EP3555337B1 - Plaque d'acier laminer a chaud et son procede de fabrication - Google Patents

Plaque d'acier laminer a chaud et son procede de fabrication

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Publication number
EP3555337B1
EP3555337B1 EP17821500.0A EP17821500A EP3555337B1 EP 3555337 B1 EP3555337 B1 EP 3555337B1 EP 17821500 A EP17821500 A EP 17821500A EP 3555337 B1 EP3555337 B1 EP 3555337B1
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EP
European Patent Office
Prior art keywords
temperature
flat steel
hot
steel product
content
Prior art date
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EP17821500.0A
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German (de)
English (en)
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EP3555337A1 (fr
Inventor
Manuela Irnich
Rainer FECHTE-HEINEN
Jens Horstmann
Richard Georg THIESSEN
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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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
    • C21D1/22—Martempering
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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    • 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
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
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    • 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
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    • 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
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    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C21D2211/008—Martensite
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0447—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment following hot rolling
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    • 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
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    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium

Definitions

  • the invention relates to a hot-rolled flat steel product that possesses optimally coordinated mechanical properties, such as high tensile strengths Rm, high yield strengths Rp, and high elongation at break A, combined with good formability, which is characterized by a high hole expansion value, for which the abbreviation " ⁇ " (“lambda”) has been introduced. Furthermore, hot-rolled flat steel products according to the invention are characterized by good fatigue strength and wear resistance.
  • the invention also relates to a method for producing such a flat steel product.
  • alloy contents refers to weight or mass, unless explicitly stated otherwise.
  • the slabs undergo hot rolling, in which they are rolled in a temperature range below the recrystallization temperature but above the A3 temperature.
  • the resulting hot strip is quenched at a quenching rate of at least 20 °C/s to a quench stop temperature that lies in the temperature range between the temperature Ms, at which martensite formation begins, and the temperature Mf, at which martensite formation is complete.
  • the quench stop temperature is in the range of more than 200 °C and less than 400 °C.
  • the quenched hot strip undergoes a partitioning treatment to transfer carbon from the martensitic to the austenitic microstructure components. Finally, the treated hot strip is cooled to room temperature. Key parameters of the quenching and partitioning treatment remain open.
  • JP 2016 194158 A reveals a high-strength steel sheet with hole expansion properties.
  • the object of the invention was to provide a flat steel product with a greater sheet thickness and an optimized combination of properties.
  • the invention has solved this problem by the hot-rolled flat steel product specified in claim 1.
  • the solution according to the invention to the above-mentioned object consists in that the work steps specified in claim 7 are carried out during the production of a flat steel product according to the invention.
  • the invention provides a hot-rolled flat steel product and a process suitable for its production.
  • Carbon "C” is present in the steel melt processed according to the invention in amounts of 0.1 - 0.3 wt.%.
  • C plays a major role in austenite formation.
  • a sufficient C concentration enables full austenitization at temperatures of up to 930 °C, which are below the final rolling temperatures usually selected for hot rolling of steels of the type in question.
  • a portion of the residual austenite is already stabilized by the carbon provided according to the invention.
  • further stabilization takes place during the later partitioning step.
  • the strength of the martensite which is reduced during the first cooling step ( ⁇ Q) or during the The C content of the final cooling step ( ⁇ P2) also depends heavily on the C content of the steel composition processed according to the invention.
  • the martensite initiation temperature shifts to increasingly lower temperatures with increasing C content.
  • Excessively high C content would therefore lead to difficulties in production, as the quench temperature to be achieved would be shifted to very low temperatures.
  • the C content of a steel processed according to the invention contributes most significantly to a higher CE value compared to other alloying elements, which negatively impacts weldability.
  • the CE value indicates which alloying elements negatively influence the weldability of the steel.
  • Manganese (Mn) is an important element for the hardenability of steel. At the same time, manganese reduces the tendency toward undesirable pearlite formation during cooling. These properties enable the creation of a suitable initial microstructure of martensite and retained austenite after the first quenching with cooling rates ⁇ 100 K/s according to the process of the invention. An excessively high Mn concentration negatively affects elongation and the CE value, i.e., weldability. Therefore, the Mn content is limited to 1.5–3.0 wt.%. An optimized coordination of the strength properties can be achieved by setting the Mn content to 1.9–2.7 wt.%.
