EP3610049A1 - Produit plat en acier laminé à froid, recuit sur base, et procédé de fabrication s'y rapportant - Google Patents

Produit plat en acier laminé à froid, recuit sur base, et procédé de fabrication s'y rapportant

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Publication number
EP3610049A1
EP3610049A1 EP17743317.4A EP17743317A EP3610049A1 EP 3610049 A1 EP3610049 A1 EP 3610049A1 EP 17743317 A EP17743317 A EP 17743317A EP 3610049 A1 EP3610049 A1 EP 3610049A1
Authority
EP
European Patent Office
Prior art keywords
less
cold
flat steel
temperature
annealing
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.)
Withdrawn
Application number
EP17743317.4A
Other languages
German (de)
English (en)
Inventor
Harald Dr. Hofmann
Thorsten RÖSLER
Matthias Schirmer
Andreas Dr. TOMITZ
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
ThyssenKrupp AG
ThyssenKrupp Hohenlimburg GmbH
Original Assignee
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
ThyssenKrupp Hohenlimburg GmbH
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, ThyssenKrupp AG, ThyssenKrupp Hohenlimburg GmbH filed Critical ThyssenKrupp Steel Europe AG
Publication of EP3610049A1 publication Critical patent/EP3610049A1/fr
Withdrawn legal-status Critical Current

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    • 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
    • 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
    • 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
    • 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
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/663—Bell-type furnaces
    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • 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
    • C22C38/46—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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/76—Adjusting the composition of the atmosphere
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/02—Superplasticity
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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

Definitions

  • the invention relates to a cold-rolled, bell annealed flat steel product which has a high manganese content and is in particular
  • the invention relates to a process for the preparation of
  • contents of a steel alloy are mentioned in the present text, the content data always refer to the weight (stated in% by weight), unless otherwise stated. If information on the composition of atmospheres or gas mixtures is given in the present text, the content information given for the individual components always refers to the volume (stated in% by volume), unless otherwise stated.
  • flat steel product in the present text in a rolling process produced steel strips or steel sheets and blanks derived therefrom, blanks and similar products understood, the thickness of each is substantially smaller than their width and length.
  • High-strength, cold-formable steels and steel flat products produced therefrom are used in particular for the production of body components for
  • the medium which has penetrated into the microstructure can lead to cracks due to the cooling voltages which occur as a result of its presence. For example, when welding galvanized sheet metal, it may happen that it is used as a corrosion protection coating on the
  • Steel sheet substrate melts zinc due to the high welding temperatures and penetrates at grain boundaries in the steel sheet.
  • Hydrogen-induced "delayed cracking" is caused by hydrogen entering from outside the steel material or by the hydrogen present in the material due to the production process. From WO 2012/077150 A1 a method for producing a
  • the proposed steel has the following chemical
  • Composition (in% by weight): C: 0.2-1.5%, Mn: 10-25%, Ni: ⁇ 2%, Si: 0.05-2.00%.
  • AI 0.01 - 2.0%, N: ⁇ 0.1, P + Sn + Sb + As: ⁇ 0.2, S + Se + Te: ⁇ 0.5, Nb + Co: ⁇ 1 and / or Re + W: ⁇ 1, the remainder being iron and
  • a cold-rolled strip is produced by hot and cold rolling. This is subjected to a final annealing after cold rolling, in which it is recrystallized in a continuous pass at a temperature of 900-1100 ° C. for 60-120 s. Alternatively, the final annealing may also be carried out as a bell annealing in which the cold rolled strip is held at a temperature of 700-800 ° C for 30-400 minutes.
  • Annealing atmosphere is adjusted so that their carbon activity is between 0.1 and 1, 0.
  • the nitrogen content is 90-100% and the hydrogen content of the annealing atmosphere is up to 10%, whereas the nitrogen content of the annealing atmosphere during the annealing
  • Dome annealing 0-100% and their hydrogen content may be between 0% and 100% at a dew point lower than 0 ° C and preferably between -10 ° C and -50 ° C.
  • Hood annealing suitable because the necessary there long annealing times too lead to undesirable carbide formation.
  • a strong carbide precipitation leads to a depletion of dissolved carbon, whereby the stacking fault energy changes and the material in addition to the TWIP effect can additionally have a TRIP effect, which has a detrimental effect in a forming process.
  • coarser particles or clusters of fine particles in the microstructure can act as defects in a forming process and, for example, cause surface defects.
