EP2768989A1 - Acier en bandes galvanisé à chaud à haute résistance - Google Patents

Acier en bandes galvanisé à chaud à haute résistance

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Publication number
EP2768989A1
EP2768989A1 EP20120759372 EP12759372A EP2768989A1 EP 2768989 A1 EP2768989 A1 EP 2768989A1 EP 20120759372 EP20120759372 EP 20120759372 EP 12759372 A EP12759372 A EP 12759372A EP 2768989 A1 EP2768989 A1 EP 2768989A1
Authority
EP
European Patent Office
Prior art keywords
steel strip
max
hot dip
dip galvanised
mpa
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.)
Granted
Application number
EP20120759372
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German (de)
English (en)
Other versions
EP2768989B1 (fr
Inventor
Bernard Leo Ennis
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Tata Steel Ijmuiden BV
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Tata Steel Ijmuiden BV
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Priority to EP12759372.1A priority Critical patent/EP2768989B1/fr
Publication of EP2768989A1 publication Critical patent/EP2768989A1/fr
Application granted granted Critical
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Active legal-status Critical Current
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Classifications

    • 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
    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the invention relates to a high strength hot dip galvanised steel strip having improved formability, such as used in the automotive industry.
  • Such steel types are known and have been developed under the name of dual phase steel types. Such steel types do not provide the required formability as required in many applications for the automotive industry. For this reason, TRIP assisted dual phase steel types have been developed.
  • EP 1 889 935 Al A document describing such steel types is EP 1 889 935 Al .
  • This document describes a high strength hot dip galvanised steel sheet containing (in mass percent) 0.05 - 0.3 % C
  • TRIP assisted dual phase steel strip Formability, however, is not the only requirement for a TRIP assisted dual phase steel strip.
  • the alloying elements should be low in amount to make the cost of the steel as low as possible, it should be as easy as possible to produce the steel strip and to coat it, the steel strip has to have high strength, good weldability and should also exhibit a good surface quality. These requirements are especially important for industrially produced TRIP assisted dual phase steel types, which have to be formed into for instance automotive parts that will be spot welded into a body in white.
  • the balance being Fe and inevitable impurities
  • the inventors have found that by a careful selection of the amounts of the main constituting elements of the steel, being carbon, manganese, silicon, aluminium and chromium, a high strength hot dip galvanised steel strip can be produced that has the required formability, processability, strength and elongation, while at the same time providing a sufficient weldability, coatability and surface quality. It has been found by the inventors that none of the examples given in the state of the art provide all these requirements at the same time.
  • Si is traditionally used to effectuate the TRIP effect, due to retardation of carbide formation in the presence of Si which leads to carbon enrichment and, hence, stabilisation of austenite at room temperature.
  • the disadvantages of Si are that in very high quantities (above 0.4 wt. %) it interferes with the wettability of zinc, making galvanisation over tradition continuous annealing lines impossible. It has also been shown in EP 1 889 935 Al that Si can be replaced by relatively high quantities of Al.
  • the present invention shows that the addition of Si can be omitted and Al kept to a minimum by careful selection of the Cr content and with the addition of Nb.
  • composition of the steel strip according to the invention is such that the formability of the steel is good and no necking occurs, and that the edge ductility of pressed parts is such that no cracking occurs.
  • the reason for the amounts of the main constituting elements is as follows.
  • C 0.13 - 0.19 mass %.
  • Carbon has to be present in an amount that is high enough to ensure hardenability and the formation of martensite at the cooling rates available in a conventional annealing/galvanising line. Martensite is required to deliver adequate strength. Free carbon also enables stabilisation of austenite which delivers improved work hardening potential and good formability for the resulting strength level. A lower limit of 0.13 mass % is desired for these reasons. A maximum level of 0.19 mass % has been found to be essential to ensure good weldability. Mn: 1.70 - 2.50 mass %. Manganese is added to increase hardenability thus making the formation of martensite easier within the cooling rate capability of a conventional continuous annealing/galvanising line.
  • Manganese also contributes to the solid solution strengthening which increases the tensile strength and strengthens the ferrite phase, thus helping to stabilise retained austenite.
  • Manganese lowers the transformation temperature range of the dual phase steel, thus lowering the required annealing temperature to levels that can be readily attained in a conventional continuous annealing/galvanising line.
  • a lower limit of 1.70 mass % is needed for the above reasons.
