EP3847284B1 - Produit plat laminé à chaud en acier et procédé de fabrication - Google Patents

Produit plat laminé à chaud en acier et procédé de fabrication Download PDF

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Publication number
EP3847284B1
EP3847284B1 EP18773945.3A EP18773945A EP3847284B1 EP 3847284 B1 EP3847284 B1 EP 3847284B1 EP 18773945 A EP18773945 A EP 18773945A EP 3847284 B1 EP3847284 B1 EP 3847284B1
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Prior art keywords
gew
weight
content
atom
flat steel
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German (de)
English (en)
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EP3847284C0 (fr
EP3847284A1 (fr
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Nicholas WINZER
Richard G. Thiessen
Rainer FECHTE-HEINEN
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to a hot-rolled flat steel product with an optimized combination of high tensile strength Rm and a high hole expansion ratio ⁇ .
  • the invention also relates to a method for producing such a hot-rolled flat steel product.
  • m Y is the atomic mass of element Y
  • i EW is the content (in % by weight)
  • m i is the atomic mass of component i in the mixture with Z components.
  • the increasing demand for fuel-efficient cars is driving an increasing need for weight reduction through lightweight construction.
  • the geometric complexity of such lightweight components calls for new steels with improved durability for complex forming processes.
  • the sensitivity of the steel to edge cracks, which can form during the forming of stamped sheets, is particularly important.
  • the edge crack sensitivity of a steel is evaluated using the so-called "hole expansion test", in which a hole punched in a sheet metal sample is expanded with a mandrel until the first cracks form.
  • Materials with very anisotropic or inhomogeneous microstructures are characterized by a relatively high sensitivity to edge cracks. These include dual-phase steels, which consist of hard (e.g. martensite) and soft (e.g. ferrite) phases and have a pronounced rolling texture.
  • dual-phase steels consist of hard (e.g. martensite) and soft (e.g. ferrite) phases and have a pronounced rolling texture.
  • flat steel products with an isotropic or homogeneous microstructure are characterized by a relatively low sensitivity to edge cracking.
  • These steels include steels with a ferritic structure in which very fine precipitates can be embedded to increase strength.
  • Such a steel is from EP 1 338 665 A1 known.
  • the steel described there has a tensile strength of at least 550 MPa, which is said to be present in combination with high elongation and excellent expansion flangeability. Because of this combination of properties, such a steel is particularly suitable for the production of complex-shaped automobile chassis parts.
  • the EP 1 338 665 A1 mentions that a hot-rolled steel strip that meets these requirements (in % by weight) contains ⁇ 0.15% C, 0.02 - 0.35% Ti and 0.05 to 0.7% Mo and should have a microstructure that should essentially consist of ferrite with single-phase and fine precipitations, which are dispersed in the ferrite matrix with a grain size of less than 10 nm.
  • EP 1 338 665 A1 specifically mentioned hot-rolled sheet steel should consist of (in % by weight) ⁇ 0.06% C, ⁇ 0.5% Si, 0.5-2.0% Mn, ⁇ 0.06% P, ⁇ 0.005 S, ⁇ 0.1% Al, ⁇ 0.006% N, 0.02 - 0.10% Ti, 0.05 - 0.6% Mo and the balance Fe.
  • the steel sheet composed in this way should have precipitations in its single-phase structure consisting of ferrite, the grain size of which is ⁇ 10 nm and of which 5 ⁇ 10 4 / ⁇ m 3 per volume unit are present in the structure.
  • the steel flat products that meet these requirements and are marketed under the name "Nanohiten” have a ferritic structure in which TiC precipitations with a size of ⁇ 5 nm are embedded, which ensure the high strength and low edge cracking sensitivity of the steel.
  • the fineness of the TiC precipitations is made possible by the addition of Mo, which prevents the TiC precipitations from becoming coarser.
  • ⁇ is composed in part of the strain energy due to the mismatch between the carbides and the surrounding ferrite matrix. Reducing the strain energy promotes a coherent interface between the carbides and the ferrite matrix and prevents coarsening of the carbides.
  • Mo or W atoms are incorporated into the carbide and replace the Ti, Nb or V atoms there. In this connection, it is known that both the inclusion of the Mo and W atoms lead to the reduction of the strain energy.
