US20240141455A1 - Flat Steel Product, Method for the Production Thereof, and Use of Such a Flat Steel Product - Google Patents

Flat Steel Product, Method for the Production Thereof, and Use of Such a Flat Steel Product Download PDF

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US20240141455A1
US20240141455A1 US18/280,058 US202218280058A US2024141455A1 US 20240141455 A1 US20240141455 A1 US 20240141455A1 US 202218280058 A US202218280058 A US 202218280058A US 2024141455 A1 US2024141455 A1 US 2024141455A1
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Prior art keywords
flat steel
steel product
cold
temperature
rolled
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Ekaterina Bocharova
Olga Sukhopar
Georg Paul
Stefan Woestmann
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Publication of US20240141455A1 publication Critical patent/US20240141455A1/en
Assigned to THYSSENKRUPP STEEL EUROPE AG reassignment THYSSENKRUPP STEEL EUROPE AG ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: BOCHAROVA, EKATERINA, SUKHOPAR, Olga, WOESTMANN, STEFAN, PAUL, Georg
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    • 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
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    • C21D1/18—Hardening; Quenching with or without subsequent tempering
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    • 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
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum

Definitions

  • the invention relates to a cold-rolled flat steel product, to a method for the production thereof, and to uses of a flat steel product according to the invention.
  • “Flat steel products” are understood here to be rolled products the length and width of which are each substantially greater than their thickness. These include in particular steel strips, steel sheets, and pre-cut parts obtained therefrom—such as blanks and the like.
  • a cold-rolled flat steel product is known from EP 2 031 081 B1, which can be hot-dip coated with a zinc-based anticorrosion coating and which has a structure that consists of 20-70% martensite, up to 8% of residual austenite, and has a remainder of ferrite and/or bainite.
  • the flat steel 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 iron and unavoidable impurities as the remainder.
  • Steel concepts of this type are characterized by a low elastic limit ratio which is attributable to significant strength differences between the structural constituents.
  • a product proposed to address this need has at least the features as described herein.
  • a method that enables the cost-effective production of a product according to the invention is specified as described herein.
  • a product can be provided in the manner indicated as described herein with an anticorrosion coating, based in particular on zinc (“Zn”).
  • FIG. 1 is a schematic showing the hole expansion test and referencing the parameters used to determine the hole expansion ratio (HER) of the inventive flat steel product;
  • FIG. 2 is a schematic showing the limiting dome height (LDH) test used to evaluate the inventive flat steel product.
  • FIG. 3 is a graph showing the relationship between hole expansion (%) and the cone angle of the punch used in the hole expansion testing apparatus as shown in FIG. 1 .
  • the steel substrate of a flat steel 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%: 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 iron and unavoidable impurities as the remainder.
  • the steel substrate of a flat steel product according to the invention has a dual-phase structure which consists of 10-40 vol. % martensite, 30-90 vol. % ferrite, including bainitic ferrite, not more than 5% residual austenite, and of other structural constituents which are unavoidable due to the production process as a remainder, wherein such other structural constituents are present only if the sum of the fractions of the other constituents of the structure is less than 100%.
  • a flat steel product according to the invention comprises 0.040-0.100% by mass of carbon (“C”).
  • C carbon
  • the maximum carbon fraction of 0.100% by weight provided according to the invention was selected with regard to good weldability of the steel.
  • carbon fractions above 0.100% by weight would lead to the formation of a harder carbon-rich martensite phase, which would significantly increase the difference in hardness between martensite and ferrite. This would have a negative effect on the hole-expansion behavior and the weldability of a flat steel product according to the invention.
  • the positive effects of the presence of C in the steel of a flat steel product according to the invention can be exploited particularly well if the C fraction is at least 0.05% by mass and at most 0.08% by mass.
  • Si Silicon
  • the upper limit of the Si fraction is 0.40% by mass, to avoid grain boundary oxidation by which the coatability and the surface properties of the steel could be negatively influenced.
  • Mn Manganese
  • the Mn fraction is preferably at least 2.20% by mass and at most 2.40% by mass.
  • Aluminum (“Al”) in fractions of up to 0.10% by mass is required for deoxidation during steel production.
  • Ca can likewise be added to the steel of a flat steel product according to the invention in fractions of up to 0.005% by mass, in order to deoxidize the steel during steel production. This effect can be achieved by adding at least 0.0005% by mass of Ca.
  • Chromium (“Cr”) likewise serves to increase the strength in the steel of a flat steel product according to the invention.
  • a Cr fraction of at least 0.30% by mass, in particular at least 0.40% by mass, is required for this purpose.
