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EP3204530B2 - Kaltgewalztes und rekristallisierend geglühtes stahlflachprodukt und verfahren zu dessen herstellung - Google Patents

Kaltgewalztes und rekristallisierend geglühtes stahlflachprodukt und verfahren zu dessen herstellung Download PDF

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Publication number
EP3204530B2
EP3204530B2 EP15762569.0A EP15762569A EP3204530B2 EP 3204530 B2 EP3204530 B2 EP 3204530B2 EP 15762569 A EP15762569 A EP 15762569A EP 3204530 B2 EP3204530 B2 EP 3204530B2
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EP
European Patent Office
Prior art keywords
flat steel
steel product
temper
skin
roll
Prior art date
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EP15762569.0A
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German (de)
English (en)
French (fr)
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EP3204530B1 (de
EP3204530A1 (de
Inventor
Marc Blumenau
Jörg STEINEBRUNNER
Udo ZOCHER
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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Application filed by ThyssenKrupp Steel Europe AG, ThyssenKrupp AG filed Critical ThyssenKrupp Steel Europe AG
Priority to PL15762569.0T priority Critical patent/PL3204530T5/pl
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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
    • 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
    • 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
    • C21D8/0421—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
    • 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
    • C21D8/0421—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
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D3/00—Electroplating: Baths therefor
    • C25D3/02—Electroplating: Baths therefor from solutions
    • C25D3/22—Electroplating: Baths therefor from solutions of zinc
    • 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

Definitions

  • the invention relates to a method for producing a cold-rolled and recrystallization-annealed flat steel product with a ferritic microstructure.
  • Flat steel products of this type are used in particular in the field of automobile body construction, where particularly high demands are placed on the formability and optical appearance of the components formed from such flat steel products.
  • Flat steel products intended for car body construction or similar applications are typically provided with a surface structure that is characterized by a defined roughness and an equally defined peak distribution in order to meet customer-specific requirements with regard to formability and surface appearance (paintability and paint gloss).
  • a typical example of corresponding specifications from the automotive industry is an arithmetic mean roughness (hereinafter referred to as "roughness") Ra of 1.1 - 1.6 ⁇ m with a peak number RPc of at least 60 1/cm.
  • the roughness Ra and the peak number RPc are determined in accordance with steel iron test sheet SEP 1940 using a stylus device in accordance with ISO 3274.
  • Wsa waviness value Wsa(1 - 5)
  • Wsa waviness value Wsa(1 - 5)
  • Typical requirements are Wsa values of 0.35 ⁇ m to 0.40 ⁇ m.
  • Particularly good paint gloss is achieved with Wsa values of ⁇ 0.35 ⁇ m, in particular ⁇ 0.30 ⁇ m.
  • peak numbers RPc of at least 75 1/cm and roughnesses Ra of 0.9 - 1.4 ⁇ m are required.
  • the adjustment of the material properties Ra and RPc in the production of cold-rolled flat steel products is typically carried out by skin passing after the recrystallization annealing that the flat steel products undergo after cold rolling in order to ensure their optimum formability.
  • Skin-passing is understood here as a pre-rolling or finishing process carried out after recrystallizing annealing, in which the flat steel product is subjected to a slight deformation of approx. 0.2 - 2.0%, which is referred to here as the "skin-passing degree".
  • the skin-passing degree is determined by comparing the peripheral speeds of the deflection rollers, which are equipped with position sensors, before and after the rolling mill in which the flat steel product is skin-passed.
  • the skin pass degree D is set too high, the roughness Ra will be too high. If, on the other hand, the skin pass degree D is set too low, the edges of the strip may not be dressed, particularly with wide strip dimensions. In these cases, the Ra and RPc values achieved are then too low.
  • the skin pass degree D cannot be varied arbitrarily with regard to the mechanical properties of the steel substrate.
  • a skin pass degree D that is too low does not adequately counteract a pronounced yield point.
  • a skin pass degree D that is too high can result in the strength of the steel substrate being uncorrectably high due to excessive work hardening.