  • a high-strength hot-rolled steel sheet which contains (in % by weight) 0.035 - 0.12% C, ⁇ 0.1% Si, ⁇ 1.2% Mn, ⁇ 0.03% P, ⁇ 0.005% S, ⁇ 0.1% Al , ⁇ 0.01% N, 0.14 - 0.30% Ti, ⁇ 3.0% Cu and the balance Fe and unavoidable impurities.
  • the Cr content of the steel is adjusted to ⁇ 0.08% in order to achieve optimum corrosion resistance of the steel sheet, with Cr contents which are as low as possible being found to be particularly advantageous in this regard.
  • the structure of the hot-rolled steel sheet composed in this way consists of at least 95% by area of ferrite with an average grain diameter of ⁇ 7 ⁇ m, with carbide precipitations with an average diameter of less than 8 nm being present in the structure and the structure containing less than 0.1 vol. -% contains cementite.
  • the steel sheet produced in this way should have a tensile strength of at least 780 MPa.
  • the invention was based on the object of specifying a hot-rolled flat steel product that can be produced cost-effectively, which has high strength and at the same time is suitable for forming into complex shaped steel parts, in particular components for the body and chassis of vehicles suitable.
  • Sheet metal blanks made of steel with a tensile strength of 550 MPa and more are increasingly being used for the construction of body and chassis components.
  • the sheet metal blanks are often subjected to particularly high deformation at their cut edges, which can lie on the outer edge of the sheet metal blank and/or on holes and recesses. These deformations can occur when using materials with heterogeneous microstructures such. B. dual-phase steels, lead to failure of the edges.
  • a flat steel product should be provided which, due to its homogeneous microstructure, is particularly suitable for the production of body and chassis components and, due to its low sensitivity to edge cracking, makes it possible to design these components in such a way that the load to be carried by them is safely exceeded by the strong deformed edges can be initiated.
  • the invention has achieved this object in that such a flat steel product has at least the features specified in claim 1 .
  • a method that achieves the above-mentioned object according to the invention is specified in claim 13 .
  • a hot-rolled flat steel product according to the invention is therefore characterized in that it has a tensile strength Rm of at least 550 MPa and a hole expansion ratio ⁇ of at least 30%, with its microstructure consisting of at least 90% by area of ferrite and the remainder being up to 10% by area. consists of pearlite or cementite and carbonitride precipitates with an average diameter of no more than 10 nm are embedded in the structure of the steel flat product.
  • the Ti OUT , V OUT , Nb OUT and Cr OUT contents of the precipitations, which are given in atomic %, can be determined, for example, by energy-dispersive X-ray micro-area analysis ("EDX").
  • EDX energy-dispersive X-ray micro-area analysis
  • a flat steel product according to the invention has a high tensile strength Rm of at least 550 MPa, in particular at least 660 MPa, and it regularly also achieves tensile strengths of at least 780 MPa or even at least 960 MPa.
  • the hole expansion ratio ⁇ determined according to ISO 16630:2017 for a flat steel product according to the invention is in each case at least 30%, in particular at least 50%, with hole expansion ratios ⁇ of at least 60% also being able to be represented.
  • a flat steel product according to the invention has a particularly favorable ratio of hole expansion capacity to strength.
  • high hole expansion ratios ⁇ are achieved even with high strengths. This is reflected in high values for the product Rm ⁇ of tensile strength Rm and hole expansion ⁇ .
  • a flat steel product according to the invention regularly achieves Rm ⁇ values of at least 30,000 MPa ⁇ %, in particular at least 40,000 MPa ⁇ % or even at least 50,000 MPa ⁇ %.
  • the microstructure of a flat steel product according to the invention consists of at least 90% by area of ferrite, a microstructure that is completely ferritic in the technical sense with carbonitride precipitations being particularly advantageous.
  • the appropriate alloy layer, cementite and pearlite can form in the structure, the proportions of which can be up to 10% by area. may amount.
  • the mean grain size of the structure is typically 3-10 ⁇ m, in particular 3-8 ⁇ m.
  • the Cr-containing carbonitride precipitates embedded in the structure of a flat steel product according to the invention based on the contents of Ti, Nb or V provided according to the invention are present with an average particle diameter of at most 10 nm.