  • bell heaters often can be used more economically than continuous furnaces, for example when processing steel strips with smaller bandwidths.
  • high-manganese steels belonging steel and thereby has a combination of properties even in the glow-annealed condition, which makes it particularly suitable for use in particular in automotive body construction.
  • An inventive cold-rolled, bell-annealed flat steel product accordingly has a yield strength Rp0.2 of more than 350 MPa, a
  • - has a microstructure characterized by an ASTM-determined particle size of at least ASTM 13 and having a carbide surface density of not more than 250 carbide particles per 1 000 pm 2 .
  • a method according to the invention for producing flat steel products according to the invention comprises the following steps: a) providing a precursor which consists of a steel which consists of (in
  • Cooling rate of at least 0.05 K / min is cooled below the cooling hood to a target cooling temperature of less than 500 ° C, wherein the total residence time under the heating and cooling hood is at most 150 h.
  • Inventive flat steel products have an optimum combination of weldability and low tendency to delayed formation of cracks with good strength and elongation at break, and a good warm and
  • step g of the method according to the invention.
  • Final annealing (step g) of the method according to the invention) are designed so that the formation of carbides, which do not serve to set a fine-grained structure during the final annealing,
  • microstructure of the microstructure is at least equivalent to ASTM 13 refers to the ASTM guideline series developed by the American Society for Testing Materials ASTM for the evaluation of the grain size of a microstructure.
  • the areal density of carbides is determined by
  • the invention prescribes an upper limit of a maximum of 250 particles per 1000 ⁇ 2 for the surface density. This upper limit is safely adhered to when observing the specifications according to the invention in the production of flat steel products according to the invention.
  • the surface density in the structure of a flat steel product according to the invention is limited to at most 250 particles per 1000 m 2 , it is ensured that the mechanical
  • a flat steel product according to the invention namely a yield strength Rp0.2 of more than 350 MPa, in particular more than 400 MPa, an elongation at break A80 of at least 35%, typically 35-45% or 35-40%, and a tensile strength Rm of at least 800 MPa, can be achieved safely and cold working of the steel flat product thus obtained can be carried out without restrictions.
  • the flat steel product according to the invention also stands for the fact that the product Rm x A80 formed from its tensile strength Rm and its elongation at break A80 is regularly greater than 32,000 [MPa%], preferably greater than 35,000 [MPa%].
  • Tensile strength Rm and breaking elongation A80 are determined according to ISO 6892-1: 2017-02.
  • a carbide surface density of more than 250 carbides per 1000 pm 2 would drastically degrade the mechanical properties and the
  • Rm * A80 product Carbide area densities of at most 200 per 1,000 pm carbide particles 2, in particular of at most 170 per 1,000 carbide pm 2 or carbide of at most 150 particles per 1,000 pm 2, therefore, prove to be particularly advantageous.
  • TWIP Twinning Induced Plasticity
  • Stacking fault energy can be set to 8 mJ / m 2 . Values above 15 mJ / m 2 increase the alloying agent costs and degrade the processing and service properties (eg weldability, corrosion resistance, etc.). To avoid these negative effects, the value of the
  • Stacking fault energy to be limited to a maximum of 13 mJ / m 2 .
  • Flat steel product C content of at least 0.1 wt .-%, in particular at least 0.2 wt .-%, at.
  • the TWIP and TRIP properties of the flat steel product according to the invention can also be specifically influenced via the respective C content, since carbon increases the stacking fault energy. Furthermore, the presence of C according to the invention increases the strength without loss of ductility. At C contents of more than 0.8% by weight, however, it may be in accordance with the invention
  • Manganese causes in steels according to the invention the required high strength and a higher stacking fault energy.
  • the contents of Mn can be used to adjust the TRIP or TWIP properties of the steels according to the invention.
  • the presence of high levels of Mn ensures that flat steel products according to the invention have the desired austenitic structure.
  • Mn content is at least 10 wt .-%, this effect is certainly achieved.
  • Mn levels does not occur in view of the properties of interest here essential Improve more. Instead, there is a risk that at over
  • the maximum tensile strength decreases.
  • Limiting the Mn content to at most 22% by weight may be advantageous in view of minimizing susceptibility to delayed cracking in combination with the Al contents of the present invention.
  • Mn contents of at least 17% by weight prove particularly favorable in this regard.