  • Soft here means a steel that, in the recrystallized state and after skin-pass rolling, has a yield strength Rp0.2 of no more than 180 N/mm2 and a tensile strength Rm of no more than 340 N/mm2. In practice, this means that flat steel products of the type in question here with dimensions typical for automobiles can currently only be produced with the desired operational reliability at great expense. Steels with a yield strength Rp0.2 of max. 150 MPa and a tensile strength Rm of no more than 310 MPa are particularly critical.
  • EP 0 234 698 B1 known method for producing a steel sheet suitable for painting.
  • This method provides for a regular pattern of depressions to be created in the surface of a skin-pass roll using an energy beam.
  • the flat steel product to be processed is skin-pass rolled using two work rolls, at least one of which is processed in the manner described above.
  • the reduction in cross-section achieved by skin-pass rolling should not be less than 0.3% in order to transfer the pattern from the work roll to the surface of the steel sheet.
  • a steel sheet which has an average surface roughness Ra within the range of 0.3 to 3.0 ⁇ m and a microscopic shape forming the surface roughness, which consists of trapezoidal raised regions with a flat upper surface, groove-like recessed regions formed in such a way that they completely or partially surround a raised region, and flat central regions formed between the raised regions outside the recessed regions in such a way that they are higher than the bottom of the recessed regions and lower or of the same height as the upper surfaces of the raised regions.
  • the raised regions and recessed regions are to have certain geometric dependencies, inter alia, on the diameter of the recesses formed in the skin-pass roll.
  • the steel sheet consists of a steel with, in % by weight, 0.10% or less C, 0.05% or less Si, 0.1 - 1.0% Mn, 0.05% or less P, 0.02% or less S, 0.02 - 0.10% Al, less than 0.005% N and the remainder being Fe and unavoidable impurities.
  • the steel sheet thus obtained is subjected to an annealing treatment in which it is annealed for at least 30 s at an annealing temperature of 730 - 850 °C and then cooled to a maximum temperature of 600 °C at a cooling rate of at least 5 °C/s.
  • the cold-rolled annealed steel flat product obtained thereafter has a structure consisting mainly of ferrite, which has an average crystal grain diameter of 5 - 30 ⁇ m.
  • the steel flat product is skin-pass rolled using a roll whose surface roughness Ra is at most 2 ⁇ m. The stretch ratio achieved by skin-pass rolling is adjusted depending on the average crystal grain diameter of the thin cold-rolled annealed sheet.
  • the object of the invention was to provide a method for producing a flat steel product.
  • a method which allows the reliable production of a flat steel product is specified in claim 1.
  • the depressions and peaks formed in the surface which determine the mean roughness Ra and the peak number RPc, are distributed stochastically.
  • a flat steel product that can be produced by the method according to the invention thus consists of a soft steel that has a yield strength Rp0.2 of up to 180 MPa, in particular less than 150 MPa, a tensile strength Rm of up to 340 MPa, in particular less than 310 MPa, and at the same time has a high elongation with a breaking elongation A80 of at least 40% and a high n-value of at least 0.23. With this combination of properties, it is optimally suited for forming, in particular for deep drawing.
  • a steel flat product that can be produced by the process according to the invention has a surface quality characterized by an arithmetic mean roughness Ra of 0.8 - 1.6 ⁇ m and a peak number RPc of at least 75 1/cm, which makes it extremely suitable for painting with optimized paint gloss.
  • Surface structures according to the invention thus reliably achieve Wsa values of at most 0.40 ⁇ m, typically at most 0.35 ⁇ m, in particular less than 0.30 ⁇ m, in particular even when the steel flat products that can be produced by the process according to the invention are in a range of dimensions typical for automotive applications with thicknesses of up to 1.0 mm and widths of at least 1000 mm.
  • a steel flac product that can be produced by the process according to the invention is particularly suitable for forming and painting in the uncoated state or in the state covered with a metallic protective layer.
  • Such a metallic coating is intended, it should be applied by electrolytic coating.
  • electrolytic coating By using known electrolytic processes, it is ensured that the surface structure of the steel strip that has been skin-rolled according to the invention is retained on the surface of the flat steel product covered with the metallic coating.
  • An electrolytically applied layer based on zinc is particularly suitable as a metallic protective layer.