  • the fineness of the precipitates makes a decisive contribution to the desired combination of high strength and good hole expansion capacity.
  • the mean particle diameter of the precipitates present in the flat steel product according to the invention is therefore preferably at most 7 nm, in particular at most 5 nm.
  • the alloy selected according to the invention lays the foundation for the optimized properties of a hot-rolled flat steel product according to the invention.
  • the carbon (C) provided in the alloy steel of the present invention is mainly fixed in the precipitates.
  • the concentration of the C dissolved in the mixed crystal is thereby minimized.
  • a C content of more than 0.02% by weight, in particular more than 0.05% by weight, is necessary in order to achieve a high precipitation density and thus to achieve the required tensile strength of at least 550 MPa. Too high a C content, in turn, would lead to the formation of larger pearlite contents in the structure, which would reduce ductility and increase sensitivity to edge cracking.
  • the C content is therefore limited to a maximum of 0.3% by weight, in particular a maximum of 0.15% by weight, with the negative effects of the presence of C being able to be avoided particularly reliably if the C content of the steel is at most is 0.10% by weight.
  • the contents of the elements determining the ratio Verh1 are set within the content ranges specified according to the invention for each of these elements such that the ratio Verh1 is 0.5 ⁇ Verh1 ⁇ 2.0, with the ratios Verh1 being 0.7-1.5 or 0.8-1.3 have turned out to be particularly favorable with regard to the desired properties of a flat steel product according to the invention.
  • Manganese (Mn) is an element that contributes to the strength of steel by forming solid solutions. Mn also suppresses the formation of pearlite and cementite and in this way promotes the formation of Cr-containing carbonitride precipitations based on the contents of Ti, Nb or V provided according to the invention. For this reason, the steel according to the invention has an Mn content of at least 0 2% by weight, in particular more than 0.3% by weight, preferably at least 0.5% by weight, particularly preferably 1.0% by weight or 1.3% by weight.
  • the upper limit of the Mn content is set to at most 2.5% by weight, with lower Mn contents of at most 2.0% by weight, in particular at most 1.7% by weight, the possible negative effects of the presence of Mn avoid particularly safe.
  • Silicon (Si) can optionally be added in amounts to suppress the formation of pearlite in the structure of a flat steel product according to the invention.
  • a content of at least 0.05% by weight of Si is required. Excessively high levels of Si would impair the surface quality of the flat steel product according to the invention.
  • the Si content is therefore limited to a maximum of 0.7% by weight, with Si contents of up to 0.25% by weight, in particular up to 0.1% by weight, prove to be particularly favorable with regard to avoiding the negative influences of the presence of Si and also enable subsequent batch galvanizing of the product according to the invention. If there are special requirements for batch galvanizing, it is particularly preferable to dispense with an Si alloy and select a maximum Si content of 0.03% by weight.
  • Si With contents of up to 0.7% by weight, Si also contributes to solid solution strengthening, so that higher Si contents can definitely be useful if lower requirements are placed on the surface quality and/or batch galvanizing ability. With Si contents above 0.7% by weight, however, the rollability of the steels according to the invention is adversely affected too much and growths can occur on the rolls during rolling.
  • Aluminum (Al) can also be added as an optional element for suppressing the generation of pearlite. Because Al is usually used to deoxidize the melt, an Al content of at least 0.01% by weight is unavoidable in the usual production of the steel from which a flat steel product according to the invention is made. However, too high an Al content can have a negative effect on castability. Therefore, the upper limit of the Al content is limited to at most 1.0% by weight, preferably at most 0.7% by weight, particularly at most 0.5% by weight.
  • Cr chromium
  • Cr can be used to prevent the coarsening of the precipitates.
  • This requires a Cr content of at least 0.05% by weight, preferably at least 0.06% by weight Cr or, particularly preferably, more than 0.08% by weight or at least 0.10% by weight .
  • the detection limit for Cr in steels of the type according to the invention is in the range of 0.03% by weight, whereas Cr contents of at least 0.05% by weight can be specifically set in the steelworks. On the other hand, lower Cr contents are regarded as ineffective.