  • Silicon "Si” plays an important role in suppressing pearlite formation and controlling carbide formation. The formation of cementite would bind carbon, making it unavailable for further stabilization of the residual austenite. On the other hand, an excessively high Si content impairs elongation at break and surface quality through accelerated red scale formation. A similar effect can be triggered by alloying with Al. A minimum of 0.7 wt.% Si is required to achieve the product properties intended according to the invention. The desired microstructure can be achieved particularly reliably if Si contents of at least 1.0 wt.% are present in the flat steel product according to the invention. Due to the desired elongation at break, the upper limit of the Si content is specified at 1.8 wt.% Si.
  • the Si content can also be set to 0.5 - 1.1 wt.%, in particular 0.7 - 1.0 wt.%, as explained in the following paragraph.
  • Al is used for deoxidation and to bind any nitrogen that may be present. Furthermore, Al can also be used, as already mentioned, to suppress cementite, but it is not as effective as Si. However, an increased addition of Al significantly increases the austenitizing temperature, which is why cementite suppression is preferably achieved solely by Si. In this case, an Al content of 0 - 0.03 wt.%, which is favorable with regard to the austenitizing temperature, is provided if Si is simultaneously present in amounts of at least 1.0 wt.%.
  • the Si content is limited, for example, to achieve optimized surface quality, i.e., set to values between 0.5 - 1.1 wt.%, preferably 0.7 - 1.0 wt.%
  • Al must be added with a minimum content of 0.5 wt.% to suppress cementite.
  • the Al content can be particularly To ensure the safe production of deoxidized melts, the Al content should be set to values of at least 0.01 wt.%.
  • the Al content is limited to a maximum of 1.5 wt.%, preferably a maximum of 1.3 wt.%, to avoid problems during steel casting.
  • Phosphorus "P” has a negative impact on weldability. Its content in the hot-rolled strip according to the invention or in the melt processed according to the invention is therefore limited to a maximum of 0.1 wt.%, although P contents of up to 0.02 wt.%, especially less than 0.02 wt.%, can be advantageous.
  • S sulfur
  • MnS or Mn, Fe manganese
  • the S content is limited to a maximum of 0.03 wt.%, although limiting the S content to a maximum of 0.003 wt.%, especially less than 0.003 wt.%, can be advantageous.
  • N Nitrogen
  • the N content should therefore be less than 0.008 wt.%.
  • very low N contents of, for example, less than 0.0010 wt.% can be achieved.
  • the N content can preferably be set to at least 0.0010 wt.%, and particularly preferably to at least 0.0015 wt.%.
  • alloying elements summarized in the group "Cr,Mo,Ni,Nb,Ti,V,B” can optionally be added individually, together or in various combinations in accordance with the instructions explained below in order to adjust certain properties of the flat steel product according to the invention.
  • Chromium is an effective pearlite inhibitor and can thus reduce the required minimum cooling rate.
  • Cr is added to the added to the steel processed according to the invention or to the steel of the hot-rolled flat steel product according to the invention.
  • a minimum content of 0.10 wt.% Cr, preferably 0.15 wt.% Cr is required.
  • the strength is greatly increased by the addition of Cr, and there is also the risk of pronounced grain boundary oxidation.
  • the formation of chromium oxides in the near-surface region of the steel makes coatability more difficult and undesirable surface defects can occur. These surface defects can lead to reduced fatigue strength and thus to premature failure of the material under cyclic loading.
  • the Cr content is limited to a maximum of 0.30 wt.%, preferably a maximum of 0.25 wt.%.
  • Molybdenum (Mo) is also a very effective element for suppressing pearlite formation. To achieve this effect, at least 0.05 wt.%, especially at least 0.1 wt.%, can be optionally added to the steel. Additions of more than 0.25 wt.% are not advisable from an effectiveness perspective.
  • the steel of a flat steel product according to the invention may optionally also contain microalloying elements such as vanadium "V”, titanium “Ti” or niobium “Nb", which contribute to increased strength through the formation of very finely distributed carbides (or carbonitrides in the presence of nitrogen "N”).
  • microalloying elements such as vanadium "V”, titanium “Ti” or niobium “Nb", which contribute to increased strength through the formation of very finely distributed carbides (or carbonitrides in the presence of nitrogen “N”).
  • the presence of Ti, V, or Nb also leads to the freezing of grain and phase boundaries after the hot rolling process during the partitioning step, which promotes the desired combination of strength and formability through grain refinement.
  • the minimum content at which a significant effect is noticeable is 0.02 wt.% for Ti, 0.01 wt.% for Nb, and 0.1 wt.% for V.
  • the upper limit is set at 0.07 wt% for Ti, 0.06 wt% for Nb and 0.3 wt% for V.