  • a maximum level of 2.50 mass % is imposed to ensure acceptable rolling forces in the hot mill and to ensure acceptable rolling forces in the cold mill by ensuring sufficient transformation of the dual phase steel to soft transformation products (ferrite and pearlite). This maximum level is also given in view of the stronger segregation during casting and the forming of a band of martensite in the strip at higher values.
  • Al 0.40 - 1.00 mass %. Aluminium is added to liquid steel for the purpose of de- oxidation. In the right quantity it also provides an acceleration of the bainite transformation, thus enabling bainite formation within the time constraints imposed by the annealing section of a conventional continuous annealing/galvanising line. Aluminium also retards the formation of carbides thus keeping carbon in solution thus causing partitioning to austenite during overaging, and promoting the stabilisation of austenite. A lower level of 0.40 mass % is required for the above reasons. A maximum level of 1.00 mass % is imposed for castability, since high aluminium contents lead to poisoning of the casting mould slag and consequently an increase in mould slag viscosity, leading to incorrect heat transfer and lubrication during casting.
  • Cr 0.05 - 0.25 mass %. Chrome is added to increase hardenability. Chrome forms ferrite and suppresses the formation of carbides, thus enhancing the forming of retained austenite. A lower level of 0.05 mass % is required for the above reasons. A maximum level of 0.25 mass % is imposed to ensure satisfactory pickling of the steel strip, and to keep the cost of the strip sufficiently low.
  • Ca max 0.004 mass %.
  • the addition of calcium modifies the morphology of manganese sulphide inclusions. When calcium is added the inclusions get a globular rather than an elongated shape. Elongated inclusions, also called stringers, may act as planes of weakness along which lamellar tearing and delamination fracture can occur. The avoidance of stringers is beneficial for forming processes of steel sheets which entail the expansion of holes or the stretching of flanges and promotes isotropic forming behaviour.
  • Calcium treatment also prevents the formation of hard, angular, abrasive alumina inclusions in aluminium deoxidised steel types, forming instead calcium aluminate inclusions which are softer and globular at rolling temperatures, thereby improving the material's processing characteristics.
  • some inclusions occurring in molten steel have a tendency to block the nozzle, resulting in lost output and increased costs.
  • Calcium treatment reduces the propensity for blockage by promoting the formation of low melting point species which will not clog the caster nozzles.
  • P max 0.10 mass %. Phosphorus interferes with the formation of carbides, and therefore some phosphorus in the steel is advantageous. However, phosphorus can make steel brittle upon welding, so the amount of phosphorus should be carefully controlled, especially in combination with other embrittling elements such as sulphur and nitrogen.
  • Niobium is added in an amount between 0.01 and 0.05 mass % for grain refinement and formability. Niobium promotes transformation on the runout table and thus provides a softer and more homogeneous intermediate product. Niobium further suppresses formation of martensite at isothermal overaging temperatures, thereby promoting stabilisation of retained austenite.
  • the optional elements are mainly added to strengthen the steel.
  • the ranges for aluminium, chromium and manganese are chosen such that a correct balance is found to deliver complete transformation on the runout table to ensure a steel strip that can be cold rolled, and to provide a starting structure enabling rapid dissolution of carbon in the annealing line to promote hardenability and correct ferritic/bainitic transformation behaviour.
  • aluminium accelerates and chromium decelerates the bainitic transformation
  • the right balance between aluminium and chromium has to be present to produce the right quantity of bainite within the timescales permitted by a conventional hot dip galvanising line with a restricted overage section.
  • the relative amounts of certain elements are of importance.
  • Aluminium and silicon together should be maintained between 0.4 and 1.05 mass % to ensure suppression of carbides in the end product and stabilisation of a sufficient amount of austenite, with the correct composition, to provide a desirable extension of formability.
  • Manganese and chromium together should be above 1.90 mass % to ensure sufficient hardenability for formation of martensite and thus achievement of strength in a conventional continuous annealing line and hot dip galvanising line.
  • element C is present in an amount of 0.13 - 0.16 %. In this range the hardenability of the steel is optimal while the weldability of the steel is enhanced.
  • element Mn is present in an amount of 1.95
  • a higher amount of manganese provides steel with a higher strength, so it is advantageous to raise the lower limit to 1.95 or even 2.00 mass % manganese.
  • hot rolling and cold rolling of the steel is more difficult for higher amounts of manganese, so it is advantageous to lower the upper limit to 2.40, 2.30 or even 2.20 mass % manganese.
  • element Si is present in an amount of 0.05 - 0.15 %.
  • Si ensures a better retardation of carbides during overaging which is advantageous for the formability of the steel.