  • Optimum effects of the presence of Mn in the steel according to the invention are achieved at Mn contents of 17-22% by weight.
  • AI increases the inventively predetermined content, the corrosion resistance and reduces the tendency for delayed cracking.
  • Welding tests have furthermore proven that with steels according to the invention, the risk of solder and hot cracking compared to known alloy concepts is lowered by the fact that the Al content is kept within the ranges prescribed according to the invention.
  • the content of aluminum is limited to 0.3-2% by weight, ensuring weldability of the steels according to the invention, which is superior to that of high-manganese steels having a higher Al content.
  • the provisos for the content of AI according to the invention are chosen so that the otherwise high risk of AI risk to small work areas
  • the maximum Si content is limited to 0.5% by weight, preferably 0.3% by weight.
  • a minimum content of Si of 0.1% by weight can be provided in the flat steel product according to the invention.
  • the system Fe-Mn-C is relevant for achieving properties according to the invention.
  • coarse iron manganese carbides e.g., (FeMn) 3 C, (FeMn) 7 C 3 , Mn 4 C, Mn 2 3C 6 )
  • Carbon depletion take place, which may involve a potentially undesirable shift of the stacking fault energy and thus cause or enhance the TRIP effect.
  • the alloy of a flat steel product according to the invention is therefore adjusted so that despite the very long annealing times in one for the
  • step g annealing according to the invention
  • Chromium carbides eg Cr23C6
  • the Cr content is limited to at most 1.5% by weight, preferably to at most 0.7% by weight, in particular to at most 0.5% by weight.
  • the inventive limitation of the Cr content also causes a significant improvement in the treatability of steels of the invention. This can be done at a be advantageous flat steel product to limit the Cr content so strong that it is completely ineffective in the technical sense. This can be achieved that in an inventive
  • Steels of the invention contain at least one of
  • Micro-alloying elements V, Nb and Ti wherein the sum of the contents of these micro-alloying elements is 0.01-0.5% by weight.
  • the positive effects of V and Nb as well as, with limitations, Ti on the fine grain of the structure of a composite steel according to the invention can be used when titanium, vanadium or niobium each alone or in
  • Presence of V, Nb and / or Ti be advantageous if the sum of the contents of these elements max. 0.3 wt .-%, in particular max. 0.2 wt .-%, is.
  • V, Nb and Ti allow the formation of a fine crystalline microstructure with a high density of precipitates (e.g., VC, VN, VCN, NbC, NbN, NbCN, VNbC, VNbN, VNbCN, TiC, TiN, TiCN) and also contribute a big one Resistance to solder cracking at. Nb, V and Ti also have an influence on the delayed cracking.
  • the precipitate formed by these elements is "trapped" (ie. Trapped) in the steel flat product or penetrating it during its processing
  • the size of the grains obtained in this way in a flat steel product according to the invention in this way is comparable to the grain sizes which have continuously annealed austenitic high manganese steels in a continuous furnace. So, as mentioned above, for one
  • the annealed, cold-rolled steel flat product is guaranteed to have a microstructural fineness which corresponds to at least ASTM 13, which is generally finer than ASTM 14. It could be shown by practical experiments that regular structures are obtained, which the
  • Titanium forms as a micro-alloying element in steels according to the invention
  • Flat steel product results at Ti contents of at least 0.01 wt .-%. If the contents of Ti are too high, coarse TiN or TiC particles may form, of which cracks may be produced during cold rolling and cold forming of flat products made from steels according to the invention. In addition, the TiN or TiC particles may be destroyed during cold rolling and cold working. Cavities form between the destroyed particles, which in turn can serve as a starting point for cracks. Finally, shallow, coarse TiC particles during cold rolling and cold forming to defects on the
  • the invention provides, if any, to keep the Ti content below an upper limit of 0.5 wt .-%, with Ti contents of up to 0.15 wt .-%, in particular up to 0, 08% by weight, have proven to be particularly favorable, provided that Ti is present in effective amounts.
  • the Nb content of a flat steel product according to the invention can, if Nb alone is present, be 0.01-0.5% by weight, with contents of up to 0.15% by weight, in particular up to 0.08% by weight. -%, as have installedstallt particularly favorable.
  • the lower upper limits of the Nb content have proven to be particularly advantageous when Nb is present in combination with V and / or Ti.