  • the effectiveness of the addition of Cr provided according to the invention is also demonstrated by the fact that a low atomic ratio Verh2 forms in the precipitates.
  • the atomic ratio of Ti to Cr in (Ti,Cr)(C,N) precipitates which are about 10 nm in size, is more than 10.
  • Previous investigations have shown that when Mo or W for the formation of carbonitrides in precipitates with a size of about 10 nm, the atomic ratio of Ti to the Mo or W present in each case is at most 4. This shows that by including Cr in the precipitates in a steel flat product according to the invention, the strain energy of the precipitate is reduced more than when Mo or W is included.
  • the upper limit of the content of Cr in a flat steel product according to the invention is set to at most 0.5% by weight, preferably at most 0.25% by weight or at most 0.15% by weight. It should be noted here that the Cr contents of a flat steel product according to the invention are adjusted in such a way that no pure Cr carbides are present in the flat steel product according to the invention.
  • micro-alloying elements titanium (Ti), niobium (Nb) and vanadium (V) are essential for the formation of precipitations in the structure of the flat steel product according to the invention.
  • V vanadium
  • the precipitates formed by Ti, Nb or V are not present in the flat steel product according to the invention as pure carbides, but rather as carbonitrides if nitrogen "N" is present in the alloy. It is known that carbides and nitrides formed with Ti, Nb and V have very different solubilities in austenite and ferrite. That is why they form at very different temperatures.
  • Ti or Nb are only added in contents of a maximum total of 0 0.01% by weight, preferably at most 0.005% by weight, which are in the range of unavoidable impurities in which neither Ti nor Nb have an effect on the properties of the steel.
  • Ti and Nb can be added alone or together since the formation temperatures at which Ti or Nb precipitates form are close enough to allow timely precipitation of both elements. Therefore, when Ti or Nb is added, V is only tolerated as an unavoidable impurity, which can be present in contents of up to 0.01% by weight, preferably up to 0.005% by weight.
  • the value X WEIGHT is limited to 0.5% by weight. In this way, it is avoided that, for example, increased Nb contents lead to crack formation during continuous casting or during slab cooling or reheating. At the same time, only a certain content of micro-alloying elements is required for the desired strength. If this is exceeded, there is only a slight further increase in strength. In addition, the average diffusion distances decrease, which increases the risk of the formation of undesired large precipitations. For these reasons, the Nb, Ti or V contents of the steel of a steel flat product according to the invention are advantageously adjusted in such a way that the value X GEW is not higher than 0.25% by weight.
  • Phosphorus (P) is unfavorable for the weldability of a steel flat product according to the invention.
  • the P contents of a flat steel product according to the invention are therefore limited to a maximum of 0.02% by weight, in particular less than 0.02% by weight, with P contents of at most 0.010% by weight, in particular less than 0.005% by weight. -%, are particularly favorable.
  • the S content must be limited to at most 0.005% by weight, particularly less than 0.003% by weight, preferably less than 0.0015% by weight.
  • N is present in the flat steel product according to the invention as an impurity that is unavoidable due to production.
  • the precipitations embedded in the structure of a steel flat product according to the invention are present as carbonitrides in the form of (Ti,Cr)(C,N); (Nb,Cr)(C,N); (V,Cr)(C,N) or (Ti,Nb,Cr)(C,N).
  • nitrogen "N" is present, Ti, Nb and V in the simultaneous presence of C form nitrides or carbonitrides preferentially with N. Therefore, in practice, under the technically and economically viable conditions, the uptake of N in the excretions is unavoidable.
  • the lowest possible N content should be aimed for, since N-dominated carbonitrides are often very coarse and angular, which is why they do not contribute to hardening but act as crack initiators.
  • the upper limit of the N content is therefore set at 0.01% by weight, preferably 0.005% by weight.
  • the upper limit of the Ca content according to the invention to 0.01% by weight, in particular at most 0.005% by weight, preferably at most 0.002% by weight.
  • the contents of Mo and W are limited to a maximum of 0.05% by weight, in particular a maximum of 0.04% by weight, preferably 0.03% by weight, since these elements are present in a flat steel product according to the invention for the reasons explained above are not needed.