  • element Al is present in an amount of 0.60
  • a raised lower level of aluminium has the same effect as a higher amount of silicon, but also improves the bainite formation.
  • a lower upper limit of aluminium improves the castability of the steel.
  • element Cr is present in an amount of 0.10 - 0.25 %.
  • a raised lower level increases the hardenability of the steel.
  • element Nb is present in an amount of 0.01
  • niobium improves the homogeneity of the intermediate product.
  • the upper limit is mainly in consideration of the cost of niobium.
  • the steel has an ultimate tensile strength Rm of at least 700 MPa, more preferably an ultimate tensile strength Rm of at least 750 MPa.
  • This strength can, due to the careful selection of the amounts of the elements present in the steel, be reached while the formability of a conventional 600 MPa dual phase steel is maintained.
  • the hot dip galvanised steel strip has an 0.2 % proof strength Rp of at least 400 MPa, preferably an 0.2 % proof strength Rp of at least 450 MPa. Also this strength can be reached due to the careful selection of the amounts of the elements present in the steel.
  • the hot dip galvanised steel strip has a total elongation of at least 18 %. This is a high elongation which is also reached by the chosen presence of the elements in the steel.
  • the hot dip galvanised steel strip has a hole expansion coefficient of at least 35 % when Rm is 750 MPa and Rp is 450 MPa. This is a good hole expansion coefficient, as will be elucidated below. The hole expansion coefficient decreases with increasing strength.
  • the hot dip galvanised steel strip has an Erichsen cupping index of more than 10.5 mm when Rm is 750 MPa and Rp is 450 MPa. This is satisfactory for the usability of the steel.
  • the Erichsen cupping index decreases with increasing strength.
  • the hot dip galvanised steel strip has a dual phase structure containing 8 - 12 % retained austenite, 10 - 20 % martensite, the remainder being a mixture of ferrite and bainite, preferably the hot dip galvanised steel strip containing not more than 10 % bainite. With such microstructures, a high elongation and a high strength will be reached.
  • the hot dip galvanised steel strip has an average grain size of at most 5 ⁇ . This small grain size helps to achieve the above mentioned mechanical properties of the steel.
  • a method for producing a high strength hot dip galvanised steel strip as defined above, wherein the cast steel is hot rolled and cold rolled to a strip having a desired thickness, after which the strip is reheated in an annealing line to a temperature above the Acl temperature and preferably between the Acl and the Ac3 temperature of the steel type and fast cooled at a cooling rate such as to avoid retransformation to ferrite, after which isothermal overaging is applied to form bainite, and the strip is hot dip galvanised.
  • the deformation schedule during hot rolling, the finish rolling temperature and the subsequent cooling pattern on a run-out table can be selected to achieve a microstructure in the hot rolled product which is conducive to further reduction of thickness in the cold mill.
  • the temperature in the annealing line can be chosen such that the steel strip comprises both ferrite and austenite.
  • the cooling rate should be such that in principle no ferrite is formed, and the isothermal overaging is applied to promote the formation of bainite.
  • Hot dip galvanising can be performed in the usual manner. During this method the temperature and duration of most steps is critical for the realisation of the desired balance between strength and ductility in the final product.
  • the annealing will be carried out a temperature between 750°C and 850°C and more preferably at a temperature between 780°C and 820°C. At these temperatures the steel strip comprises both ferrite and austenite.
  • the overaging is applied at a temperature between 360°C and 480°C.
  • the iron-carbon eutectoid system has a number of critical transformation temperatures as defined below. These temperatures are dependent on chemistry and processing conditions:
  • A2 - Curie temperature temperature above which the material ceases to be magnetic
  • the suffixes c and r denote transformations in the heating and cooling cycle respectively.
  • the invention will be elucidated hereinafter; a number of compositions will be evaluated with regard to some well-known formability parameters that are elucidated first.
  • n-value The work hardening coefficient or n- value is closely related to uniform elongation. In most sheet forming processes the limit of formability is determined by the resistance to local thinning or "necking". In uniaxial tensile testing necking commences at the extent of uniform elongation, n-value and uniform elongation derived from the tensile test can be taken as a measure of the formability of sheet steels. When aiming to improve formability of strip steels n-value and uniform elongation represent the most suitable optimisation parameters.
  • Hole expansion coefficient To be successfully applied in industrial stamping operations, sheet metals must have a certain ability to withstand stretching of their sheared edges. This is tested in accordance with the international technical specification ISO/TS 16630. A hole having a diameter of 10mm is made in the centre of a test piece having the dimensions 90 x 90mm. A cone punch of 40mm diameter with a 60° apex is forced into the hole while the piece is fixed with a die having an inner diameter of 55mm. The diameter of the hole is measured when a crack had extended through the thickness of the test piece.