  • B boron
  • a hot-rolled steel flat product according to the invention has a tensile strength Rm of 800 - 1500 MPa, a yield strength Rp of more than 700 MPa and an elongation at break A of 7 - 25%, wherein the tensile strength Rm, the yield strength Rp and the elongation at break A are determined according to DIN EN ISO 6892-1-2009-12.
  • the hot strip according to the invention is characterized by a very good Formability, which is reflected in a hole expansion ⁇ of more than 20% as determined according to DIN ISO 16630.
  • Hot-rolled strip manufactured according to the invention and, in particular, produced by the process according to the invention has a microstructure of tempered and untempered martensite with portions of retained austenite, whereby bainite, polygonal ferrite, non-polygonal ferrite, and cementite may also be present in small portions in the microstructure.
  • the martensite portion of the microstructure is at least 85 area%, preferably at least 90 area%, of which at least half is tempered martensite.
  • the proportion of retained austenite in a hot-rolled flat steel product according to the invention is accordingly at most 15 vol.
  • up to 15 area% of bainite, up to 15 area% of polygonal ferrite, up to 5 area% of cementite, and/or up to 5 area% of non-polygonal ferrite may be present in the microstructure, each at the expense of the retained austenite.
  • the proportion of polygonal ferrite as well as the proportion of non-polygonal ferrite is 0 area%, since in this case the values for hole expansion are particularly high due to the delayed crack formation in a predominantly martensitic structure with uniform hardness.
  • the microstructure of the hot-rolled strip according to the invention is very fine, making its assessment using conventional light-optical microscopy almost impossible. Therefore, assessment using scanning electron microscopy (SEM) and a magnification of at least 5000x is recommended. However, the maximum permissible retained austenite content is difficult to determine even at high magnification. Therefore, quantitative determination of retained austenite using X-ray diffraction (XRD) according to ASTM E975 is recommended.
  • SEM scanning electron microscopy
  • XRD X-ray diffraction
  • the structure of the hot-rolled flat steel product according to the invention is characterized by a defined, local misorientation in the crystal lattice. This applies in particular to the desired proportion of primary martensite, ie the Martensite formed during the initial cooling.
  • This local misorientation is quantified by the so-called "Kernel Average Misorientation,” or “KAM” for short, which is greater than or equal to 1.50°, preferably greater than 1.55°.
  • KAM Kernel Average Misorientation
  • the KAM value should be at least 1.50°, because then a homogeneous deformation resistance is present due to uniform lattice distortion in the grain. This prevents locally limited pre-damage to the multiphase microstructure at the beginning of deformation. If the KAM value is below 1.50°, the microstructure is excessively tempered, resulting in strength properties outside the desired range according to the invention.
  • the distortion of the crystal lattice is crucial for the mechanical properties of a steel product designed and manufactured according to the invention.
  • This lattice distortion represents a measure of the initial resistance to plastic deformation, which determines the properties due to the desired strength ranges.
  • a suitable method for measuring and thus quantifying lattice distortion is electron backscatter diffraction (EBSD).
  • EBSD electron backscatter diffraction
  • EBSD generates and combines a large number of local diffraction measurements to detect small differences and patterns, as well as local misorientations in the microstructure.
  • a common EBSD evaluation method in practice is the aforementioned kernel average misorientation (KAM), in which the orientation of a measurement point is compared with that of neighboring points.
  • KAM kernel average misorientation
  • a threshold value typically 5°
  • neighboring points are assigned to the same (distorted) grain.
  • the neighboring points are assigned to different (sub-)grains. Due to the very fine microstructure, a maximum step size of 100 nm is recommended for the EBSD evaluation method.
  • the KAM is always calculated in relation to the current measuring point and its third-nearest neighboring point. evaluated.
  • a product according to the invention must then have a KAM average value from a measuring range of at least 75 ⁇ m x 75 ⁇ m of ⁇ 1.50°, preferably >1.55°.
  • Fig. 1 The process-technical production of hot strip according to the invention is shown schematically in Fig. 1 and is explained in detail below.
  • a pre-product is cast from the melt alloyed according to the invention, which will typically be a slab or thin slab.
  • the precursor product is heated to a heating temperature TWE that lies within the temperature range in which austenite forms in the steel according to the invention.
  • the heating temperature TWE of the steels according to the invention should therefore be at least 1000 °C in the process according to the invention, since excessive hardening occurs at lower heating temperatures during the subsequent hot rolling process. At the same time, the heating temperature should not exceed 1300 °C to avoid partial melting of the slab surfaces.