  • B must not exceed 0.002% by weight, in particular 0.001% by weight, preferably 0.0005% by weight, in order to prevent the movement of the phase boundaries being slowed down by B segregated on them and thus the formation of Ti, Nb and V carbides and carbonitrides.
  • the allowable upper limit of the Cu content in the flat steel product according to the invention is 0.1% by weight, in particular less than 0.04% by weight or less than 0.02% by weight.
  • Ni, Sn, As, Co, Zr and rare earths, in particular La and/or Ce are also not required as alloying elements in the flat steel product according to the invention and, if they are nevertheless detectable in the flat steel product according to the invention, are among the unavoidable impurities.
  • the Ni content is at most 0.1 wt%
  • the Sn content is at most 0.05 wt%
  • the As content is at most 0.02 wt%
  • the Co content is at most 0.02% by weight
  • the Zr content to a maximum of 0.002% by weight, in particular a maximum of 0.0002% by weight
  • the content of the rare earth elements, such as La and Ce to a maximum of 0.002% by weight in each case %, in particular a maximum of 0.0002% by weight.
  • O is also undesirable in the flat steel product according to the invention, since a Oxide coating, which can result from the presence of higher O contents, would have a negative effect both on the mechanics and on the castability and rollability of the steel flat product.
  • the maximum permissible O content is therefore set at 0.005% by weight, preferably at 0.002% by weight.
  • H is very mobile in the interstitial spaces in the steel and can lead to cracking in the core, particularly in high-strength steels when cooling from hot rolling.
  • the H content of a flat steel product according to the invention should therefore be as low as possible, but in any case not more than 0.001% by weight, in particular not more than 0.0006% by weight or not more than 0.0004% by weight, with H Contents of at most 0.0002% by weight are particularly desirable.
  • the steel alloyed according to the invention in accordance with the explanations given above in connection with the composition of a flat steel product according to the invention is, after it has been melted, cast into a preliminary product which, in the case of the classic production route, will be a slab of conventional dimensions.
  • the steel can also be made into a continuous cast by direct hot rolling a thin slab as a preliminary product in a casting-rolling plant or a cast strip as a preliminary product in a strip casting plant.
  • the precursor is heated to at least 1150 °C or kept at this temperature.
  • a high heating temperature is required in order to dissolve carbides and nitrides already present in the pre-product. If the heating temperatures are too low, the alloying elements remain bound in the precipitations, so that no new precipitations can be formed. For economic reasons, the heating temperature is limited to a maximum of 1350 °C.
  • the preliminary product is hot-rolled in a conventional manner, with the final temperature of hot-rolling having to be at least 880 °C. If the final hot rolling temperatures are too low, the rolling forces increase disproportionately and the desired isotropy of the material is lost due to the effects of thermomechanical rolling. End temperatures above 980 °C are technically not feasible.
  • the hot-rolled steel strip leaving the hot-rolling train is cooled at a cooling rate of 20 - 400 °C/s to a coiling temperature in the range of 560 - 690 °C.
  • a cooling rate of at least 20 °Cls is required to avoid as much as possible the formation of perlite and cementite. Cooling rates of more than 400°C/s are technically not feasible.
  • Coiling temperatures of 560 - 690 °C cover the temperature range in which precipitates with an average size of less than 10 nm, in particular less than 5 nm, are formed. At higher temperatures, the average size of the carbonitrides is more than 10 nm, which means that the target properties of the flat steel product according to the invention can no longer be achieved.
  • a targeted formation of small Precipitations whose size is less than 7 nm, in particular less than 5 nm, can be brought about by coiling temperatures of 580-670.degree. C., in particular 590-650.degree. At coiling temperatures below 580 °C, carbonitrides would no longer be separated and their strength-increasing effect would be absent.
  • the atomic ratio Verh2 is of particular importance.
  • a Verh2 ratio of 2-20 in the precipitates is required in order to prevent coarsening of the precipitates during cooling in the coil after coiling when producing a flat steel product according to the invention.
  • the maximum size of the carbonitrides of at most 10 nm specified according to the invention and, associated with this, the minimum strength and the desired high hole expansion ratio could not be achieved.
  • the ratio Verh2 is less than 2
  • the edges of the precipitations have a significantly higher Cr content than the core of the precipitations.