  • the flat steel product that can be produced by the method according to the invention can also be coated with an inorganic or organic coating.
  • Inorganic coating means a passive layer typical for strip processes, e.g. as phosphating or chromating.
  • Organic coating means a thick-layer passivation typical for strip processes, e.g. based on Cr(III)-containing compounds.
  • Known coating agents can also be used here, which are usually used to improve paint adhesion, friction behavior in the forming tool and the like.
  • the surface texture formed on the surface of a flat steel product produced by the method according to the invention is characterized by a stochastic distribution of depressions and peaks which Determine the roughness value Ra according to the invention and the peak number RPc according to the invention.
  • Stochastic surface textures are irregular surface textures that are characterized by an irregular statistical distribution of design features such as depressions, which in turn can vary in distance, shape and size from one another.
  • Deterministic surface textures are regular surface textures that are characterized by a regular distribution of similar design features.
  • a stochastic surface texturing is aimed at in order to optimize the friction behavior between the steel surface and the tool during forming processes in the oiled or greased state.
  • a stochastic surface structure is characterized by the fact that under high pressure loads the lubricant can flow out of the stress zone via microchannels that open up between the peaks and valleys of the surface texture.
  • this more finely structured network of microchannels allows a more even distribution of the lubricant over the entire surface where contact occurs between the tool and the flat steel product during the forming process.
  • a stochastic basic structure ensures flow and adhesion properties for organic or metallic coatings, which can, if necessary, also be applied to the flat steel product that can be produced using the method according to the invention.
  • the roughness value Ra should not be less than 0.8 ⁇ m for the surface according to the invention of a flat steel product such as the one before, because otherwise the surface is too smooth. However, the roughness value Ra should not be greater than 1.6 ⁇ m either, because the surface is then too rough to achieve optimized forming properties. In order to be able to use the advantages of the invention reliably, roughness values Ra of 0.9 -1.4 ⁇ m can be provided.
  • the peak number RPc should not be less than 75 per cm because this would have a negative effect on the Wsa value.
  • the peak number at at least 75 1/cm, it is ensured that the Wsa value of a flat steel product that can be produced by the process according to the invention does not rise above 0.40 ⁇ m, in particular not above 0.35 ⁇ m, and that a coating achieves an optimal paint gloss.
  • Higher peak numbers lead to further improved Wsa values of the surface of a flat steel product that can be produced by the process according to the invention. In this way, the Wsa values of flat steel products that can be produced by the process according to the invention of less than 0.30 ⁇ m can be achieved.
  • Wsa values of at most 0.40 ⁇ m are reliably achieved if the peak number RPc for the surface produced according to the invention is set at at least 75 per cm. Wsa values of 0.35 ⁇ m or less are achieved if the peak number RPc for the flat steel product surface created according to the invention is set at at least 80 per cm. Finally, Wsa values of less than 0.30 ⁇ m can be ensured by setting a minimum value of 90 per cm for the peak number RPc.
  • a flat steel product that can be produced using the method according to the invention contains C, Si, Mn, P, Al and Ti as mandatory alloying elements with the following proviso:
  • the C content of the flat steel product that can be produced using the method according to the invention is 0.0001 - 0.003 wt.%.
  • C is unavoidably contained in the steel melt, so that C contents of at least 0.0001 wt.% can always be found in a steel according to the invention.
  • a C content above 0.003 wt.% impairs the desired formability due to an excessively strong strengthening contribution from carbon. This can be reliably prevented by reducing the C content to 0.002 wt.% or less.
  • Si is present in a flat steel product such as the one above in amounts of 0.001 - 0.025 wt.%. Si is also unavoidably present in the steel melt. However, a Si content above the limit of 0.025 wt.% according to the invention impairs the formability due to an excessive contribution to hardening. In order to avoid negative effects of the presence of Si, the Si content of a flat steel product such as the one above can be limited to a maximum of 0.015 wt.%.
