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EP2366035B1 - Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication - Google Patents

Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication Download PDF

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Publication number
EP2366035B1
EP2366035B1 EP09760726.1A EP09760726A EP2366035B1 EP 2366035 B1 EP2366035 B1 EP 2366035B1 EP 09760726 A EP09760726 A EP 09760726A EP 2366035 B1 EP2366035 B1 EP 2366035B1
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EP
European Patent Office
Prior art keywords
steel strip
manganese steel
rolled
hot
cold
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EP09760726.1A
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German (de)
English (en)
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EP2366035A1 (fr
Inventor
Reinhold Schneider
Ludovic Samek
Enno Arenholz
Klemens Mraczek
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Voestalpine Stahl GmbH
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Voestalpine Stahl GmbH
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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
    • 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
    • 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • 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

Definitions

  • the invention relates to an austenitic manganese steel strip and to a method for producing austenitic manganese steel strips. Furthermore, the invention relates to a manganese steel sheet with a deformed, in particular stretched or deep-drawn sheet steel section.
  • Manganese austenites are lightweight structural steels that are particularly strong and elastic at the same time.
  • the weight reduction afforded by the higher strength makes manganese austenite a material of great potential in the automotive industry. Because through lighter bodies fuel consumption can be reduced, with a high elasticity and stability for the production of the body parts and their crash behavior are important.
  • TRIP-steels (TRANSformation Induced Plasticity), which are increasingly used in the automotive industry, are already known.
  • High-alloyed TRIP steels reach high tensile strengths of up to more than 1000 MPa and can have elongations of up to about 30%. Due to these high mechanical properties thinner plates and thus a reduction in body weight can be achieved in vehicle construction.
  • TRIP steel consists of several phases of iron-carbon alloys, mainly ferrite, bainite and carbon-rich residual austenite.
  • the TRIP effect is based on the deformation-induced transformation of residual austenite into martensite. This remodeling of the crystal structure results in a simultaneous increase in strength and formability in product manufacture or in product use in the event of a crash.
  • the TRIP effect can be specifically influenced by admixing the alloying elements aluminum and silicon.
  • TWIP TWinning Induced Plasticity
  • the particular ductility of TWIP steels can be caused by different mechanisms in the crystal structure.
  • the extensibility can be promoted by lattice defects in the crystal structure, at which the crystal structure can fold-induced induced, whereby the folding mechanism runs on a mirror plane and regularly mirrored crystal areas (so-called twins) arise.
  • twins Different types of twins can be distinguished.
  • further effects such as the occurrence of slip bands can influence the mechanical properties.
  • TWIP steels Due to their high ductility, TWIP steels are excellently suited for the production of metal sheets in the automotive industry, especially for accident-relevant areas of the body. TWIP steels have an austenitic structure and are characterized by a high manganese content (usually over 25%) and relatively high alloying additions of aluminum and silicon.
  • hot and cold rolled austenitic manganese steel tapes are from the US 2008/0035248 A1 which have a maximum phosphorus content of 0.05% and whose mean particle sizes are given as ⁇ 10 ⁇ m for hot-rolled manganese steel or ⁇ 5 ⁇ m for cold-rolled manganese steel.
  • One object of the invention is to provide a steel with improved mechanical properties.
  • good weldability of the steel and / or good formability should be achievable.
  • the invention aims to provide a method for producing a steel with improved mechanical properties, in particular high ductility in combination with high tensile strength, and in particular a good weldability and a good formability.
  • the steel according to the invention is characterized, inter alia, by the fact that with a carbon content in% by weight of about 0.4% ⁇ C ⁇ 1.2%, a manganese content of about 12.0% ⁇ Mn ⁇ 25.0 % is available.
  • the percentages of chemical constituents in this document always refer to percentages by weight, phosphorus, which increases the yield strength or tensile strength, reduces the elongation at break, promotes brittleness, lowers austenite stability, hampers cementite precipitation, and usually weldability decreases, is alloyed according to the invention in a relatively high proportion of at least 0.03%. It turned out in the case of an extensive omission of the alloying element aluminum (Al ⁇ 0.05%) with this alloy concept, high mechanical properties and a surprisingly good weldability with very good formability of the manganese steel strip produced can be achieved.
  • a product of elongation at break in MPa and tensile strength in percent of over 65,000 MPa%, especially over 70,000 MPa% can be obtained.
  • this product is above 75,000 MPa% and may be above 80,000 MPa%, in particular also above 85,000 MPa%, preferably above 100,000 MPa%.
  • the bake-hardening effect can also be used to increase the yield strength.
  • the bake hardening values were determined according to the European standard EN 10325.
  • the high levels of interstitially dissolved alloying elements ensure an increased bake-hardening potential and can further improve the mechanical properties of the final product.
  • the manganese content of an austenitic manganese steel tape according to the invention may preferably be in the range of 14% ⁇ Mn ⁇ 18.0%, in particular 14% ⁇ Mn ⁇ 16.5%.