  • the heating temperature TWE is preferably at least 1150 °C, because in this way structural inhomogeneities that could arise, for example, from manganese segregation can be reliably avoided.
  • the heating itself and further process steps starting from this temperature range can be operated economically.
  • Heating to the temperature TWE can be carried out in a conventional pusher or walking beam furnace.
  • a conventional thin-slab caster in which the steel composition according to the invention is cast into thin slabs with a thickness of typically 40-120 mm (see DE 4104001 A1 )
  • heating can also take place in the furnace connected directly to the casting system after casting.
  • the precursor product is hot-rolled into hot strip with final thicknesses between 1.5 and 10 mm.
  • hot rolling may involve roughing, possibly in reverse, in a roughing stand, followed by finish rolling in a so-called finishing stage, which consists of several, typically five or seven, rolling stands passed through in a continuous sequence.
  • the final rolling temperature TET of the hot rolling process must be set according to the requirement TET ⁇ (A3 - 100°C). In practice, it has proven advantageous to set the final rolling temperature TET at least equal to the A3 temperature of the respective steel composition being processed or above the A3 temperature. For example, it may be advantageous to set the final rolling temperature TET in the range of 850 - 950°C.
  • the steel After hot rolling, the steel is quenched in a first quenching step starting from the hot rolling end temperature TET at a high cooling rate to a quench temperature TQ.
  • the cooling rate ⁇ Q is more than 30 K/s.
  • the quench temperature TQ targeted during cooling is not lower than room temperature. On the other hand, it is at most 100 °C higher than the martensite start temperature TMS, at which the martensitic transformation begins.
  • the desired proportion of primary martensite would not form. Instead, excessive amounts of ferrite, pearlite, or bainite would be formed. which are each above the proportions specified according to the invention for the flat steel product according to the invention. If the proportions of these microstructural components are too high, the stabilization of the residual austenite during the partitioning treatment following cooling is prevented. In addition, the primary martensite formed would relax so much during further cooling through self-tempering that the KAM values desired according to the invention would not be achieved. In addition, at quench temperatures TQ above the limit of TMS + 100 °C specified according to the invention, inhomogeneities and thus segregation of individual elements can occur more frequently, which in turn could lead to the formation of an undesirable row-like microstructure.
  • An optimal microstructure with regard to the desired formability of the final product can thus be achieved, particularly with regard to the primary martensite formed during quenching, by ensuring that the quench temperature TQ is at most 100 °C higher than the martensite start temperature TMS and at least equal to the martensite start temperature TMS - 250 °C, so that: TMS ⁇ 250 ° C ⁇ TQ ⁇ TMS + 100 ° C .
  • a quench temperature TQ between the martensite start temperature TMS and the martensite start temperature TMS -150 °C has proven particularly favorable.
  • the flat steel product quenched to the quench temperature TQ can be wound into a coil after step e) in order to ensure temperature constancy and homogeneity throughout the material.
  • the temperature of the flat steel product may not fall below the quench temperature TQ by more than 80 °C.
  • the hot-rolled flat steel product After cooling, the hot-rolled flat steel product, cooled to the quench temperature TQ, is kept in a temperature range of TQ - 80 °C to TQ + 80 °C for a period of 0.1 - 48 hours in order to ensure the targeted transformations and, when using micro-alloying elements, the formation of finely distributed carbides.
  • the aim of this work step is to form a martensitic structure which can contain up to 15 vol.% residual austenite.
  • Practical tests have shown that with hot-rolled strip made from the steel specified according to the invention, this result is generally already achieved with holding times of up to 2.5 hours. Therefore, with regard to energy utilization, it may be expedient to limit the holding time to a maximum of 2.5 hours. Longer holding times are harmless and are therefore selected if this makes sense taking into account the available plant technology or its utilization. Holding times of at least 1 hour have also proven expedient in order to achieve complete temperature homogeneity of the material and the associated formation of up to 15 vol.% residual austenite in the martensitic structure.
  • Maintaining within the temperature range from TQ -80 °C to TQ +80 °C can be done both isothermally, i.e. at a constant temperature, and non-isothermally, i.e. at a decreasing or increasing or oscillating temperature.
  • the maximum permissible cooling rate is 0.05 K/s.
  • the rate at which temperature changes occur during the hold is typically in the range of -0.05 K/s to +0.01 K/s, based on the respective quench temperature TQ.
  • the holding conditions must be selected so that the specified temperature window of TQ +/-80 °C is not exceeded despite the temperature changes that occur.