  • the upper limit of the range specified according to the invention for the Cr fraction is limited to at most 0.90% by mass, in particular at most 0.80% by mass.
  • the method for producing the flat steel product obtained according to the invention is to be carried out such that an annealing temperature GT of at least 840° C. is set, in order to obtain the desired dual phase structure and the desired mechanical properties of the flat steel product according to the invention in a reliable manner.
  • Titanium (“Ti”) is provided in the steel of a flat steel product according to the invention in fractions of 0.020-0.080% by mass, in order likewise to improve the strength by the formation of fine Ti precipitates, such as TiC or Ti(C,N) precipitates, and to obtain a fine-grained structure.
  • Ti fractions of at least 0.030% by mass can be provided.
  • the quantity of precipitation enabled by the Ti fraction provided according to the invention contributes among other things to the optimal 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 flat steel product according to the invention can be exploited particularly effectively in the case of Ti fractions of up to 0.07% by mass.
  • Ti in the steel of a flat steel product according to the invention can additionally be assisted by adding Ti in an amount which corresponds at most to 11 times the respective N and B fractions of the steel of a flat steel product according to the invention.
  • Ti fraction % Ti applies:
  • B Boron
  • N nitrogen
  • the nitrogen (“N”) fraction is limited in the steel of a flat steel product according to the invention to up to 0.010% by mass, so that Ti acts as an alloying element in the structure and is not completely bound with N. Fractions of at least 0.003% by mass N are provided in order to ensure a sufficient amount of Ti(C,N) precipitates in the structure.
  • the impurities include fractions of phosphorus (“P”) and sulfur (“S”).
  • the fraction of P is limited to up to 0.025% by mass, in particular less than 0.015% by mass, in order to avoid worsening of the weldability.
  • the S fraction is limited to at most 0.010% by mass in order to avoid the formation of MnS and/or (Mn/Fe)S, which would have a negative effect on the tensile properties of the steel according to the invention.
  • the total fraction of impurities is limited in the steel of a flat steel product according to the invention to at most 0.5% by mass, wherein an impairment of the properties of the flat steel product at a total of impurities of at most 0.3% by mass is particularly reliably avoided.
  • Mo molybdenum
  • Nb niobium
  • Cu copper
  • V vanadium
  • Ni nickel
  • the fractions of these elements are limited in such a way that they have only 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., be so low that they can be considered impurities, and do not produce any 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, an elastic limit of 440-650 MPa, and an elongation at break A80 of more than 13%, and is characterized by particularly good forming properties with minimized edge crack tendency, and likewise good weldability.
  • the tensile strength Rm, the elastic limit Rp0.2, and the elongation at break A80 are each determined in accordance with DIN ISO 6892 (longitudinal tensile direction; sample form 2).
  • This structure state can be achieved primarily by a carbon fraction limited according to the invention, and a certain addition of Ti and B amounts. In this way, an above-average robust behavior with increasing shape change gradients in the hole expansion test is achieved.
  • martensite and ferrite fractions including bainitic ferrite in the structure of a flat steel product according to the invention are quantified by means of image analysis.
  • the martensite fraction in the structure of a flat steel product according to the invention is limited to not more than 40 vol. %, wherein at least 10 vol. % of martensite is present in order to secure the required strength.
  • the rest of the structure of a flat steel product according to the invention in addition to fractions of not more than 5 vol. % residual austenite, is primarily ferrite, including bainitic ferrite, which may not be more than 90 vol. % and is at least 30 vol. %.
  • a flat steel product according to the invention displays particularly good forming properties which manifest themselves in high values for the hole expansion ratio HER of greater than 20% (determined according to DIN ISO 16630), and a maximum drawing depth of greater than 33 mm (determined in the limiting dome height (LDH) test with a 100 mm hemispherical die). These are achieved by an early local hardening which is higher than with comparable goods in this strength class, and which are reflected in a tensile strain hardening exponent n, measured in the elasticity 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 suitable, in particular, for the production of axially loaded components, such as longitudinal members and cross-members, or for producing bending-load-bearing components, such as B-pillars, B-pillar reinforcements, or sills of automobile bodies.