  • Mn is present in a flat steel product such as the one before in amounts of 0.05 - 0.20 wt.%. Mn contents in this range contribute optimally to the formability of a flat steel product such as the one before. If the Mn contents lie outside the range specified by the invention, the amount is too low or too high due to solid solution strengthening. An optimal influence of the presence of Mn in the flat steel product such as the one before can be ensured by limiting the Mn content to a maximum of 0.15 wt.%.
  • P is provided in a flat steel product as before in amounts of 0.001 - 0.015 wt.%.
  • P is also unavoidably contained in the steel melt and contributes to solid solution strengthening.
  • a P content above the limit according to the invention impairs the desired formability and has negative effects on the desired painting result.
  • the P content can be limited to a maximum of 0.012 wt.%.
  • Al is present in a flat steel product as before in contents of 0.02 - 0.055 wt.%. Al is used in steel production to calm the steel melt and must therefore be within the limits of the invention However, an Al content above the upper limit of the Al content provided for in the invention impairs the desired formability.
  • the positive influence of Al in the alloy of a flat steel product such as the one above can be optimally utilized by limiting the Al content to a maximum of 0.03 wt.%.
  • Ti is present in a flat steel product like the one before in amounts of 0.01 - 0.1 wt.%.
  • Ti serves to bind interstitial alloying elements and thus contributes to precipitation strengthening.
  • a Ti content of less than 0.01 wt.% interstitial alloying elements are still dissolved in the crystal lattice, which has a negative effect on the desired formability.
  • Ti contents above 0.1 wt.% do not further improve the formability.
  • the positive effects of the presence of Ti can be used with a high degree of certainty when the Ti content is 0.05 - 0.09 wt.%.
  • a flat steel product which can be produced by the process according to the invention can optionally additionally contain the following alloying elements in order to achieve or adjust certain properties: Cr can be added to a flat steel product that can be produced by the process according to the invention in amounts of 0.001 - 0.05 wt.%, so that the presence of Cr at such low amounts has a positive effect on the mechanical properties of the flat steel product that can be produced by the process according to the invention, in particular its yield strength and tensile strength.
  • a Cr content above the range provided for in the invention impairs the desired formability.
  • V can optionally be added to the steel melt to also contribute to the binding of interstitial alloying elements and thus to precipitation strengthening.
  • V can be present in the flat steel product as before in contents of up to 0.005 wt.%.
  • Mo can optionally be present in the flat steel product as before in amounts of up to 0.015 wt.% to serve for solid solution strengthening.
  • a Mo content above the limit according to the invention impairs the desired formability.
  • N contents in the flat steel product are to be classified as technically unavoidable impurities.
  • N can also serve as precipitation strengthening through the formation of TiN. If the N content is greater than 0.004 wt.%, there is a risk that nitrogen will be dissolved in the crystal lattice and cause a pronounced yield point, which results in poor deep-drawing formability. Therefore, the optional N content is optimally limited to a maximum of 0.003 wt.% in order to ensure the desired forming properties.
  • impurities can be present in the flat steel product as before.
  • These include B, Cu, Nb, Ni, Sb, Sn and S, the total amount of which is no more than 0.2% by weight, whereby in the case of the presence of Nb, B or Sb the following special requirements apply to these impurities: Sb content no more than 0.001% by weight, Nb content no more than 0.002% by weight and B content no more than 0.0005% by weight.
  • Flat steel products can, for example, be manufactured reliably using the manufacturing method according to the invention.
  • step b) of the method according to the invention the respective sub-steps intended for the heat treatment of the flat steel product are carried out in a continuous furnace.
  • the heat treatment process takes place as a continuous annealing process because in this way the individual sub-steps of the heat treatment fit together homogeneously.
  • the uninterrupted process results in a significantly lower scatter in the mechanical properties of the flat steel product over its length and width.
  • individual sections can be heated directly in a manner known per se, for example in the manner of a DFF (Direct Fired Furnace), a DFI (Direct Flame Impingement) or an NOF (Non Oxidizing Furnace) furnace, or indirectly, for example in the manner of an RTF (Radiant Tube Furnace).