  • the aim of this process step is to create a microstructure with martensite, tempered martensite and, if necessary, retained austenite.
  • step h) the steel flat product is brought to a partitioning temperature TP starting from the temperature set in step g) or, if the partitioning temperature TP is increased by +/- 80°C, by the
  • the partitioning temperature TP should preferably be at least as high as the quench temperature TQ, but preferably at least 50 °C higher, especially at least 100 °C higher.
  • the partitioning temperature TP is lower than the temperature after step g) (quench temperature TQ +/-80 °C), the carbon mobility is too low to stabilize the retained austenite. Furthermore, the tempering effect of the primary martensite does not occur to the desired extent.
  • the partitioning temperature TP for the steels according to the invention is a maximum of 500 °C, in particular a maximum of 470 °C, in order to achieve the optimal tempering state.
  • the partitioning time tPT is between 30 minutes and 30 hours to allow sufficient redistribution of carbon without causing the decomposition of the residual austenite present in the structure.
  • the partitioning time tPT is composed of the time tPR (heating ramp) required for the heating process and the time tPl provided for the isothermal holding, where tPl can also be zero.
  • the proportions of the times tPR and tPl in the partitioning time tPT are variable as long as the total partitioning time tPT specified according to the invention is maintained.
  • heating in step h) occurs with a coiled steel flat product
  • the hot strip is ideally heated at a heating rate ⁇ P1 of up to 0.075 K/s. Heating rates ⁇ P1 below 0.005 K/s appear impractical. At heating rates ⁇ P1 > 1 K/s, unacceptable temperature differences may occur between the outer, middle, and inner turns of the coiled hot strip. These differences should not exceed 85 °C to ensure homogeneous material properties across the entire length of the hot-rolled flat steel product produced according to the invention.
  • the formation of pearlite and the decomposition of retained austenite are specifically suppressed by an adjusted holding time at a defined temperature.
  • the time tPl is zero.
  • the desired microstructure is achieved solely during the heating process, i.e., during the time tPR.
  • the partitioning temperature can also be equal to the temperature of the flat steel product after step g) (quenching temperature TQ+/-80°C), so that no time tPR is required for heating the flat steel product.
  • Partitioning (step h) is carried out batchwise in a bell annealing furnace, which allows for slow heating of the hot strip, which in this case is necessarily wound into a coil.
  • Annealing in a bell-type annealing furnace offers the following advantages: Lower temperature gradients occur during heating, resulting in a more homogeneous heating of the material. The maximum heating rate depends on the target temperature and the respective charging weight in the bell-type furnace. If heating is too fast, the strip is not heated completely and evenly. This leads to an uneven microstructure, in particular to a different martensite morphology, which affects the further partitioning behavior and thus the This is particularly the case with heating units that are directly integrated into the hot strip mill (continuous annealing or induction inline annealing, such as in US 2014/0299237 ). An uneven microstructure leads to poor formability, in particular to poor hole expansion.
  • the maximum heating rate ⁇ P1 during the partitioning step is 0.075 K/s to achieve uniform properties across both the length and width of the flat steel product. Otherwise, local irregularities associated with reduced forming properties, particularly impaired hole expansion, occur. It is particularly advantageous to heat at a maximum heating rate ⁇ P1 of 0.03 K/s to ensure optimal homogeneity of the final microstructure and thus the best hole expansion and fatigue strength properties.
  • the minimum heating rate ⁇ P1 is 0.005 K/s, preferably 0.01 K/s.
  • a further advantage of using a bell annealing furnace is that the target annealing temperatures can be set more precisely than in continuous annealing furnaces. Annealing also takes place in a protective gas mixture, which prevents harmful effects on the hot strip surface, such as oxidation. Hydrogen, nitrogen, and mixtures of hydrogen and nitrogen are used as protective gases. Furthermore, partitioning the process in a separate bell annealing furnace allows for cycle time decoupling from the hot rolling mill. This enables better utilization of hot rolling capacities.
  • step h If a bell annealing furnace is used in step h), the flat steel product should be transported to the bell annealing furnace during step g) taking into account the requirements explained above with regard to maintaining the temperature TQ.
  • step h the hot-rolled flat steel product is cooled to room temperature. Cooling in step i) should be carried out at a cooling rate ⁇ P2 of no more than 1 K/s to control the stress in the flat steel product. For economic reasons, a minimum cooling rate of 0.01 K/s may be used.
  • the flat steel product obtained or obtained according to the invention may undergo a surface treatment such as descaling, pickling or the like.