  • cold-rolled flat steel products obtained according to the invention can be produced by performing at least the following work steps:
  • the cold-rolled flat steel product heated to the annealing temperature GT is cooled to a cooling end temperature KET in two steps, wherein the cold-rolled flat steel product in the first step of its cooling is cooled from the given annealing temperature GT to an intermediate temperature ZT lying in the range of 750-620° C., with a cooling rate AR1 which is greater than 1.5 K/s, and in the second step from the intermediate temperature ZT to the given cooling end temperature KET, with a cooling rate AR2 for which the following applies: AR2>4 ⁇ AR1 or
  • the cold-rolled flat steel product heated to the annealing temperature GT is cooled to a cooling end temperature KET in two steps, wherein the cold-rolled flat steel product in the first step of its cooling is cooled from the given annealing temperature GT to an intermediate temperature ZT lying in the range of 700-450° C., with a cooling rate AR1 which is greater than 5 K/s, and in the second step from the intermediate temperature ZT to the given cooling end temperature KET, with a cooling rate AR2 for which the following applies: AR2 ⁇ (AR1)/3;
  • the melting of a melt alloyed according to the invention can likewise take place in a conventional manner, as can the casting of the melt to make the precursor, which is typically a slab or thin slab (work steps a) and b).
  • Slabs in this case typically have thicknesses of 180 mm to 260 mm, while the thicknesses of thin slabs typically lie around 40 mm to 60 mm.
  • the hot rolling of the precursor can likewise take place in a conventional manner on assemblies known from the prior art.
  • the hot rolling end temperature is set to 850-980° C., preferably to 880-950° C.
  • the hot-rolled strip obtained is cooled to a coiling temperature which is 480-650° C., and is wound into a coil at this temperature.
  • a range of the coiling temperatures which is particularly reliable is limited to at least 500° C. and at most 600° C.
  • the risk of grain boundary oxidation increases, which would worsen the surface quality of the flat steel product.
  • the strength of the hot-rolled strip decreases greatly, which causes difficulties in the subsequent forming.
  • the coiled hot-rolled flat steel product cools down to room temperature in the coil.
  • the flat steel product can optionally be descaled.
  • it can, for example, pass through a pickling device in which scale adhering to the flat steel product is removed.
  • the optionally descaled hot-rolled strip is then cold rolled to form a cold-rolled flat steel product, wherein the total degree of cold rolling KG ([thickness of the flat steel product prior to cold rolling—thickness of the flat steel product after cold rolling]/thickness of the flat steel product prior to cold rolling] ⁇ 100%) achieved in the course of cold rolling is 25-70%.
  • a flat steel product according to the invention is to be coated with an anticorrosion layer based on zinc by hot dip coating
  • the cold-rolled flat steel product can be produced in accordance with the work steps a)—f), and then can complete the following work steps in a continuous run:
  • This cooling is carried out in two steps:
  • the cold-rolled flat steel product in the first step of its cooling is cooled from the given annealing temperature GT to an intermediate temperature ZT lying in the range of 750-620° C., with a cooling rate AR1 which is greater than 1.5 K/s, and in the second step from the intermediate temperature ZT to the given cooling end temperature KET, with a cooling rate AR2 for which the following applies: AR2>4 ⁇ AR1
  • the cold-rolled flat steel product in the first step of its cooling is cooled from the given annealing temperature GT to an intermediate temperature ZT lying in the range of 700-450° C., with a cooling rate AR1 which is greater than 5 K/s, and in the second step from the intermediate temperature ZT to the given cooling end temperature KET, with a cooling rate AR2 for which the following applies: AR2 ⁇ (AR1)/3;
  • the choice of the respective cooling rates in the first and second steps achieves the desired structure formation of a flat steel product according to the invention.
  • the composition of the melt bath can be selected in a conventional manner, wherein the melt bath can be a pure zinc melt, or consists of at least 75% by weight of Zn.
  • a cold-rolled flat steel product according to the invention is to remain uncoated or is to be electrolytically coated, an annealing treatment takes place in a continuous furnace at an annealing temperature in the range from 780 to 920° C., with an annealing duration Gt between 10-1000 s. Subsequently, the heated cold-rolled flat steel product is cooled to a cooling end temperature KET in the range 380 to 500° C.
  • the cooling of the cold-rolled flat steel product heated to the annealing temperature GT to a cooling end temperature KET occurs in two steps, wherein the cold-rolled flat steel product in the first step of its cooling is cooled from the given annealing temperature GT to an intermediate temperature ZT lying in the range of 700-450° C., with a cooling rate AR1 which is greater than 5 K/s, and in the second step from the intermediate temperature ZT to the given cooling end temperature KET, with a cooling rate AR2 for which the following applies: AR2 ⁇ (AR1)/3; This is followed by cooling of the cold-rolled flat steel product to room temperature.
  • the obtained cold-rolled flat steel product provided with the anticorrosion coating, or uncoated can still be subjected to skin-pass rolling in order to optimize its mechanical properties, its surface properties, and its dimensional accuracy.