  • the “core” is defined as that area of the excretions that makes up approximately 50% of the area of the excretion in microscopy and is closest to the centroid of the area.
  • the remaining area of the excretion is defined as the edge.
  • the Cr content at the edge is significantly higher than in the core area and Cr no longer has any effect in terms of preventing coarsening of the precipitations.
  • melts A - S alloyed according to the compositions given in Table 1 were produced and cast into slabs.
  • the melts not according to the invention and their contents of certain alloying elements that deviate from the requirements of the invention are underlined in Table 1 (steels B, D, E, F, N, O).
  • the tensile strength Rm, the upper yield point ReH, the lower yield point ReL and the elongation A50 were determined on the hot-rolled steel strips obtained in this way in accordance with DIN EN ISO 6892-1:2017.
  • the hole expansion ⁇ was determined according to ISO 16630:2017, the product Rm ⁇ ⁇ was formed and the average particle size of the precipitations and the ratio Verh2 were determined.
  • Verh2 of X OUT (see Table 1) to Cr OUT (in atomic %) in the precipitates is given in Table 2.
  • Verh2 increases with increasing coil temperature and increasing precipitate size.
  • the correlation between Verh2 and the precipitation diameter indicates that Cr prevents the coarsening of the carbides.
  • Example A is a reference composition used to study the effect of coiling temperature (see Examples A1 to A7). With this composition, the optimal mechanical-technological properties were achieved at coiling temperatures in the range of 590 - 650 °C.
  • Steels G and H are also based on example steel A, but the ratio Verh1 was varied here.
  • the variation of Verh1 in the range from 0.8 to 1.2 has no negative impact on the mechanical-technological properties under similar production specifications (see examples G14, G15, H17 and H18).
  • the tests based on steels G and H were also used to study the influences of the heating temperature EWT and the finish rolling temperature ET on the properties of the steel strip obtained. Here it was shown that too low a heating temperature EWT or final rolling temperature ET leads to the formation of coarse precipitations or an anisotropic structure and thus poor mechanical-technological properties (see examples G13 and H16).
  • Steels I and J are Nb concepts and steels K and L are V concepts, from which steel strips were produced with different coiling temperatures (see Examples 119 to K28).
  • Examples I to L contain different contents of Si and Al.
  • the optimum mechanical and technological properties were achieved at coiling temperatures of 590 - 650 °C.
  • Steels M to O have a similar X GEW concentration to steel A but different combinations of Ti, Nb and V.
  • the steel strip produced in example M30 based on steel M (Ti and Nb) has comparable mechanical and technological properties to those Steel strips that have been produced on the basis of steel A at similar coiling temperatures.
  • Steel P has a very high ratio Verh1.
  • the steel strips consisting of steel P were produced in tests P33 - P35 with different cooling rates. If the cooling rate was too low, too much pearlite was formed, with the result that the mechanical-technological properties were severely impaired (see example P33).
  • Steel Q has a high Al content but is otherwise relatively low alloyed.
  • the steel R is relatively highly alloyed.
  • Steel strips were produced from the steels Q and R under optimal conditions. These tests show that very different strengths can be achieved with high Rm ⁇ values, provided the ratio Verh1 is within the target range.
  • Steel S was produced as a high-purity laboratory melt and processed with increased heating and hot-rolling temperatures as well as a very high cooling rate in order to validate the influences of varying manufacturing parameters.
  • TEM transmission electron micrographs
  • All samples show fine (Ti,Cr)(C,N) precipitates (darker particles).
  • the diameter of the precipitates increases with increasing coiling temperature, so that the diameters of the particles in Examples A3, A4 and A5 are on average below 5 nm, this being the case particularly clearly in Example A3.
  • the precipitates are not recognizable as individual particles and are in the form of agglomerates.
  • Example A1 contained no (Ti,Cr)(C,N) precipitates.

