanical properties, is subjected to a rolling process allowing to change the degree of reduction over the length of the strip (laterally) and/or over the width of the strip (longitudinally).
  • the degrees of reduction are chosen such so as to produce the TRB having the desired geometrical properties, but more importantly, to have the desired mechanical properties in each part of the TRB.
  • Parts which have been subjected to a higher degree of cold reduction will possess a higher yield strength than the parts which have not been cold deformed to a smaller or no extent.
  • the parts undergoing small reductions still have a large formability potential and can be used on the location where the TRB will be subjected to a large deformation during the production of the finished part .
  • each cold reduced microstructure was brought about by an aggregate cold rolling reduction of at most 20% between the end of the hot-rolling step and the use of the steel strip.
  • the metal coating is a conventional zinc or zinc alloy coating provided by hot dip coating or electro-coating.
  • the metal coating is a Mg-Zn alloy coating layer, wherein the zinc alloy consists of 0.3 - 4.0 %Mg and 0.05 - 6.0 % Al, optionally at most 0.2 % of one or more additional elements, unavoidable impurities and the remainder being zinc.
  • the aluminium content is limited to 6%, because above 6% the weldability is impaired. If only one additional element is added, the maximum amount is 0.2%. If two or more additional elements are added, the maximum sum of the amounts of these additional elements is 0.2%.
  • the Mg-Zn alloy comprises 0.3 - 2.3 weight % magnesium and 0.6 - 2.3 weight % aluminium more preferably wherein the zinc alloy contains 1.6 - 2.3 weight % magnesium and 1.6 - 2.3 weight % aluminium.
  • these Mg-Zn alloy coatings performed well and showed good adherence and corrosion properties throughout. These coatings have a relatively high melting point which reduces the risk of the coating to melting, flowing and fouling the hot forming tools during the heat treatment. This means that the shaped product is likely to maintain a high form and surface quality individually over the course of a production series.
  • the magnesium containing zinc alloy coating layer provides lubrication during the thermomechanical shaping step.
  • the elements of the Mg-Zn alloy coating layer diffused into the steel substrate during the prolonged exposure to heat when the coated steel material was heated prior to hot forming, thereby resulting in a diffusion coating, whilst the magnesium and aluminium are oxidised.
  • This diffusion coating already provides the steel substrate with corrosion protection, whereas it is also believed to promote the adhesion of the zinc alloy coating layer to the steel substrate.
  • the thickness of the Zn-diffusion layer should be chosen such that active corrosion protection after the forming and cooling step is achieved.
  • the coating provides excellent crack closure of any cracks formed in the coating during forming, good resistance against abrasion during forming and providing good corrosion resistance prior to, during and after the thermomechanical operation, including protection of the edges of the part due to the galvanic behaviour of zinc with steel.
  • An additional element that could be added in a small amount to the Mg-Zn layers, less than 0.2 weight %, could be Pb or Sb, Ti, Ca, Mn, Sn, La, Ce, Cr, Ni, Zr or Bi. Pb, Sn, Bi and Sb are usually added to form spangles. These small amounts of an additional element do not alter the properties of the coating nor the bath to any significant extent for the usual applications.
  • the amount of zinc alloy on one side of the steel strip should be between 25 and 600 g/rn 2 . This corresponds to a thickness of between about 4 and 95 ⁇ m. Preferably the thickness is between 4 and 20 ⁇ m (50-140 g/m 2 ) because thicker coatings are not necessary for most applications.
  • the zinc alloy coating layer according to the invention improves the protection against corrosion at a thickness of at most 12 ⁇ m.
  • a thinner coating layer is beneficial for welding together two sheets of steel with the coating layer according to the invention, for instance by laser welding.
  • the zinc alloy coating layer has a thickness of 3 - 10 ⁇ m, this being a preferred thickness range for automotive applications.
  • the zinc alloy coating layer has a thickness of 3 - 8 ⁇ m or even 7 ⁇ m.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Rolling (AREA)