  • DFF Direct Fired Furnace
  • DFI Direct Flame Impingement
  • NOF Non Oxidizing Furnace
  • the cooling of the flat steel product to the overaging start temperature T2 and the final cooling of the flat steel product to room temperature can be carried out in a conventional manner by blowing gas, e.g. N2, H2 or a mixture thereof, by applying water, mist or by cooling by contact with cooling rolls, whereby each of these measures can also be carried out in combination with one or more of the other cooling measures.
  • blowing gas e.g. N2, H2 or a mixture thereof
  • a holding temperature T1 is provided for the recrystallizing annealing, which lies in the temperature range of 750 - 860 °C.
  • annealing temperatures below 750 °C complete recrystallization of the structure of the flat steel product can no longer be reliably achieved.
  • temperatures above 860 °C there is a risk of coarse grain formation. Both would have a negative effect on the forming properties.
  • Optimum results from recrystallizing annealing are obtained when the temperature T1 is 800 - 850 °C.
  • the duration t1 for which the steel flat product is held at the holding temperature T1 during recrystallization annealing is 30 - 90 seconds in order to ensure optimum forming properties of the steel flat product produced according to the invention. If t1 were less than 30 seconds, complete recrystallization of the structure could no longer be achieved in an operationally reliable manner. If the holding time t1 is longer than 90 seconds, there would again be a risk of coarse grain formation.
  • the flat steel product After holding at the holding temperature T1, the flat steel product is cooled to the overaging start temperature T2 at a cooling rate CR1 of 2 -100 °C/s.
  • the cooling rate CR1 is selected so that a flat steel product with optimal forming properties is obtained.
  • a minimum cooling rate CR1 of 2 °C/s is required to avoid coarse grain formation. If, on the other hand, the cooling rate CR1 is above 100 °C/s, the grain would be too fine, which would also be contrary to the desired good formability.
  • the overaging start temperature T2 is at least 400 °C, because at temperatures below this the cooling capacity required for cooling to the overaging start temperature T2 would be high, but the material properties would no longer be positively influenced. If the overaging start temperature T2 were above 600 °C, however, the recrystallization would not be stopped sustainably enough and there would be a risk of coarse grain formation. With an overaging start temperature T2 of 400 - 600 °C, in particular 400 - 550 °C, optimized forming properties can be achieved.
  • the flat steel product is subjected to an overaging treatment for a period t2 of 30 - 400 seconds, during which it is cooled to the overaging end temperature T3 at a cooling rate CR2 of 0.5 - 12 °C/s. If the time t2 were less than 30 seconds, the time in which the interstitial alloy atoms could distribute themselves evenly by diffusion in the recrystallized structure of the flat steel product would be too short. This would have a negative effect on the forming properties. An overaging treatment lasting longer than 400 seconds would not have any additional positive effect. A cooling rate CR2 of at least 0.5 °C/s is set in order to complete the overaging treatment within a practical time.
  • the final temperature T3 of the overaging treatment is 250 - 350 °C. If the final overaging temperature T3 were above 350 °C, the flat steel product would be too hot when it enters the final cooling stage, which would have a negative effect on the surface quality and thus the painting properties of the flat steel product as before. On the other hand, an final overaging temperature T3 below 250 °C would have no additional positive effect.
  • the partial work steps of work step b) are carried out in a protective gas annealing atmosphere that has a hydrogen content of 1 - 7 vol.% and also consists of nitrogen and technically unavoidable impurities.
  • a protective gas annealing atmosphere that has a hydrogen content of 1 - 7 vol.% and also consists of nitrogen and technically unavoidable impurities.
  • the dew point of the annealing atmosphere is between -10 °C and -60 °C. If the dew point of the annealing atmosphere were above -10 °C, there would also be a risk of oxide formation on the surface of the flat steel product, which is undesirable with regard to the desired surface. A dew point below -60 °C would only be possible on a large scale with great effort and would not have any additional positive effect. Optimum operating conditions are achieved when the dew point of the annealing atmosphere is between -15 °C and -50 °C.
  • a cooling rate CR3 of 1.5 - 5.0 °C/s is provided. This cooling rate CR3 is selected in such a way that deterioration of the surface quality due to oxide formation, which could occur if the cooling is too slow, is avoided in an economical manner.
  • the step c) of the method according to the invention is essential for the particularly good suitability of flat steel products for painting with optimized paint gloss.
