EP4301885A1 - Produit plat en acier, son procédé de production, et utilisation d'un tel produit plat en acier - Google Patents

Produit plat en acier, son procédé de production, et utilisation d'un tel produit plat en acier

Info

Publication number
EP4301885A1
EP4301885A1 EP22710062.5A EP22710062A EP4301885A1 EP 4301885 A1 EP4301885 A1 EP 4301885A1 EP 22710062 A EP22710062 A EP 22710062A EP 4301885 A1 EP4301885 A1 EP 4301885A1
Authority
EP
European Patent Office
Prior art keywords
flat steel
steel product
cold
temperature
cooling
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.)
Pending
Application number
EP22710062.5A
Other languages
German (de)
English (en)
Inventor
Ekaterina Bocharova
Olga SUKHOPAR
Georg PAUL
Stefan Woestmann
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Steel Europe AG
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 ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Publication of EP4301885A1 publication Critical patent/EP4301885A1/fr
Pending legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
    • C—CHEMISTRY; METALLURGY
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
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    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
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    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0442—Flattening; Dressing; Flexing
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    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0478—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • 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
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    • 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

Definitions

  • the invention relates to a cold-rolled flat steel product, a method for its production and uses of a flat steel product according to the invention.
  • “Flat steel products” are understood here to mean rolled products whose length and width are significantly greater than their thickness. These include in particular steel strips, steel sheets and blanks obtained from them, such as blanks and the like.
  • EP 2031 081 B1 discloses a cold-rolled flat steel product which can be hot-dip coated with a zinc-based anti-corrosion coating and has a structure which consists of 20-70% martensite, up to 8% retained austenite and the remainder ferrite and/or or bainite.
  • the steel flat product has a tensile strength of at least 950 MPa and consists of a steel consisting of (in % by weight) C: 0.050 - 0.105%, Si: 0.10 - 0.60%, Mn: 2.10 - 2, 80%, Cr: 0.20 - 0.80%, Ti: 0.02 - 0.10%, B: ⁇ 0.0020%, Mo: ⁇ 0.25%, Al: ⁇ 0.10%, Cu : up to 0.20%, Ni: up to 0.10%, Ca: up to 0.005%, P: up to 0.2%, S: up to 0.01%, N: up to 0.012% and as The rest is composed of iron and unavoidable impurities.
  • Steel concepts of this type are characterized by a low yield strength ratio, which can be attributed to the significant differences in strength of the structural components.
  • a product proposed to solve this problem has at least the features specified in claim 1.
  • a method which enables a product according to the invention to be produced inexpensively is specified in claim 9.
  • Such a product can be provided in the manner specified in claim 8 with an anti-corrosion coating based in particular on zinc (“Zn").
  • the steel substrate of a steel flat product according to the invention is accordingly produced from a steel which, in % by mass, consists of C: 0.040-0.100%, Mn: 2.10-2.50%, Si: 0.10-0.40%, Cr : 0.30 - 0.90%, Ti: 0.020 - 0.080%, B: 0.0005 - 0.0020%, N: 0.003 - 0.010%, Al: up to 0.10%, Ca: up to 0.005% , P: up to 0.025%, S: up to 0.010%, Mo: up to 0.20%, Nb: up to 0.050%, Cu: up to 0.10%, V: up to 0.020%, Ni: up to 0.10% and the remainder consists of iron and unavoidable impurities.
  • the steel substrate of a flat steel product according to the invention has a dual-phase structure consisting of 10-40% by volume of martensite, 30-90% by volume of ferrite including bainitic ferrite, no more than 5% retained austenite and the remainder made up of other structural components that are unavoidable due to production exists, whereby such other structural components are only present if the sum of the contents of the other structural components is less than 100%.
  • a steel flat product according to the invention contains 0.040-0.100% by mass of carbon ("C"). With C contents below 0.040% by mass, the strength would decrease too much.
  • the maximum carbon content of 0.100% by weight provided according to the invention was selected with a view to good weldability of the steel. In addition, carbon contents above 0.100 wt.% would lead to the formation of a harder, carbon-rich martensite phase, thereby significantly increasing the hardness difference between martensite and ferrite.
  • Si Silicon
  • the upper limit of the Si content is 0.40% by mass to avoid grain boundary oxidation, which could adversely affect the coatability and surface properties of the steel.