  • the Nb and Ti contents optionally present in flat steel products according to the invention already lead to Nb and Ti precipitations during hot rolling and thus increase the rolling resistance in hot and cold
  • vanadium vanadium precipitates arise only at the final annealing of the finished rolled sheet and therefore do not hinder the hot and cold rolling.
  • the V content of the flat steel product according to the invention can be 0.01-0.5% by weight, whereas Nb and Ti can only be used in technically ineffective, if necessary, the
  • the S content is therefore limited to less than 0.03 wt .-% and the P content to less than 0.08 wt .-% in flat steel products according to the invention. It goes without saying that the S and P content should preferably be adjusted in each case in such a way that it has no negative effects on the properties of the flat steel product according to the invention, ie it is ineffective in the technical sense.
  • Nitrogen "N” in amounts of up to 0.1% by weight is used to form
  • the invention preferably provides an N content of at least 0.003 wt .-%, in particular at least 0.005 wt .-%, in a flat steel product according to the invention before.
  • the N content should still be set low. Al and N form precipitates that can significantly degrade the mechanical properties, in particular the elongation values. Even after a subsequent heat treatment, the AIN excretions can no longer be dissolved.
  • the maximum content of nitrogen in steels according to the invention is advantageously limited to less than 0.1% by weight, in particular at most 0.025% by weight, in particular at most 0.0170% by weight. Optimal effects of the presence of nitrogen in the flat steel product according to the invention therefore arise when the N content is 0.0030-0.0250% by weight, in particular 0.005-0.0170% by weight.
  • Mo is also a very strong carbide former, its content is preferably limited to max. 1% by weight,
  • the effect of Mo in the steel of the present invention can be safely utilized by containing Mo in contents of at least 0.1% by weight.
  • Co may optionally be present in amounts of up to 0.5% by weight, especially up to 0.2% by weight, in the flat steel product of the present invention to inhibit grain growth and thus contribute to the fine grain of the structure. This effect can be achieved at levels of at least 0.01 wt .-%.
  • boron substituted in its effect on the mechanical properties of the alloying element Mn.
  • a steel having an Mn content of 20 wt% and 0.003% boron has a similar property profile to a steel containing 25% Mn but no B. Therefore, the addition of up to 0.01% by weight of boron to a steel alloy of the present invention, while maintaining high strengths, allows for reduced Mn contents which are favorable in terms of prevention of delayed cracking and solder cracking.
  • small amounts of boron have a positive effect on the strip edge quality of a
  • Optionally added nickel can contribute to high elongation at break and increase the toughness of the steel of a flat steel product of the invention as well as the resistance to delayed cracking.
  • nickel contents to 8 wt .-%, preferably 5 wt .-% and in particular 3 wt .-%, limited.
  • Ni in the flat steel product according to the invention can be used safely when the Ni content is at least 0.1% by weight.
  • the hardness of a steel according to the invention can be increased by the formation of precipitates.
  • higher levels of Cu can cause surface defects, for example
  • the contents of Cu should preferably be restricted to less than 3% by weight, especially below 0.5% by weight.
  • the effects of Cu in the flat steel product according to the invention can be safely used if the Cu content is at least
  • compositions according to the invention can be improved.
  • Ca forms together with alumina (AI203) calcium aluminates, which are taken up in the slag and thus render the clay harmless. In this way, the risk is counteracted that alumina to clogging
  • Mg can optionally be used for deoxidizing during steelmaking and forms with O and S fine oxides, which, when welding a flat steel product according to the invention, have an advantageous effect on the ductility of the steel
  • Heat affected zone of the weld can affect. At too high levels of Mg, however, coarse precipitates may form in the structure of the flat steel product. Therefore, the optional Mg content is limited to max. 0.0015 wt .-% limited.
  • Antimony and tin can be embrittling as they too
  • Zr, Ta and W can degrade weldability and cold workability at too high a levels. Therefore, the upper limit of the sum of the contents of Zr, Ta and W in a flat steel product according to the invention to max. 2 wt .-%, in particular max. 1% by weight, limited.
  • the positive effects of Zr, Ta, W can certainly be exploited if at least one of these elements is present in amounts of 0.05% by weight.
  • the elements belonging to the group of rare earth metals may optionally have contents of up to 0.2% by weight in the invention
  • Steel flat product be present. They can be used for deoxidizing, if particularly low oxygen contents are to be adjusted, in order to prevent the emergence of unwanted Al oxides.