  • This special suitability results from a Wsa value of at most 0.40 ⁇ m, typically at most 0.35 ⁇ m, in particular less than 0.30 ⁇ m, which represents a minimized waviness of the flat steel product surface.
  • the above-defined degree of skin passing D for the skin passing rolls (work step c)) provided according to the invention after the heat treatment (work steps b.)) is 0.4 - 0.7%.
  • a degree of skin passing D of less than 0.4% the deformation of the flat steel product would be insufficient for optimal forming properties.
  • the values specified according to the invention for the roughness Ra and the peak number RPc could also not be achieved.
  • a degree of skin passing D of more than 0.7% however, there would be a risk that too much hardening would be introduced into the steel strip, which in turn would have a negative effect on the forming properties.
  • degrees of skin passing D of more than 0.7% could lead to a roughness Ra that would lie outside the range of roughnesses specified according to the invention with regard to the desired surface properties.
  • the skin pass degree D can be set to at least 0.5%. If any negative effect of skin pass rolling is to be avoided, the skin pass degree D can be limited to a maximum of 0.6%. The latter is particularly useful if the alloying components of the steel from which a flat steel product is made, such as the one above, are each present in contents that are in the ranges highlighted above as being particularly advantageous.
  • the skin-pass work roll acting on the relevant surface of the flat steel product has a roughness Ra of .0 - 2.5 ⁇ m and a peak number RPc of at least 100 per cm. If the roughness Ra of the work roll were less than 1.0 ⁇ m or greater than 2.5 ⁇ m, the values of Ra and RPc according to the invention cannot be applied to the flat steel product within the limits of the invention. Forming and painting properties would deteriorate accordingly.
  • the roughness Ra of the skin-pass work roll can be set to 1.2 - 2.3 ⁇ m.
  • the peak number RPc of the skin-pass work roll surface is at least 100 per cm, with higher peak numbers RPc, such as peak numbers RPc of the work roll of at least 110 per cm, in particular more than 130 per cm, being particularly advantageous.
  • the surface structure of the peripheral surface of the skin-pass work roll that comes into contact with the flat steel product is also formed stochastically.
  • EDT Electro Discharge Texturing
  • the EDT technique is based on roughening the roll surface by spark erosion.
  • the skin-pass work roll is moved past an electrode in a tank containing a dielectric. Sparks are created in the roll surface by sparking. If the electrode is connected as an anode (+) (i.e. the current flows away from the roll towards the electrode), very inhomogeneous craters are created on the roll, which is associated with a higher number of peaks. In the opposite case (i.e. connecting the electrode as a cathode (-)), the current flows towards the roll. The results are smooth craters.
  • the cap(-) variant of the EDT technique is based on a capacitor discharge that occurs as soon as the electrode is close enough to the roll.
  • the cap process produces a stochastic texture on the work rolls because the capacitor capacitance fluctuates to different degrees (between 30% and 100%) and thus holes of different sizes are shot into the roll material.
  • the pulse (+) variant of the EDT technique is based on a principle in which the same amount of energy is always applied to the roller to be textured. This creates a stochastic surface texture with greater regularity, which nevertheless offers a sufficiently stochastic distribution of the depressions and peaks for the purposes of the invention.
  • the work roll according to the invention can optionally undergo a post-treatment.
  • the post-treatment can be carried out as a SuperFinish treatment.
  • This is a fine machining process with the aim of removing peaks that protrude above the average roughness depth or reducing their number to a minimum.
  • Possibilities for the practical implementation of the SuperFinish process are, for example, from the DE 10 2004 013 031 A1 or the EP 2 006 037 B1 known.
  • the number of peaks changes negligibly as a result of the respective post-treatment.
  • the skin-pass work rolls can be hard-chrome plated in the usual way before use in order to optimize their wear resistance.
  • the heat treatment device (work step b)) and the skin-pass rolling stand required for work step c) are set up in a line.