  • Manganese (“Mn”) in contents of 2.10-2.50% by mass purposefully prevents pearlite from forming in the steel flat product according to the invention during cooling in the annealing line.
  • Mn in the contents determined according to the invention promotes the formation of martensite in the structure and thus contributes significantly to increasing the strength.
  • the loss of strength which would otherwise be expected as a result of the C content set to comparatively low values according to the invention is thus compensated, inter alia, by the Mn contents provided according to the invention.
  • the Mn content is preferably at least 2.20% by mass and at most 2.40% by mass.
  • Aluminum (“AI”) in contents of up to 0.10% by mass is required for deoxidation in steel production.
  • Ca can also be added to the steel of a flat steel product according to the invention in amounts of up to 0.005% by mass in order to deoxidize the steel during steel production. This effect can be reliably achieved by adding at least 0.0005% by mass of Ca.
  • chromium also serves to increase the strength.
  • the upper limit of the range specified according to the invention for the Cr content is limited to at most 0.90% by mass, in particular at most 0.80% by mass.
  • the process for producing the flat steel product according to the invention is to be carried out in such a way that an annealing temperature GT of at least 840° C. is set in order to reliably achieve the desired dual-phase structure and the desired mechanical properties of the flat steel product according to the invention receive.
  • Titanium is provided in the steel of a steel flat product according to the invention in contents of 0.020 - 0.080% by mass in order to also improve the strength through the formation of fine Ti precipitates such as TiC or Ti(C,N) precipitates and to obtain a fine-grained structure.
  • Ti contents of at least 0.030% by mass can be provided.
  • the amount of precipitation made possible by the Ti content provided according to the invention contributes, among other things, to the optimum combination of mechanical properties which characterizes a steel according to the invention.
  • the positive influence of the presence of Ti in the steel of a steel flat product according to the invention can be used particularly effectively with Ti contents of up to 0.07% by mass.
  • the effect of Ti in the steel of a flat steel product according to the invention can also be supported by alloying Ti in an amount that corresponds at most to 11 times the respective N and B content of the steel of a flat steel product according to the invention.
  • B Boron
  • N nitrogen
  • the nitrogen (“N”) content in the steel of a flat steel product according to the invention is limited to 0.010% by mass so that Ti acts as an alloying element in the structure and is not completely bound with N. Contents of at least 0.003% by mass N are intended to ensure a sufficient amount of Ti(C,N) precipitates in the structure.
  • Impurities are permitted in the steel of a flat steel product according to the invention, which are technically unavoidable in a practical, economical production of a flat steel product according to the invention, but are kept so low that they have no negative influence on the desired properties of a flat steel product according to the invention.
  • Impurities include phosphorus (“P”) and sulfur (“S”) levels.
  • P phosphorus
  • S sulfur
  • the content of P is up to 0.025% by mass, in particular less than 0.015% by mass, limited to avoid deterioration of weldability.
  • the S content is limited to a maximum of 0.010% by mass in order to avoid the formation of MnS or (Mn,Fe)S, which would have a negative effect on the ductility of the steel according to the invention.
  • the total content of impurities in the steel of a flat steel product according to the invention is limited to a maximum of 0.5% by mass, with impairment of the properties of the flat steel product being particularly reliably avoided with a maximum total of impurities of 0.3% by mass.
  • Mo molybdenum
  • Nb niobium
  • Cu copper
  • V vanadium
  • Ni nickel
  • the contents of these elements are so limited that they only have a minor influence on the properties of a flat steel product according to the invention. They can therefore also be “0%” in the technical sense, i.e. so small that they are considered impurities and have no effect in the flat steel product according to the invention.
  • a flat steel product consisting of a dual-phase steel which has a tensile strength Rm of 750-940 MPa, a yield point of 440-650 MPa and an elongation at break A80 of more than 13 % and is characterized by particularly good forming properties with a minimized tendency to edge cracks and equally good weldability.
  • the tensile strength Rm, the yield point Rp0.2 and the elongation at break A80 are each determined in accordance with DIN ISO 6892 (longitudinal tensile direction, specimen shape 2).
  • a significant difference between the invention and, for example, the prior art acknowledged at the outset and known from EP 2031 081 B1 consists in the distribution of the hardness values in the martensitic and ferritic phases and in the precipitation state of one of the microstructure of a flat steel product according to the invention, which is characterized by a large quantity of fine excretions.