  • contents of rare earth metals can have a fine grain and contribute to the formation of non-metallic inclusions. Therefore, the optional content of rare earth metals in a flat steel product according to the invention is preferably limited to at most 0.05 wt .-%. The positive influence of the presence of the rare earth metals can certainly be exploited if the content of rare earth metals is at least 0.02% by weight.
  • Flat steel products according to the invention are generally characterized by a particularly high energy absorption capacity in the event of sudden loading.
  • Armor or parts for personal protection are made from flat steel products according to the invention.
  • elements made from flat steel products according to the invention can be used to produce elements which are worn directly on the body and serve to protect against bombardment or comparable impulsive attacks.
  • high-strength engine parts such as camshafts or piston rods, are determined.
  • This protective coating can be an Al or Zn-based layer, which can be composed in a manner known per se and in the same known manner
  • electrolytic galvanizing by hot-dip galvanizing, by post-annealed or galvanized coating method, as ZnNi coatings or by fire aluminizing.
  • good coating results can be achieved in particular by electrolytic galvanizing.
  • a precursor which has been prepared from a composite according to the above explanatory steel The steel may be conventionally produced in a converter steelworks or an electric arc furnace and then cast in a conventional manner into a precursor.
  • This precursor is blocks, slabs or thin slabs produced in a conventional casting process or strip cast by means of the known strip casting process.
  • Hot rolling process which is carried out inline or offline following the casting.
  • the hot strips obtained in these ways are cold rolled into cold strip in a tandem mill, a reversing mill or a Sendzimir mill.
  • the hot strip produced from a steel alloy according to the invention can first be pickled.
  • the resulting cold strip is finally annealed in the annealing furnace and can then optionally surface-coated (Z, ZE, ZF, ZMg, ZN, ZA, AS, S, thin film, tinder-preventing coatings that are suitable for hot forming and press-hardening).
  • a separate heat treatment after application of the surface coating is just as possible.
  • Cold strip according to the invention can then be provided with a coating which is used in hot or warm forging processes allows.
  • a coating which is used in hot or warm forging processes allows.
  • the high resistance of inventive flat steel products against delayed cracking can be further improved by thermal aftertreatment.
  • zinc-coated material is treated so that alloying of the zinc layer with the base material is used. Due to the thermal post-treatment Zn is alloyed in the
  • the precursor provided in step a) is reheated to a holding temperature of not less than 1100 ° C. or held at this temperature, the holding temperature preferably being at least 1150 ° C.
  • Reheating to the holding temperature will be particularly necessary if the precursor is slabs or blocks that are produced in a process separate from hot striping.
  • the precursor is fed directly to the hot rolling in a continuous operation after casting, as is the case, for example, in the known cast roll mills, poured into the thin slabs in continuously successive operations and to
  • Hot strip can be processed, the step b) also consist of a hold at the respective holding temperature by utilizing the casting heat.
  • step b) The re-heated or held in step b) to the holding temperature precursor goes through in step c) a hot rolling process in which it is hot rolled to a hot strip at a hot rolling end temperature of at least 800 ° C.
  • the number of passes during hot rolling per pass is at least 10%, in order to produce a hot-rolled under practical production conditions
  • the hot rolling end temperature should expediently not higher than 1050 ° C. As the hot rolling end temperature increases, the tensile strength and yield strength of the hot strip decrease, while the elongation values increase.
  • the Walzendtemperaturen given by the invention frame of 800 - 1050 ° C, especially 950 - 1000 ° C the cold rollability of the hot strip can be adjusted in a simple manner.
  • the hot strip obtained in step c) is wound in step d) at a maximum of 750 ° C amounting reel temperature to form a coil.
  • a maximum of 750 ° C. in particular less than 700 ° C., in particular 300-600 ° C.
  • the risk of grain boundary oxidation is minimized.
  • a grain boundary oxidation could cause material chipping and, as such, make further processing difficult or even impossible.
  • the premature precipitation of carbonitrides is avoided by reeling at the temperatures predetermined according to the invention.
  • the reel temperature should be at least 300 ° C, since underlying temperatures too
  • the contents of V are at least 80%, in particular at least 90%, and Nb, if present, at least 50%, in particular at least 60%, in dissolved form.
  • the remaining contents of V and / or Nb are as
  • the hot strip is cold rolled after the reeling and an optional surface cleaning by pickling (step e) in a conventional manner to cold strip (step f)).