  • a metallic coating may also be appropriate to apply a metallic coating to the flat steel product in a conventional manner to protect against corrosion. This can be achieved, for example, by electrolytic galvanizing.
  • a flat steel product according to the invention or produced according to the invention is processed in the hot-rolled state. This allows for flat steel product thicknesses of 1 mm and more, with typical thicknesses in the range of 1.5 - 10 mm.
  • the hot-rolled flat steel product according to the invention is particularly suitable for structural lightweight construction, as the higher strength allows for a reduction in material thickness.
  • Conventional higher- and ultra-high-strength grades are unsuitable for more heavily formed parts because they lack the necessary formability.
  • the flat steel product according to the invention enables component integration, since the good formability despite high strength makes it possible to replace several components of an assembly with a component made of the hot-rolled flat steel product according to the invention.
  • the increased hole expansion is particularly advantageous for automotive chassis components, significantly facilitating the formation of through-holes.
  • Insufficient hole expansion was previously considered a disqualification criterion for use in chassis components for grades with strengths above 800 MPa.
  • the cyclic loading typical of chassis components requires that the material also ideally exhibit good fatigue strength.
  • the mechanical properties of the inventive flat steel products can be used for the lightweight construction of stamped parts.
  • Component integration also offers the possibility of eliminating joining operations, thus simultaneously increasing production reliability and generating cost advantages.
  • the use of the flat steel products according to the invention in the construction industry is also advantageous, as they offer improved formability while maintaining high strength. Furthermore, they have a higher yield strength ratio compared to other flat steel products of comparable strength levels. These properties ensure improved structural stability under unforeseen load conditions such as earthquakes, impact loads, or exceeding the maximum load specified in the design.
  • test melts A - O with the compositions given in Table 1 were melted.
  • Table 2 shows the A3-determined temperatures according to equation (1) and the martensite start temperatures TMS determined according to equation (2) for steels A - O.
  • melts A - O were cast into slabs, each of which was subsequently heated to a reheating temperature (TWE).
  • TWE reheating temperature
  • the heated slabs were then conventionally rolled into hot strip with a thickness of 2 - 3 mm.
  • the hot rolling in a conventional manner, comprised a roughing and a finish rolling step, each of which was terminated at a final hot rolling temperature (TET).
  • the resulting hot-rolled steel strips were quenched at a cooling rate ⁇ Q to a quench temperature TQ, at which they were subsequently held for a duration tQ.
  • Those hot strips that were subsequently subjected to batch annealing were wound into a coil between quenching and holding.
  • the hot strips were heated at a heating rate ⁇ P1 over a duration tPR to a partitioning temperature TP and held there for a duration tPl.
  • Table 3 lists the aggregate used for the partitioning treatment (step h)) and the respective difference between the quenching temperature TQ and the partitioning temperature TP for each of the experiments. When a bell-type annealer was used, it is also indicated whether it was used to increase (“heat”) the temperature or to maintain (“maintain”) the temperature.
  • Table 5 shows the proportions of polygonal ferrite "pF”, non-polygonal ferrite “npF”, tempered martensite “AM”, cementite “Z”, retained austenite “RA”, untempered martensite “M” and bainite “B” in the microstructure as well as the KAM value of the hot strips obtained in tests 1 - 47.
  • test 7 which is not inventive, the value required for hole expansion according to the invention was not achieved because the quenching was stopped at temperatures that were too high.
  • tests 3-6 resulted in an increase in hole expansion of 7% to 38% compared to the non-inventive comparative test 7, while simultaneously avoiding an excessive bainite content.
  • tests 3-5 only traces of bainite were present, and in test 6, 10 area% bainite was present, whereas in test 7, 20 area% bainite was present in the microstructure.
  • Tests 11 - 13 show the necessity of rolling above the A3 temperature and of maintaining a sufficiently long holding time t Q .
  • melts D and E With melts D and E, it was possible to produce a material with a strength of 1028 - 1500 MPa and a hole expansion of 22 - 87%.
  • melt F not according to the invention, the formation of cementite could not be prevented despite a sufficiently long holding time (see test 29).
  • Melt M as an example of a variant with optimized surface quality, exhibits a reduced Si content and a simultaneously increased Al content.
  • a simultaneously low TET see test 45
  • a 5 area % polygonal ferrite content forms in the microstructure, allowing for low yield strengths combined with good hole expansion.
  • melt N was produced as a laboratory melt in a vacuum furnace. With the high-purity melt N, it was possible to produce a material with very good hole expansion (see test 46).