  • This structural state can be achieved primarily by means of a carbon content which is limited according to the invention and a specific addition of Ti and B amounts. In this way, an above-average robust behavior with increasing strain gradients in the hole expansion test is achieved.
  • the proportions of martensite and ferrite, including bainitic ferrite, in the microstructure of a flat steel product according to the invention are quantified by means of image analysis.
  • the proportion of martensite in the structure of a flat steel product according to the invention is limited to a maximum of 40% by volume, with at least 10% by volume of martensite being present in order to ensure the required strength.
  • the remainder of the microstructure of a flat steel product according to the invention in addition to proportions of no more than 5% by volume residual austenite, is mainly taken up by ferrite including bainitic ferrite, which must be no more than 90% by volume and at least 30% by volume.
  • a steel flat product according to the invention shows particularly good forming properties, which are reflected in high values for the hole expansion HER of more than 20% (determined according to DIN ISO 16630) and in a maximum drawing depth of more than 33 mm (determined in the limiting dome height (LDH) test with a 100 mm half-round punch). These are achieved through early local hardening, which is higher than in comparable grades of this strength class and is reflected in a hardening exponent n, measured in Elongation interval between 0.2% and 2.2% according to DIN EN ISO 10275:2014, of at least 0.22%.
  • flat steel products according to the invention are particularly suitable for the production of axially stressed components, such as longitudinal and cross members, or for the production of bending stressed components, such as B-pillars, B-pillar reinforcements or sills of automobile bodies.
  • cold-rolled flat steel products made according to the invention can be produced by completing at least the following work steps: a) Melting a steel melt consisting of, in % by mass, C: 0.040-0.100%, Mn: 2.10-2.50%, Si : 0.10 - 0.40%, Al: up to 0.10%, Cr: 0.30 - 0.90%, Ti: 0.020 - 0.080%, B: 0.0005 - 0.0020%, Ca: up to 0.005%, P: up to 0.025%, S: up to 0.010%, N: 0.003 - 0.010%, and optionally up to 0.20% Mo, up to 0.050% Nb, up to 0.10% Cu, up to 0.020% V and up to 0.10% Ni and balance iron and unavoidable impurities; b) Casting of the melt into a preliminary product, such as a slab or thin slab; c) Hot rolling of the preliminary product with a final hot rolling temperature of 850 - 980 °C to form
  • a melt alloyed according to the invention can be melted in the same conventional manner as can the melt be cast to form the preliminary product, which is typically a slab or thin slab (steps a) and b)).
  • Slabs are typically 180 mm to 260 mm thick, while thin slabs are typically 40 mm to 60 mm thick.
  • the preliminary product can also be hot-rolled in a conventional manner on units known for this purpose from the prior art.
  • the hot rolling finish temperature is set at 850 - 980°C, preferably 880 - 950°C.
  • the hot strip obtained is cooled to a coiling temperature of 480-650° C. and wound into a coil at this temperature.
  • a range of coil temperatures that is to be maintained in a particularly reliable manner is limited to at least 500 °C and at most 600 °C.
  • the risk of grain boundary oxidation increases, which would impair the surface quality of the steel flat product.
  • the strength of the hot strip increases significantly, which causes difficulties in the subsequent deformation.
  • the coiled hot-rolled flat steel product cools down to room temperature in the coil.
  • the flat steel product can then optionally be descaled. For this purpose it can, for example, run through a pickling device in which scale adhering to the flat steel product is removed.
  • Zinc-based anti-corrosion layer can be covered by hot-dip coating, the cold-rolled flat steel product can be produced according to steps a) - f) and then complete the following work steps in a continuous process: g) annealing of the cold-rolled flat steel product in a continuous furnace at an annealing temperature GT of 780 - 920 °C to achieve a sufficient degree of recrystallization after cold forming. Optimum annealing results are achieved when the annealing temperature is set to 810 - 890 °C.
  • the typical annealing time Gt during which the flat steel product is kept at the annealing temperature GT in the annealing furnace, is between 10 and 1000 s.
  • This cooling is carried out in two stages:
  • the cold-rolled flat steel product is in the first stage of its cooling from the respective annealing temperature GT to a temperature in the range of 750 -620 °C Intermediate temperature ZT with a cooling rate AR1, which is greater than 1.5 K / s, and is cooled in the second stage from the intermediate temperature ZT to the final cooling temperature KET with a cooling rate AR2, for which applies: AR2> 4 x AR1.