  • the degree of cold rolling achieved in cold rolling is in the range of 30% to 80% to the optimized deformation and strength properties of the finished
  • step f) is followed by a final annealing in the hood furnace as operating step g) whose annealing temperatures, in order to ensure sufficient recrystallization, are at least 600 ° C. and not more than 1200 ° C., but preferably below 800 ° C., in particular between 650 and 750 ° C, lie.
  • the atmosphere in the protective hood can first with an inert gas to a non-ignitable
  • Oxygen content are exchanged (rinsing). This prevents explosive H2-air mixtures. On the other hand, an oxidation of the material can be prevented.
  • the rinsing with hydrogen is then carried out to the desired H2-inert gas mixture in which at least 50% H 2 are present.
  • the remainder of the annealing atmosphere thus formed is filled by an inert gas, which is typically N 2 .
  • the annealing at the target annealing temperature takes place in a reducing atmosphere with a low dew point of below 0 ° C., preferably below -50 ° C., in a protective gas atmosphere with at least 50% hydrogen.
  • An atmosphere of at least 50% H 2 is necessary in the annealing process in order to be able to achieve the required heating and cooling rates and to be able to comply with them reliably.
  • the dew point In the high temperature range of the annealing curve (T> 600 ° C), the dew point must be continuously less than -50 ° C, preferably less than -60 ° C, amount.
  • the heating rate with which the cold strip under the heating hood is brought to the target annealing temperature, is particularly relevant. On average, this amounts to at least 0.1 K / min, preferably at least 0.5 K / min. Subsequently, the cold-rolled strip is held for a holding time at the target annealing temperature, which is sufficient for uniform heating of the strip.
  • the holding time depends on the thermal conductivity of the flat steel product, the batch weight, the
  • Target annealing temperature, the protective gas and the furnace technology used but it should not fall below 30 minutes and can be up to 60 hours. In any case, it should be so long that a complete recrystallization is ensured even in the middle coil windings of the flat steel product.
  • the hold time is at least 5 hours, especially at least 7 hours, with maximum hold times of max. 30 hours, in particular max. 20 hours, as proven to have practical.
  • the subsequent cooling to the target cooling temperature that is, the temperature at which the cooling hood is usually drawn, i. is removed from the annealed coil, in the jargon also called "drawing temperature"
  • the target cooling temperature that is, the temperature at which the cooling hood is usually drawn, i. is removed from the annealed coil, in the jargon also called "drawing temperature"
  • the cooling rate during cooling should be as fast as possible, but on average not less than 0.05 K / min and preferably not less than 0.3 K / min.
  • the goal of rapid cooling here is not the recrystallization, since already done completely, but the substantial avoidance of carbide formation, especially when passing through critical temperature ranges during cooling, and a Kornvergröberung.
  • a protective hood can also be set, likewise in itself, over the respective coil to be annealed or the stack of coils to be annealed, which serves to adjust the gas atmosphere during the annealing process.
  • About the guard can, as also usual, first put a heating hood over which the heating to the target annealing and holding at the target annealing takes place.
  • this heating hood also in a conventional manner, be exchanged for a cooling hood, which is adapted to accelerate a controlled, for example by means of fans cooling gas flow a controlled
  • the total residence time of the cold strip under the heating and cooling hood in technical language also called "base time” (ie Bankhaubenzeit including cooling time without service time), in the inventive method up to 150 h, preferably up to 80 h.
  • base time ie Bankhaubenzeit including cooling time without service time
  • the batch obtained can be packaged in accordance with the invention hood-annealed, cold-rolled steel flat product.
  • the obtained band has the desired
  • the area fraction of precipitates with micro-alloying elements is more than 1%, preferably more than 1.5% while steel flat products made from identically assembled steels but annealed in continuous flow exhibit less than 1% areal fraction for these precipitates.
  • the high surface fractions in the heat-treated steels according to the invention stabilize the microstructure in a particular way against grain coarsening. Transmission electron microscopy bright field images (20,000 times magnification) of carbon carrier films were created, binarized, inverted and subsequently analyzed by image analysis to determine the area fractions. The preparation procedure for transmission electron microscopy is described in K. Möldner, Elektronenmikroskopische
  • the step g) can be used as open-coil annealing with wrapped wires between the coil turns.
  • Advantages of open-coil annealing are higher heating and cooling speeds of the coil inner turns and, as a result, shorter process times with even more uniform properties over
  • Fine Grain regularly meets at least ASTM 13 and finer.