  • Max HEC % ((Dh - Do)/Do) x 100, wherein Do is the original hole diameter and Dh is the diameter of the hole after cracking. Stretch flangeability is evaluated on the basis of the maximum HEC and is deemed satisfactory when HEC > 25%
  • EI Erichsen Index
  • ISO 20482:2003 The Erichsen test describes the ability of metals to undergo plastic deformation in stretch forming and is tested in accordance with the international standard test ISO 20482:2003.
  • a hemispherical punch is driven into a fully clamped sheet.
  • As lubrication graphite grease is used on top of the punch.
  • the punch travel is stopped when a through thickness crack is detected. Due to friction the fracture is not on top of the punch but to the side, so not in equi bi-axial strain but more towards plane strain.
  • the depth of the punch penetration is measured.
  • the value of the Erichsen cupping index (IE) is the average of a minimum of three individual measurements, expressed in millimetres and for the present invention is deemed satisfactory when EI > 10mm.
  • Weldability Resistance spot welding is the major joining technique used in the automotive industry, with an average car containing around 2000 - 3000 spot welds. Traditionally spot welds have always been a very cheap and reliable joint type, however since the introduction of AHSS, this reliability has been compromised. The weldability is measured by the ability of the material to be spot-welded. Welding conditions were taken from BS 1 140: 1993 which are standard for industry, although not necessarily optimised for AHSS. Spot-weldability is measured by the failure mode of the resultant spot- weld (plug). When a material cannot be welded then the plug will split along the interface between the two joining surfaces.
  • the failure will be in the parent metal, outside of the plug and preferably also outside the heat-affected zone. This is known as full-plug failure, that is the full plug is pulled out of the parent metal. Spot-weldability can be expressed on the scale between full-interface failure and full-plug failure with the former being deemed un-weldable.
  • One of the aims of the present invention is to provide a high strength hot dip galvanised steel strip that has a formability in the range of a 600MPa AHSS hot dip galvanised steel strip, but having a strength level of at least 700 MPa. This is achieved by realising a suitable increase in the uniform elongation and n-value.
  • Table 1 shows six different alloys A to F, of which alloys B, C and F have a composition according to the invention and alloys A, D and E are comparative examples.
  • alloys A, D and E processing conditions according to the invention have been applied as shown in Table 2.
  • the mechanical properties of the alloys A and E are clearly outside the values as desired for according to the invention, because for alloy A the Rp value is below 400 MPa, and for alloy E the hole expansion coefficient is only 25% and the Erichsen cupping index is less than 10.
  • Alloy D has a composition according to the invention, but the Si level is too high.
  • Table 2 shows that the mechanical properties as measured fall within the values as desired for according to the invention, though the Rm value is only just above the lower limit of 700 MPa, and clearly lower than the preferred value of at least 750 MPa.
  • the structure of alloy D is not in accordance with the desired structure, because the amount of martensite and retained austenite is too low.
  • Alloy B is an alloy according to the invention.
  • different processing conditions have been applied as shown in Table 2.
  • Different annealing temperatures and different isothermal holding temperatures result in mechanical properties that fulfil the desired values according to the invention as regards the ultimate tensile strength and the 0.2% proof strength, though desired total elongation is not always met. This occurs when the overaging temperature is above the optimum bainite holding temperature (i.e. above 480°C), thus reducing the amount of retained austenite available.
  • Alloy C is also an alloy according to the invention.
  • this alloy two different processing conditions have been applied as shown in Table 2.
  • the ultimate tensile strength Pan is more than 750 MPa and the total elongation is more than 18 %.
  • the Erichsen Index is more than 10, the n-value is 0.17 and the HEC is above 30.
  • Alloy F is another alloy according to the invention. Three different processing conditions have been applied, as shown in Table 2, and in all three cases the ultimate tensile strength is more than 750 MPa, the total elongation is even more than 19 %, and the n-value is 0.15 or more. Where measured, the Erichsen Index is more than 10 and the HEC is above 30.
  • Hole expansion coefficient HEC and Erichsen cupping index EI are not always measured but where measured the value is satisfactory. Also the work hardening coefficient or n-value is good in all cases.
  • the TRIP assisted dual phase steel according to the invention with low amounts of silicon thus shows to be a steel type that gives satisfactory mechanical properties, contrary to the expectation by the person skilled in the art that a certain amount of added silicon is always needed.