  • Test 47 with melt analysis O shows that if all production parameters are observed, a material with just sufficient values for elongation and hole expansion can be produced.
  • Table 1 melt C Si Mn Al P S N Cr V Mon Ti Nb B N A* 0.145 0.24 2.15 0.660 0.011 0.0017 0.0033 0.71 - - 0.028 0.027 - - B 0.186 1.52 2.54 0.025 0.009 0.0021 0.0021 0.25 - - 0.041 - 0.0019 - C 0.249 1.71 1.89 0.019 0.011 0.0015 0.0025 0.17 - 0.102 0.027 - - - D 0.201 1.46 1.98 0.028 0.013 0.0013 0.0032 - - 0.100 0.017 - - - E 0.179 1.51 2.05 0.021 0.007 0.0025 0.0029 0.14 - - - - 0.13 F* 0.150 0.29 1.82 0.027 0.015 0.0027 0.0041 0.37 - 0.101 0.0

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Claims (11)

  1. Produit plat en acier laminé à chaud constitué d'un acier ayant la composition suivante, en % en poids : C: 0,1 à 0,3 % Mn: 1,5 à 3,0 % Si: 0,5 à 1,8 % Al: jusqu'à 1,5 % P: jusqu'à 0,1 % S: jusqu'à 0,03 % N: jusqu'à 0,008 %
    éventuellement un ou plusieurs éléments du groupe « Cr, Mo, Ni, Nb, Ti, V, B » ayant les teneurs suivantes : Cr : 0,1 à 0,3 % Mo : 0,05 à 0,25 % Ni : 0,05 à 2,0 % Nb : 0,01 à 0,06 % Ti : 0,02 à 0,07 % V : 0,1 à 0,3 % B : 0,0008 à 0,0020 %
    un reste de fer et d'impuretés inévitables dues à la fabrication,
    - dans lequel le produit plat en acier présente une résistance à la traction Rm allant de 800 à 1500 MPa, une limite d'élasticité Rp supérieure à 700 MPa, un allongement à la rupture A allant de 7 à 25 % et un élargissement de trou λ supérieur à 20 %,
    - dans lequel la structure du produit plat en acier est à au moins 85 % en surface de martensite, dont au moins la moitié est de la martensite revenue, dans lequel le reste de la structure va respectivement jusqu'à 15 % en volume d'austénite résiduelle, jusqu'à 15 % en surface de bainite, jusqu'à 15 % en surface de ferrite polygonale, jusqu'à 5 % en surface de cémentite et/ou jusqu'à 5 % en surface de ferrite non polygonale,
    - dans lequel la structure du produit plat en acier présente une désorientation moyenne du noyau « KAM » qui est d'au moins 1,50°, mesurée comme indiqué dans la description, et
    - dans lequel le produit plat en acier présente une épaisseur dans la plage allant de 1,5 à 10 mm.
  2. Produit plat en acier laminé à chaud selon la revendication 1, caractérisé en ce que sa teneur en Al est d'au plus de 0,03 % en poids.
  3. Produit plat en acier laminé à chaud selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Si est d'au moins 1,0 % en poids.
  4. Produit plat en acier laminé à chaud selon la revendication 1, caractérisé en ce que sa teneur en Al est d'au moins 0,5 % en poids.
  5. Produit plat en acier laminé à chaud selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Si est d'au plus 1,1 % en poids.