  • the invention provides that the contents of V, Nb and / or Ti present in the hot strip in the hot strip form fine precipitates (VCN, NbCN, etc.) during the final annealing, which largely prevent grain growth during the final annealing process.
  • the cold strip obtained may optionally be subjected to temper rolling in a manner known per se in order to further improve its dimensional stability and its mechanical properties.
  • the flat steel product is to be delivered in the bare state, it can be used instead of a metallic coating for temporary protection
  • Table 1 shows the compositions of steels D, G, I, O, P, R, S with composition according to the invention and of steels J, K, L, M, N, Q with compositions which are not according to the invention. In each case so-called full analyzes are shown. In other words, information on the contents is also given for such elements which are present only in technically inactive contents in the respective steel, although the elements in question have no influence on the properties of the respective steel due to their low contents.
  • slabs produced from the steels listed in table 1 are at a holding temperature VWT over one for their Warming sufficient duration has been maintained and then hot rolled at a hot rolling end temperature WET to 2 mm thick hot strip.
  • the hot-rolled strips obtained were wound into coils with a coiling temperature HT and, after cooling to room temperature, descaled in a conventional pickling device. Finally, the hot-rolled strip was cold rolled to cold strip with a cold rolling grade KWG.
  • the resulting cold strips were wound into a coil and placed in a hood annealing furnace.
  • the cold strips are at a heating rate HR over a heating time resulting from the heating rate HR to the respective
  • Target annealing temperature TG have been heated, on which they have been held over a holding time HZ. Then the cold strips with a
  • the yield strength Rp0.2, the tensile strength Rm, the elongation at break A80, the product Rm x A80 and the fineness of their microstructure were determined in accordance with the relevant ASTM guideline series.
  • Carbide surface density determined and classified into classes.
  • Carbide class "1" are cold strips with a carbide surface density of less than 250 particles per 1000 ⁇ 2
  • carbide "2" are cold strips with a carbide surface density of at least 250 particles per 1000 pm 2 .
  • Table 3 summarizes the results of evaluation of the properties of the cold tapes produced in Runs 1-25.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
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Abstract

L'invention concerne un produit plat en acier laminé à froid, qui est constitué d'un acier appartenant aux aciers à teneur élevée en manganèse et qui, dans l'état recuit sur base, comprend une association de propriétés qui le rendent approprié pour être utilisé en particulier dans la construction de carrosseries d'automobiles. Selon l'invention, le produit plat en acier laminé à froid, recuit sur base possède en outre une limite d'élasticité Rp0,2 > 350 MPa, un allongement à la rupture A80 ≥ 35 % et une résistance à la traction Rm ≥ 800 MPa, une énergie de défaut d'empilement allant de 7 à 15 mJ/m2 ainsi qu'une structure comprenant une grosseur de grain ≥ ASTM 13 et une densité superficielle de carbure ≤ 250 particules de carbure pour 1 000 µm2, et est constitué d'un acier comportant (en % en poids) C : 0,1 à 0,8 %, Mn : 10 à 25 %, AI : 0,3 à 2 %, d'un élément ou de plusieurs éléments choisis dans le groupe constitué par "V, Nb, Ti", à condition que la somme des teneurs en "V, Nb, Ti" s'élève à 0,01 - 0,5 %, Si : jusqu'à 0,5 %, Cr : < 1,5 %, S : < 0,03 %, P : < 0,08 %, N : < 0, 1 %, Mo : < 2 %, Co : ≤ 0,5 %, B : < 0,01 %, Ni : < 8 %, Cu : < 5 %, Ca : ≤ 0,015 %, Mg : ≤ 0,0015 %, Sb : ≤ 0,2 %, Sn : jusqu'à 0,2 %, d'un élément ou de plusieurs éléments choisis dans le groupe constitué par "Zr, Ta, W", à condition que la somme des teneurs en Zr, Ta et W ≤ 2 %, des métaux des terres rares : ≤ 0,2 %, le reste étant du fer et des impuretés inévitables. L'invention concerne en outre un procédé de fabrication d'un tel produit plat en acier laminé à froid.
EP17743317.4A 2017-04-11 2017-07-20 Produit plat en acier laminé à froid, recuit sur base, et procédé de fabrication s'y rapportant Withdrawn EP3610049A1 (fr)

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