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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)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Coating With Molten Metal (AREA)

Abstract

L'invention se rapporte à un acier en bandes galvanisé à chaud à haute résistance qui se compose, en pourcentage en masse, des éléments suivants : le carbone (C) en une quantité comprise entre 0,13 et 0,19 % ; le manganèse (Mn) en une quantité comprise entre 1,70 et 2,50 % ; le silicium (Si) en une quantité maximale de 0,15 % ; l'aluminium (Al) en une quantité comprise entre 0,40 et 1,00 % ; le chrome (Cr) en une quantité comprise entre 0,05 et 0,25 % ; le niobium (Nb) en une quantité comprise entre 0,01 et 0,05 % ; le phosphore (P) en une quantité maximale de 0,10 % ; le calcium (Ca) en une quantité maximale de 0,004 % ; le soufre (S) en une quantité maximale de 0,05 % ; l'azote (N) en une quantité maximale de 0,007 % et facultativement au moins l'un des éléments suivants : le titane (Ti) en une quantité maximale de 0,50 % ; le vanadium (V) en une quantité maximale de 0,40 % ; le molybdène (Mo) en une quantité maximale de 0,50 % ; le nickel (Ni) en une quantité maximale de 0,50 % ; le cuivre (Cu) en une quantité maximale de 0,50 % ; le bore (B) en une quantité maximale de 0,005 %, le reste étant du fer (Fe) et des impuretés inévitables, et 0,40 % < Al + Si < 1,05 % et Mn + Cr > 1,90 %. Cet acier présente une meilleure aptitude à la déformation à une résistance élevée, une bonne soudabilité et une bonne qualité de surface ainsi qu'une bonne aptitude à la production et au revêtement.
EP12759372.1A 2011-09-13 2012-09-12 Acier en bandes galvanisé à chaud à haute résistance Active EP2768989B1 (fr)

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Application Number Priority Date Filing Date Title
EP12759372.1A EP2768989B1 (fr) 2011-09-13 2012-09-12 Acier en bandes galvanisé à chaud à haute résistance

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP11007431 2011-09-13
EP12759372.1A EP2768989B1 (fr) 2011-09-13 2012-09-12 Acier en bandes galvanisé à chaud à haute résistance
PCT/EP2012/003823 WO2013037485A1 (fr) 2011-09-13 2012-09-12 Acier en bandes galvanisé à chaud à haute résistance

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EP2768989A1 true EP2768989A1 (fr) 2014-08-27
EP2768989B1 EP2768989B1 (fr) 2015-11-18