  • skin-pass degrees forming degrees
  • melts A-J were melted, the compositions of which are indicated in Table 1.
  • the melts A-J were cast into slabs in a conventional continuous casting plant, which are subsequently hot-rolled to form hot-rolled strips, coiled to form a coil, and cooled to room temperature. Subsequently, the hot-rolled strips are pickled and cold rolled with a total degree of cold rolling KG, to form a cold-rolled flat steel product present as a cold strip.
  • the cold-rolled flat steel products were annealed at the given annealing temperature GT over a given annealing duration Gt.
  • the cold-rolled flat steel products were cooled to a cooling end temperature KET.
  • the cooling of the flat steel product was carried out in one step, or in two steps, wherein the cooling proceeded in the first step of the cooling to an intermediate temperature ZT with a cooling rate AR1, and then in the second step of the cooling to the cooling end temperature KET with a cooling rate AR2 starting from the intermediate temperature ZT (Table 2).
  • the cooled cold-rolled flat steel products are subsequently heated or cooled to the bath entry temperature BT and conveyed through a melt bath consisting of at least 75% Zn.
  • the thickness of the anticorrosion coatings applied in this way by hot dip coating on the cold-rolled flat steel products was adjusted in a conventional manner by blowing off the excess coating material when the flat steel products exit the melt bath.
  • the tensile strength Rm, the elastic limit Rp0.2 and the elongation A80, and also the hole expansion ratio HER according to DIN ISO 16630 were determined for the cold-rolled flat steel products thus obtained, according to DIN ISO 6892 (longitudinal tensile direction, sample form 2).
  • the structural fractions of ferrite F and martensite M were determined using light microscopy according to DIN 50601: 1985-08.
  • the remaining structure, if present, consisted of small fractions of bainite and residual austenite. The latter was determined by means of standard quantitative phase analysis according to DIN EN 13925 (2003.07) with the aid of Rietveld refinement. These properties are specified in Table 3.
  • the steel strips with a tensile strength Rm of at least 750 MPa produced with the alloy concept according to the invention are characterized by the fact that, for a 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 varied in the range of 180° to 50° in order to influence the shape change distribution in a targeted manner in the region of the punched hole, which is close to 0 mm to 5 mm wide.
  • the punched hole is produced by mechanical shear cutting. Identical cutting parameters are set for all samples. The width of the cutting gap is in the range of 9 to 15% of the thickness of the flat steel product being tested.
  • the material failure is characterized by a constriction or a crack over the entire sheet thickness in the region of the cutting edge.
  • a diameter of the punched hole of 20 mm, which is significantly larger 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 low.
  • the achieved hole expansion values of the different punches are more easily compared by a geometric conversion to the center plane of the metal sheet. Assuming “single-axis tensile force” on the edge and using the measured hole expansion, the sheet thickness reduction can be found according to the relationships depicted in Table 4:
  • the effects which occur in the hole expansion experiments carried out in the manner explained above can be detected by means of FE analysis.
  • the moment of failure and/or the maximum possible expansion is determined by means of video analysis.
  • the process is observed centrally from above by means of a camera.
  • the hole expansion and/or the diameter of the inner edge delimiting the given hole can be measured before the moment of failure and calculated as a percentage hole expansion with respect to the exit diameter.
  • the image frequency of the video film is at least 10 images per mm of punch path, for a punch speed of 1 mm/s.
  • the drawing depth was analyzed in a limiting dome height test (LDH test).
  • LDH test limiting dome height test
  • the material flow from the flange region is completely prevented during formation, and the material is formed with a 0100 mm hemispherical punch (Nakazima tool) up 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 is shown in each case as a function of the opening angle of the forming punch used relative to the center plane, according to the conversion explained above.
  • the metal sheets being tested were each 1.5 mm thick.
  • One group consisted of a steel composed according to the invention in accordance with the melt analysis A in Table 1 (the associated values are reproduced in FIG. 2 by circles connected to one another by a dotted line).
  • the other group consisted of a conventional steel available under the name “DP800-DH”, which consists, in % by mass, of 0.157% C, 1.98% Mn, 0.114% Si, 0.324% Al, 0.106% Cr, 0.004% Ti, 0.0002% B, 0.012% P, 0.001% S, 0.0038% N, 0.02% Mo, 0.022% Nb, 0.01% Cu, 0.001% V, 0.02% Ni, and iron and unavoidable impurities as the remainder.
  • the hole expansions achieved in the sheet metal samples consisting of the material according to the invention were clearly better than in the case of the sheet-metal samples consisting of the conventional steel.

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