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Claims (15)

  1. Produit plat laminé à chaud en acier présentant une résistance à la traction Rm d'au moins 550 MPa, déterminée selon la norme DIN EN ISO 6892-1:2017, un rapport d'expansion de trou λ d'au moins 50%, déterminé selon la norme ISO 16650:2017, et une structure constituée à raison d'au moins 90% en surface de ferrite et, comme reste, à raison de jusqu'à 10% en surface, de perlite ou de cémentite, dans laquelle des précipités de carbonitrure présentant un diamètre moyen d'au plus 10 nm sont incorporés, constitué par un acier qui est constitué par, en % en poids, 0,02-0,5% de C, ≤ 0,7% de Si, ≤ 1,0% d'Al, 0,2-2,5% de Mn, 0,05-0,5% de Cr, ≤ 0,02% de P, ≤ 0,005% de S, ≤ 0,01% de N, ≤ 0,1% de Cu ainsi que par au moins un élément formant les précipités de carbonitrure du groupe "Ti, Nb, V" et, comme reste, par du fer et des impuretés inévitables avec les critères suivants :
    - dans le cas où V est présent, la somme des teneurs TiPDS en Ti et NbPDS en Nb est limitée à au plus 0,01% en poids ;
    - dans le cas où Ti et/ou Nb est/sont présent(s), la teneur en V VPDS est d'au plus 0,01% en poids ;
    - pour une concentration totale XPDS en % en poids = TiPDS + (VPDS/1,06)+(NbPDS/1,94), la relation 0,02% ≤ XPDS ≤ 0,5% est d'application ;
    - pour un rapport de quantités Rapp1 = (XAT + CrAT)/(CAT + NAT), la relation 0,5 ≤ Rapp1 ≤ 2,0 est d'application, avec XAT = TiAT + VAT + NbAT ;
    TiAT correspondant à la teneur en Ti TiPDS recalculée en % en atome, VAT correspondant à la teneur en V VPDS recalculée en % en atome, NbAT correspondant à la teneur en Nb NbPDS recalculée en % en atome, CrAT correspondant à la teneur en Cr CrPDS recalculée en % en atome, CAT correspondant à la teneur en C CPDS recalculée en % en atome et NAT correspondant à la teneur en N NPDS recalculée en % en atome et les teneurs TiPDS, VPDS, NbPDS, CrPDS, CPDS et NPDS étant à chaque fois indiquées en % en poids, les impuretés inévitables étant limitées à au plus 0,01% en poids de Ca, 0,05% en poids de Mo, 0,05% en poids de W, 0,002% en poids de B, 0,1% en poids de Cu, 0,1% en poids de Ni, 0,05% en poids de Sn, 0,02% en poids d'As, 0,02% en poids de Co, 0,002% en poids de Zr, à chaque fois 0,002% en poids de terres rares, 0,005% en poids d'a et 0,001% en poids d'H.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que pour un rapport de quantités Rapp2 = XDÉP/CrDÉP, la relation 2 ≤ Rapp2 ≤ 20 est d'application, avec XDÉP en % en atome = TiDÉP + VDÉP + NbDÉP et
    TiDÉP : teneur en Ti des dépôts, en % en atome
    VDÉP: teneur en V des dépôts, en % en atome
    NbDÉP : teneur en Nb des dépôts, en % en atome
    CrDÉP: teneur en Cr des dépôts, en % en atome.
  3. Produit plat en acier selon la revendication 1, caractérisé en ce que sa teneur en Cr est supérieure à 0,08% en poids.
  4. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que la grosseur moyenne des grains de sa structure ferritique est de 3-10 µm.
  5. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que sa teneur en Mn est d'au moins 1,5% en poids.
  6. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que sa teneur en Si est d'au moins 0,05% en poids.
  7. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que la valeur XPDS vaut 0,05-0,25% en poids.
  8. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que pour le rapport de quantités Rapp1, la relation 0,7 ≤ Rapp1 ≤ 1,5 est d'application.
  9. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que pour le rapport de quantités Rapp2, la relation 2,3 ≤ Rapp2 ≤ 15 est d'application.
  10. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que le diamètre moyen des dépôts est ≤ 5 nm et en ce que, pour le rapport de quantités Rapp2, la relation 2,5 ≤ Rapp2 < 5 est d'application.
  11. Produit plat en acier selon l'une quelconque des revendications 1 à 9, caractérisé en ce que le diamètre moyen des dépôts est > 5 nm et en ce que, pour le rapport de quantités Rapp2, la relation 5 ≤ Rapp2 < 15 est d'application.