Abstract

Cette invention porte sur un procédé pour la fabrication d'une bande d'acier à plasticité induite par maclage, selon lequel de l'acier fondu est coulé dans une machine à coulée continue avec une ou plusieurs barres pour former une brame ayant une épaisseur d'au moins 30 mm et au plus 120 mm et, tout en utilisant la chaleur de coulée, est transporté à travers un four, et laminé à chaud dans un laminoir à chaud comprenant une ou plusieurs cages de laminage en une bande d'acier d'une épaisseur finale désirée (hf), i) dans un traitement de laminage sans fin dans lequel, a) il y a une liaison de matériau entre l'acier dans la machine de coulée continue, dans le four et dans le laminoir à chaud et la zone de refroidissement forcé facultatif, ou b) des brames d'une pluralité de barres sont reliées de façon à former une brame continue, permettant ainsi d'obtenir une liaison de matériau entre l'acier dans le four, le laminoir à chaud et la zone de refroidissement forcé facultatif ; ou ii) dans un traitement de laminage semi-sans fin, dans lequel il y a une liaison de matériau entre l'acier dans le four, le laminoir à chaud et la zone de refroidissement forcé facultatif, et dans lequel la bande, après le laminage sans fin ou semi-sans fin et après le refroidissement forcé facultatif, est découpée en des parties de la longueur désirée qui sont ultérieurement bobinées.
PCT/EP2009/000633 2008-01-30 2009-01-30 Procédé de production d'un acier à plasticité induite par maclage, laminé à chaud, et produit en acier à plasticité induite par maclage produit à l'aide du procédé Ceased WO2009095264A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
EP09705515.6A EP2257394B1 (fr) 2008-01-30 2009-01-30 Procédé de fabrication d'un acier twip laminé à chaud et acier twip laminé à chaud fabriqué selon ce procédé
ES09705515T ES2705203T3 (es) 2008-01-30 2009-01-30 Método para producir un acero TWIP laminado en caliente y un producto de acero TWIP producido de ese modo
KR1020167007883A KR20160039304A (ko) 2008-01-30 2009-01-30 열간-압연 ｔｗｉｐ-강의 제조 방법 및 이에 의해 제조된 ｔｗｉｐ-강 제품

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP08101119.9 2008-01-30
EP08101119 2008-01-30

Publications (1)

Publication Number Publication Date
WO2009095264A1 true WO2009095264A1 (fr) 2009-08-06

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PCT/EP2009/000633 Ceased WO2009095264A1 (fr) 2008-01-30 2009-01-30 Procédé de production d'un acier à plasticité induite par maclage, laminé à chaud, et produit en acier à plasticité induite par maclage produit à l'aide du procédé

Country Status (5)

Country Link
EP (1) EP2257394B1 (fr)
KR (2) KR20100108610A (fr)
ES (1) ES2705203T3 (fr)
TR (1) TR201900039T4 (fr)
WO (1) WO2009095264A1 (fr)

Cited By (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2011154153A1 (fr) * 2010-06-10 2011-12-15 Tata Steel Ijmuiden Bv Procédé de production d'acier austénitique
CN101898200B (zh) * 2009-12-16 2012-11-14 安徽工业大学 锌锭直接轧制方法
EP2531308A2 (fr) * 2010-02-03 2012-12-12 ThyssenKrupp Steel Europe AG Bande métallique ayant une epaisseur constantes présentant des différentes propriétés mécaniques
JP2013510727A (ja) * 2009-11-16 2013-03-28 ジョンソン コントロールズ テクノロジー カンパニー Ｔｗｉｐ鋼と低炭素鋼とをレーザ溶接する方法
CN104532137A (zh) * 2014-12-23 2015-04-22 福建工程学院 钼铬合金化的高强度高塑性高碳twip钢及其制备方法
WO2015117696A1 (fr) * 2014-02-07 2015-08-13 Primetals Technologies Austria GmbH Procédé de formation d'ébauches de coulée sur mesure
CN105441796A (zh) * 2014-09-26 2016-03-30 鞍钢股份有限公司 具有高强塑积twip钢及其制备方法
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EP2257394A1 (fr) 2010-12-08
KR20160039304A (ko) 2016-04-08

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