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US (1) US20140205858A1 (fr)
EP (1) EP2768989B1 (fr)
JP (1) JP2014531511A (fr)
KR (1) KR20140068186A (fr)
CN (1) CN103857808B (fr)
BR (1) BR112014005641A2 (fr)
CA (1) CA2848161A1 (fr)
ES (1) ES2562478T3 (fr)
IN (1) IN2014CN02734A (fr)
MX (1) MX2014002922A (fr)
PT (1) PT2768989E (fr)
WO (1) WO2013037485A1 (fr)
ZA (1) ZA201402590B (fr)

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WO2020245678A1 (fr) 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
WO2020245626A1 (fr) 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
WO2021123880A1 (fr) * 2019-12-18 2021-06-24 Arcelormittal Tôle d'acier laminée à froid et recuite et son procédé de fabrication
WO2023281035A1 (fr) * 2021-07-07 2023-01-12 Tata Steel Ijmuiden B.V. Bande d'acier à deux phases revêtue à haute résistance et son procédé de production

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ES2625754T3 (es) * 2013-03-11 2017-07-20 Tata Steel Ijmuiden Bv Fleje de acero de fase compleja galvanizado por inmersión en caliente de alta resistencia
DE102014017274A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Höchstfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
JP2018524471A (ja) * 2015-07-01 2018-08-30 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ 高強度溶融亜鉛めっき鋼帯
KR20180095536A (ko) 2015-12-15 2018-08-27 타타 스틸 이즈무이덴 베.뷔. 고강도 용융 아연도금 강 스트립
WO2018157136A1 (fr) * 2017-02-27 2018-08-30 Nucor Corporation Traitement thermique pour affinage de grain d'austénite
WO2018220430A1 (fr) * 2017-06-02 2018-12-06 Arcelormittal Tôle d'acier destinée à la fabrication de pièces trempées à la presse, pièce trempée à la presse présentant une association de résistance élevée et de ductilité d'impact, et procédés de fabrication de cette dernière
DE102021121997A1 (de) 2021-08-25 2023-03-02 Thyssenkrupp Steel Europe Ag Kaltgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung
CN115537665A (zh) * 2022-10-14 2022-12-30 山东钢铁集团日照有限公司 一种可用相同原料生产连退、镀锌两类590MPa级DH钢的生产方法

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JPH01127623A (ja) 1987-11-09 1989-05-19 Sumitomo Metal Ind Ltd 加工性と耐食性の良好な高強度鋼板の製造法
US20090211668A1 (en) 2005-04-20 2009-08-27 Nippon Steel Corporation Method for producing high-strength hot-dip galvannealed steel sheet
JP2010132975A (ja) 2008-12-05 2010-06-17 Jfe Steel Corp 高強度溶融亜鉛めっき鋼板及び高強度合金化溶融亜鉛めっき鋼板の製造方法
JP2010255100A (ja) 2009-03-31 2010-11-11 Jfe Steel Corp 高強度溶融亜鉛めっき鋼板およびその製造方法
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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2020245678A1 (fr) 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
WO2020245626A1 (fr) 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
WO2020245627A1 (fr) 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
WO2020245668A1 (fr) 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
WO2021123880A1 (fr) * 2019-12-18 2021-06-24 Arcelormittal Tôle d'acier laminée à froid et recuite et son procédé de fabrication
WO2023281035A1 (fr) * 2021-07-07 2023-01-12 Tata Steel Ijmuiden B.V. Bande d'acier à deux phases revêtue à haute résistance et son procédé de production

Also Published As

Publication number Publication date
ZA201402590B (en) 2015-07-29
CN103857808A (zh) 2014-06-11
PT2768989E (pt) 2016-03-18
ES2562478T3 (es) 2016-03-04
BR112014005641A2 (pt) 2017-03-28
IN2014CN02734A (fr) 2015-07-03
JP2014531511A (ja) 2014-11-27
US20140205858A1 (en) 2014-07-24
CA2848161A1 (fr) 2013-03-21
EP2768989B1 (fr) 2015-11-18
KR20140068186A (ko) 2014-06-05
CN103857808B (zh) 2016-11-23
WO2013037485A1 (fr) 2013-03-21
MX2014002922A (es) 2014-05-21

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