  • the cold-rolled flat steel product is cooled in the first stage from the respective annealing temperature GT to an intermediate temperature ZT in the range of 700 - 450 °C at a cooling rate AR1 that is greater than 5 K/s, and in the second stage from the intermediate temperature ZT to the respective final cooling temperature KET with a cooling rate AR2, for which the following applies: AR2 ⁇ (AR1)/3.
  • the desired microstructure formation of a flat steel product according to the invention is achieved through the selection of the respective cooling rates in the first and second stages.
  • the composition of the molten bath can be selected in a conventional manner, it being possible for the molten bath to be pure zinc melt or to consist of at least 75% by weight Zn.
  • annealing is carried out in a continuous furnace at an annealing temperature in the range of 780-920.degree with an annealing time Gt between 10 - 1000 s.
  • the heated cold-rolled flat steel product is then cooled to a final cooling temperature KET in the range of 380 - 500 °C in such a way that the cooling of the cold-rolled flat steel product, which has been heated to the annealing temperature GT, to a final cooling temperature KET in two stages takes place, with the cold-rolled steel flat product in the first stage of its cooling from the respective annealing temperature GT to an intermediate temperature ZT in the range 700 - 450 °C at a cooling rate AR1 that is greater than 5 K/s, and in the second stage from the Intermediate temperature ZT is cooled to the respective final cooling temperature KET at a cooling rate AR2, for which the following applies: AR2 ⁇ (AR1)/3.
  • the cold-rolled flat steel product is then cooled to room temperature.
  • the cold-rolled flat steel product obtained, provided with the anti-corrosion coating or uncoated can also be subjected to skin-pass rolling in order to optimize its mechanical properties, its surface quality and its dimensional accuracy.
  • degrees of deformation degree of skinning
  • melts A - J were melted, the compositions of which are given in Table 1.
  • the melts A - J were cast in a conventional continuous casting plant to form slabs, which were then hot-rolled to form hot strip, coiled into a coil and cooled to room temperature.
  • the hot strip was then pickled and cold-rolled in a conventional manner with a total cold-rolling degree KG to form a cold-rolled flat steel product in the form of a cold-rolled strip.
  • the cold-rolled flat steel products In order to coat the cold-rolled flat steel products obtained in this way with a Zn-based anti-corrosion coating, the cold-rolled flat steel products have been annealed at the respective annealing temperature GT for a respective annealing time Gt.
  • the cold-rolled flat steel products have been cooled to a final cooling temperature KET.
  • the flat steel product was cooled in one step or in two stages, with the first stage of cooling to an intermediate temperature ZT at a cooling rate AR1 and then the second stage of cooling starting from the intermediate temperature ZT at a cooling rate AR2 to the final cooling temperature KET has been cooled (Table 2).
  • the cooled, cold-rolled flat steel products are then heated or cooled to the bath inlet temperature BT and passed through a molten bath that consists of at least 75% Zn.
  • the thickness of the anti-corrosion coatings applied in this way by hot-dip coating to the cold-rolled flat steel products has been adjusted in a conventional manner by blowing off the excess coating material when the flat steel products emerge from the molten bath.
  • the tensile strength Rm, the yield point Rp0.2 and the elongation A80 as well as the hole expansion HER according to DIN ISO 16630 were determined on the cold-rolled flat steel products obtained in this way according to DIN ISO 6892 (longitudinal direction of tension, specimen shape 2).
  • the structural proportions of ferrite F and martensite M were determined using a light microscope in accordance with DIN 50601: 1985-08.
  • the rest of the structure consisted, if present, of small amounts of bainite and retained austenite, the latter was determined by means of the standard-free quantitative phase analysis according to DIN EN 13925 (2003.07) with the help of a Rietveld refinement.
  • the properties concerned are given in Table 3.
  • the steel strips produced with the alloy concept according to the invention with a tensile strength Rm of at least 750 MPa are characterized in that in the hole expansion test with decreasing cone angle, an above-average increase in the measured hole expansion is achieved when the tests are carried out with cone angles varying in the range from 180° to 50° is carried out in order to selectively influence the deformation distribution in the 0 mm to 5 mm wide area of the punched hole near the edge.
  • the punched hole is produced by mechanical shearing. Identical cutting parameters are set for all samples. The width of the cutting gap is in the range of 9 - 15% of the thickness of the steel flat product examined.