  • the steel flat product cooled after work step b) and emerging from the heat treatment device according to the skin-pass rolling according to work step c) is then processed in a single skin-pass pass. If, however, the skin-pass rolling is to be carried out offline, i.e. independently of the heat treatment process, several skin-pass rolling passes can also be carried out, whereby it can also be seen here that optimal results are achieved when the offline skin-pass rolling is carried out in just one pass.
  • dry skin-pass rolling can have advantages in terms of a cleaning or lubricating effect during skin-pass rolling.
  • Dry skin-pass rolling can have the advantage that the flat steel product does not come into contact with any wetting medium and, as a result, the risk of corrosion formation during subsequent storage or further processing of the flat steel product is minimized.
  • the surface texturing according to the invention which is characterized by roughness values Ra and peak numbers RPc corresponding to the specifications according to the invention, allows a significantly better paint gloss to be produced compared to a comparative product with surface texturing not according to the invention.
  • the steel flat products were heat treated in various dimensions in a continuously operating RTF heat treatment furnace, then cooled to room temperature and subsequently skin pass rolled in-line.
  • the heat treatment comprises a recrystallization annealing in which the steel strips B1 - B12 were heated to a holding temperature T1 of 835 °C ⁇ 15 °C, at which they were held for a holding time T1 of 60 s.
  • steel strips B1 - B12 were subjected to an overaging treatment. For this purpose, they were cooled from the holding temperature T1 at a cooling rate CR1 of 8.5 °C/s to an overaging start temperature T2 of 530 ⁇ 15 °C.
  • the steel strips B1 - B12 were then cooled over an aging period t2 of 302 seconds to an aging end temperature T3 of 280 ⁇ 15 °C.
  • the cooling rate CR2 with which the steel strips B1 - B12 were cooled from the aging start temperature T2 to the aging end temperature T3 was 0.82 °C/s.
  • the steel strips B1 - B12 were cooled to room temperature under the protective gas atmosphere at a cooling rate CR3 of 3.5 °C/s and were fed in a continuous flow into a four-high rolling stand with backup rolls and skin-pass work rolls intended for skin-pass rolling.
  • the skin-pass work rolls of the skin-pass rolling stand were always roughened in cap(-) mode using EDT technology and subjected to hard chrome plating in a conventional manner. All skin-pass rolling tests were carried out without the use of a skin-pass agent (dry skin-passing).
  • the parameters of the skin-pass rolling (skin-pass degree D, roughness Ra_W and peak number RPc_W of the circumferential surface of the skin-pass work rolls that comes into contact with the steel strips) as well as the width b, thickness d, yield strength Rp0.2, tensile strength Rm, elongation A80 and the n-value determined for the steel strips B1 - B12 are given in Table 2.
  • the mechanical properties were determined in a quasi-static tensile test according to DIN 6892 with the sample positioned longitudinally to the rolling direction.
  • the roughness Ra and peak count RPc determined for the surfaces of steel strips B1 - B12 are also listed in Table 2.
  • the arithmetic mean roughnesses Ra, Ra_W and peak count RPc, RPc_W were always measured according to the Steel-Iron Test Sheet (SEP) 1940 using an electrical stylus device according to ISO 3274.
  • the steel strips B11 and B12 which were not manufactured according to the invention, demonstrate the importance of the degree of skin-passing for the success of the invention.
  • the Wsa values were determined for the surfaces of the steel strips B1 - B12.
  • the results are also entered in Table 2. They confirm that the embodiments according to the invention achieve a Wsa value of ⁇ 0.40 ⁇ m and thus offer optimal conditions for a particularly good paint gloss.
  • the waviness characteristic value Wsa was measured in accordance with the Steel-Iron Test Sheet (SEP) 1941, measured on a steel sample that experienced 5% plastic elongation in the Marciniak cupping test.
  • Fig. 1 and Fig. 2 illustrate this by comparing components which were produced from a flat steel product according to the invention and a flat steel product not produced according to the invention by forming and painting.
  • the flat steel product not produced according to the invention in Fig. 2

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EP15762569.0A 2014-10-09 2015-09-09 Kaltgewalztes und rekristallisierend geglühtes stahlflachprodukt und verfahren zu dessen herstellung Active EP3204530B2 (de)

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CA2961427C (en) 2019-01-08
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