  6. Procédé pour la fabrication d'un produit plat en acier réalisé conformément à l'une des revendications précédentes, comprenant les étapes de travail suivantes :
    a) fusion d'un alliage d'acier ayant la composition suivante, en % en poids : C: 0,1 à 0,3 % Mn: 1,5 à 3,0 % Si : 0,5 à 1,8 % Al: jusqu'à 1,5 % P: jusqu'à 0,1 % S: jusqu'à 0,03 % N: jusqu'à 0,008 %
    éventuellement un ou plusieurs éléments du groupe « Cr, Mo, Ni, Nb, Ti, V, B » ayant les teneurs suivantes : Cr : 0,1 à 0,3 % Mo : 0,05 à 0,25 % Ni : 0,05 à 2,0 % Nb : 0,01 à 0,06 % Ti : 0,02 à 0,07 % V : 0,1 à 0,3 % B : 0,0008 à 0,0020 %
    un reste de fer et d'impuretés inévitables dues à la fabrication ;
    b) coulée de la masse fondue pour former un précurseur, tel qu'une brame ou une brame mince ;
    c) chauffage continu du précurseur à une température de chauffage TWE allant de 1000 à 1300 °C ;
    d) laminage à chaud du précurseur chauffé en continu pour former un feuillard chaud d'une épaisseur allant de 1,5 à 10 mm, dans lequel le laminage à chaud se termine à une température finale de laminage à chaud TET à laquelle TET ≥ (A3 - 100 °C) s'applique, dans lequel « A3 » désigne la température A3 respective de l'acier ;
    e) première trempe du feuillard chaud en partant de la température finale de laminage à chaud TET, à une vitesse de refroidissement θQ supérieure à 30 K/s, jusqu'à une température de trempe TQ à laquelle (TMS - 250 °C) ≤ TQ ≤ TMS s'applique, dans lequel « RT » désigne la température ambiante et « TMS » la température de transformation martensitique de l'acier, et dans lequel la température de transformation martensitique TMS est déterminée comme suit : TMS [°C] = 462 - 273 % de C - 26 % de Mn - 13 % de Cr - 16 % de Ni - 30 % de Mo avec % de C = teneur en C de l'acier, % de Mn = teneur en Mn de l'acier, % de Cr = teneur en Cr de l'acier, % de Ni = teneur en Ni de l'acier, % de Mo = teneur en Mo de l'acier, respectivement en % en poids ;
    f) enroulement éventuel du produit plat en acier trempé à la température de trempe TQ pour former une bobine ;
    g) maintien du produit plat en acier refroidi à la température de trempe TQ dans une plage de températures allant de TQ -80 °C à TQ +80 °C pendant une durée allant de 0,1 à 48 heures ;
    h) chauffage du produit plat en acier à une température de partitionnement TP ou maintien du produit plat en acier à une température de partitionnement TP au moins égale à la température TQ+/-80 °C existante du produit plat en acier après l'étape de travail g) et au plus égale à 500 °C, pendant un temps de partitionnement tPT allant de 0,5 à 30 heures, dans lequel, au cas où un chauffage a lieu, la vitesse de chauffage θP1 est d'au plus 0,075 K/s, et dans lequel l'étape de travail h) est réalisée dans un recuit sous cloche ;
    i) refroidissement du produit plat en acier jusqu'à la température ambiante ;
    j) décalaminage éventuel du produit plat en acier ;
    k) revêtement éventuel du produit plat en acier.
  7. Procédé selon la revendication 6, caractérisé en ce que la vitesse de chauffage θP1 est de 0,03 K/s au maximum.
  8. Procédé selon l'une des revendications 6 ou 7, caractérisé en ce que, à l'étape de travail c), la température de chauffage TWE va de 1150 à 1250 °C.
  9. Procédé selon l'une des revendications 6 à 8, caractérisé en ce que la température de trempe TQ est comprise entre la température de transformation martensitique TMS et une température inférieure d'au plus 150 °C à la température de transformation martensitique TMS.
  10. Procédé selon l'une des revendications 6 à 9, caractérisé en ce que la durée de maintien à l'étape de travail g) est de 2,5 heures au maximum.
  11. Procédé selon l'une des revendications 6 à 10, caractérisé en ce que la température de partitionnement TP à l'étape de travail h) est supérieure d'au moins 50 °C à la température de trempe TQ.
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CZ308468B6 (cs) * 2019-07-30 2020-09-02 Západočeská Univerzita V Plzni Způsob výroby součástí z ocelí kalením s vyrovnáním teplot na teplotu Ms
CN112522580A (zh) * 2019-09-19 2021-03-19 宝山钢铁股份有限公司 一种马氏体钢带及其制造方法
CN114761583B (zh) * 2019-12-13 2024-04-05 安赛乐米塔尔公司 经热处理的冷轧钢板及其制造方法
WO2021123877A1 (fr) * 2019-12-17 2021-06-24 Arcelormittal Tôle d'acier laminée à chaud et son procédé de fabrication
US20230065607A1 (en) * 2020-01-22 2023-03-02 Nippon Steel Corporation Steel sheet and producing method therefor
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KR102478025B1 (ko) 2022-12-15
JP2020509161A (ja) 2020-03-26
CA3046108A1 (fr) 2018-06-21
CN110088326B (zh) 2022-06-24
US20200071785A1 (en) 2020-03-05
MX2019006862A (es) 2019-08-14
WO2018108653A1 (fr) 2018-06-21
KR20190095340A (ko) 2019-08-14
US11371113B2 (en) 2022-06-28
CN110088326A (zh) 2019-08-02
JP7193454B2 (ja) 2022-12-20
EP3555337A1 (fr) 2019-10-23

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