  12. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que son rapport d'expansion de trou λ est d'au moins 50%.
  13. Procédé pour la fabrication d'un produit plat en acier selon l'une quelconque des revendications précédentes, comprenant les étapes de travail suivantes :
    a) fusion d'un acier constitué par, en % en poids, 0,02-0,5% de C, ≤ 0,7% de Si, ≤ 1,0% d'Al, 0,2-2,5% de Mn, 0,05-0,5% de Cr, ≤ 0,02% de P, ≤ 0,005% de S, ≤ 0,01% de N, ≤ 0,1% de Cu ainsi que par au moins un élément formant les précipités de carbonitrure du groupe "Ti, Nb, V" et, comme reste, par du fer et des impuretés inévitables, avec les critères suivants :
    - dans le cas où V est présent, la somme des teneurs TiPDS en Ti et NbPDS en Nb est limitée à au plus 0,01% en poids ;
    - dans le cas où Ti et/ou Nb est/sont présent(s), la teneur en V VPDS est d'au plus 0,01% en poids ;
    - pour une concentration totale formée par la teneur respective en Ti TiPDS, la teneur respective en V VPDS et la teneur respective en Nb NbPDS de l'acier XPDS en % en poids = TiPDS + VPDS/1,06)+(NbPDS/1,94), la relation 0,02% ≤ XPDS 0,5% est d'application ;
    - pour un rapport de quantités Rapp1 = (XAT + CrAT)/(CAT+NAT), la relation 0,5 ≤ Rapp1 ≤ 2,0 est d'application, avec XAT = TiAT + VAT + NbAT,
    TiAT correspondant à la teneur en Ti TiPDS recalculée en % en atome, VAT correspondant à la teneur en V VPDS recalculée en % en atome, NbAT correspondant à la teneur en Nb NbPDS recalculée en % en atome, CrAT correspondant à la teneur en Cr CrPDS recalculée en % en atome, CAT correspondant à la teneur en C CPDS recalculée en % en atome et NAT correspondant à la teneur en N NPDS recalculée en % en atome et les teneurs TiPDS, VPDS, NbPDS, CrPDS, CPDS et NPDS étant à chaque fois indiquées en % en poids, les impuretés inévitables étant limitées à au plus 0,01% en poids de Ca, 0,05% en poids de Mo, 0,05% en poids de W, 0,002% en poids de B, 0,1% en poids de Cu, 0,1% en poids de Ni, 0,05% en poids de Sn, 0,02% en poids de As, 0,02% en poids de Co, 0,002% en poids de Zr, à chaque fois 0,002% en poids de terres rares, 0,005% en poids d'a et 0,001% en poids d'H,
    b) coulée de l'acier en une ébauche, telle qu'une brame, une brame mince ou une bande coulée,
    c) conditionnement thermique de l'ébauche à une température de 1150-1550°C,
    d) laminage à chaud de l'ébauche en un produit plat laminé à chaud en acier à une température finale de laminage à chaud de 880-980°C,
    e) refroidissement du produit plat laminé à chaud en acier obtenu à une vitesse de refroidissement de 20-400°C/s jusqu'à une température de bobine de 560-690°C,
    f) bobinage de la bande chaude refroidie à la température de bobinage en une bobine.
  14. Procédé selon la revendication 13, caractérisé en ce que la température de bobinage est de 590-650°C.
  15. Élément, en particulier élément de carrosserie ou composant de châssis, caractérisé en ce qu'il est fabriqué par façonnage d'un produit plat en acier selon l'une quelconque des revendications 1-12.
EP18773945.3A 2018-09-06 2018-09-06 Produit plat laminé à chaud en acier et procédé de fabrication Active EP3847284B1 (fr)

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DE102021105357A1 (de) 2021-03-05 2022-09-08 Thyssenkrupp Steel Europe Ag Kaltgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung
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EP1338665B1 (fr) 2000-10-31 2018-09-05 JFE Steel Corporation Tole d'acier laminee a chaud presentant une resistance elevee a la traction et procede de fabrication
JP5903883B2 (ja) 2011-12-27 2016-04-13 Ｊｆｅスチール株式会社 耐食性に優れためっき用高強度熱延薄鋼板とその製造方法

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