  • Material failure is characterized by a constriction or a crack across the entire sheet thickness in the area of the cut edge. Due to the use of a significantly larger diameter of the punched hole of 20 mm compared to the test according to DIN ISO 16630, the influence of the sheet thickness in the typical sheet thickness range of 1.0 to 2.0 mm is comparatively small. The achieved hole expansion values of the different punches can be better compared through the geometric conversion to the center plane of the sheet. By assuming "uniaxial tension" at the edge and the measured hole expansion, the sheet thickness reduction can be calculated according to the relationships given in Table 4
  • Sheet thickness edge [mm] initial sheet thickness xe (-0.5 * LN((HER/ 100) + 1) ),
  • HER center plane [%] [( ⁇ center plane HER - ⁇ exit) / ⁇ exit] x 100% (see also Fig. 1).
  • the effects that arise in the hole expansion tests carried out in the manner explained above can be verified by means of FE analysis.
  • the determination of the time of failure or the maximum possible expansion is carried out by means of a video analysis.
  • the process is observed centrally from above using a camera.
  • the hole expansion or the achieved diameter of the inner edge surrounding the respective hole can be measured before the point of failure and calculated as a percentage of the hole expansion in relation to the initial diameter.
  • the frame rate of the video film is at least 10 frames per mm of stamp travel at a stamp speed of 1 mm/s.
  • the drawing depth was carried out in the Limiting Dome Height Test (LDH Test).
  • LDH Test Limiting Dome Height Test
  • the flow of material from the flange area is completely prevented during the forming and the material is cut with a 0100 mm half-round punch (Nakazima tool) up to transformed to material failure (see Fig. 1).
  • the hold-down force was set to 400 kN and the drawing speed to 1.0 mm/sec (+/- 0.2).
  • FIG. 3 shows a diagram in which the hole expansion achieved in each case is shown as a function of the opening angle used of the forming die used, based on the center plane, according to the conversion explained above.
  • the sheets examined were each 1.5 mm thick. They consisted on the one hand of a steel composed according to the invention according to melt analysis A in Table 1 (the associated values are shown in Fig.
  • cell 1 data in % by mass, remainder iron and unavoidable impurities; Alloys not according to the invention, i.e. alloy components, are marked by underlining

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Abstract

L'invention concerne un produit plat en acier laminé à froid, son substrat en acier présentant une résistance à la traction de 750 à 940 MPa, une résistance élevée, une soudabilité améliorée et des propriétés de façonnage optimisées et qui, en même temps, peut être produit à faibles coûts. Un produit plat en acier laminé à froid selon l'invention est constitué d'un acier qui est composé, en pourcentage en masse, de C : de 0,040 à 0,100 % ; de Mn : de 2,10 à 2,50 % ; de Si : de 0,10 à 0,40 % ; de Cr : de 0,30 à 0,90 % ; de Ti : de 0,020 à 0,080 % ; de B : de 0,0005 à 0,0020 % ; de N : de 0,003 à 0,010 % ; d'Al : jusqu'à 0,10 % ; de Ca : jusqu'à 0,005 % ; de P : jusqu'à 0,025 % ; de S : jusqu'à 0,010 % ; éventuellement un ou plusieurs des éléments suivants : du Mo : jusqu'à 0,20 %; du Nb : jusqu'à 0,050 % ; du Cu : jusqu'à 0,10 % ; du V : jusqu'à 0,020 % ; du Ni : jusqu'à 0,10 %, le complément étant constitué de fer et d'impuretés inévitables, la teneur totale en impuretés étant limitée à au plus 0,5 % en masse et les teneurs en phosphore (« P ») et en soufre (« S ») faisant partie des impuretés. De plus, le substrat en acier possède une structure à deux phases qui est constituée de 10 à 40 % en volume de martensite, de 30 à 90 % en volume de ferrite y compris de ferrite bainitique, d'une teneur en austénite résiduelle inférieure ou égale à 5 %, le complément étant constitué d'autres constituants structuraux inévitables associés à la production.
EP22710062.5A 2021-03-03 2022-03-03 Produit plat en acier, son procédé de production, et utilisation d'un tel produit plat en acier Pending EP4301885A1 (fr)

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KR102020411B1 (ko) * 2017-12-22 2019-09-10 주식회사 포스코 가공성이 우수한 고강도 강판 및 이의 제조방법
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