  • the grain size can be influenced in a targeted manner by the ratio of N to Al.
  • AlN aluminum nitride
  • a high grain size can be made possible with an austenitic manganese steel strip.
  • the Al content can be kept very low in the alloying concept pursued here, as much carbon is available for the deoxidation of the liquid steel.
  • the manganese steel according to the invention can have the lowest possible aluminum content, which is limited only by unavoidable impurities in the production process (ie no aluminum addition). In the case of the steel strip according to the invention, this results in maximum grain size growth during recrystallization (ie during hot rolling or during annealing).
  • appropriately high phosphorus contents of 0.03% ⁇ P, in particular 0.05% ⁇ P, 0.06% ⁇ P, 0.07% ⁇ P, 0.08% ⁇ P and also 0.10% ⁇ P are used. It may even be provided a phosphorus content 0.20% ⁇ P.
  • a high phosphorus content can increase the tensile strength and especially the yield strength at higher particle sizes. Surprisingly, no significant reduction in elongation at break and no significant deterioration in weldability were observed with an increase in phosphorus content.
  • the tensile strength and the yield strength as well as the elongation at break of the produced steel strip can be changed in a targeted manner.
  • the larger the grain the lower the tensile strength and the yield strength and the higher the elongation at break.
  • Medium particle sizes of more than 5 ⁇ m or more than 10 ⁇ m can be set.
  • the manganese steel according to the invention preferably has a very low silicon content (Si ⁇ 1.0%, in particular Si ⁇ 0.2%, particularly preferably Si ⁇ 0.05%), which is optionally limited only by unavoidable impurities in the production process (ie in this case no addition of silicon, the Si content may then be below Si ⁇ 0.03%).
  • silicon has an influence on deformation mechanisms. Silicon impairs twinning, ie a low silicon concentration facilitates the formation of twins and possibly the formation of small micro-twins or nano-twins.
  • the silicon content of the manganese steel of the present invention can be set low, preferably as low as possible.
  • the silicon content can be kept very low, as much carbon is available for the deoxidation of the liquid steel, and because the strength of the steel (silicon causes an increase in strength) by other measures such as high concentrations of C and / or P. is guaranteed.
  • Niobium (Nb), vanadium (V) and titanium (Ti) are elements that form precipitates (carbides, nitrides, carbonitrides) and may optionally be added to improve strength through precipitation hardening.
  • these elements have a grain-fine effect, which is why their concentration should be kept low, if a high grain size is to be ensured.
  • Nickel can stabilize the austenite phase (so-called ⁇ -stabilizer). Nickel may optionally be added in larger amounts (e.g., over 1% to 5% or even 10%).
  • the solid solution strengthener chromium (Cr) stabilizes the ⁇ -ferrites. Additions of chromium up to 10% by weight prefer the formation of ⁇ -martensite and / or ⁇ '-martensite, resulting in higher tensile strength and lower ductility.
  • the proportion of chromium should therefore be limited. For example, Cr ⁇ 5%, in particular Cr ⁇ 0.2%, can preferably be set.
  • Molybdenum (Mo) and tungsten (W) also show a grain-refining angle. Tungsten has a high affinity for carbon and forms the hard and very stable carbides W 2 C and WC steel. The proportion of tungsten should be limited.
  • W ⁇ 1% in particular W ⁇ 0.02%
  • Tungsten is an even better solid solubility enhancer than chromium and also forms carbides (but to a lesser extent than chromium).
  • Mo ⁇ 1%, in particular, Mo ⁇ 0.02% is set.
  • the grain size of a hot-rolled steel strip is also greatly influenced by the final rolling temperature during hot rolling.
  • the steel strip according to the invention can be rolled with a final rolling temperature of between 750 ° C and 1050 ° C, preferably between 800 ° C and 900 ° C. For a given chemical composition can be adjusted by the choice of the final rolling temperature, the average grain size.
  • the tensile strength of the hot-rolled steel may preferably be above 1050 MPa.
  • Cold rolling can increase the mechanical properties of the hot rolled austenitic manganese steel strip.
  • the grain size of a cold-rolled steel strip is strongly influenced by the annealing temperature.
  • the annealing performed after the cold rolling may be carried out at an annealing temperature between 750 ° C and 1050 ° C, and in particular, the annealing temperature may be greater than 900 ° C.
  • Tensile strengths of more than 1100 MPa, in particular more than 1200 MPa can be achieved with an elongation at break of more than 75%, in particular over 80%.
  • a manganese steel sheet according to the invention with the said chemical compositions has a reshaped, in particular stretched or deep-drawn sheet steel section whose microstructure micro-twins having an average thickness of less than 30 nm, in particular less than 20 nm and nano-twins having an average thickness of less than 10 nm.
  • these micro- and nano-twins form during the forming process, whereby the high mechanical properties of the starting material are presumably due - at least in part - to this deformation mechanism.
  • the semi-finished product is heated to a temperature above 1100 ° C after casting a semi-finished steel.
  • the heated semi-finished product is rolled at a final rolling temperature between 750 ° C and 1050 ° C, preferably between 800 ° C and 900 ° C.
  • the rolled steel strip is cooled at a rate of 20 ° C./s or higher.
  • rapid cooling of the hot rolled steel strip is performed at a rate of 50 ° C / s or higher, more preferably 200 ° C / s or higher. Rapid cooling helps to provide high solids solubility of C, N and P elements in the granules.
  • the rapid cooling leads to a "freezing" of the dissolved elements without or with only little excretion formation.
  • the excretion formation can be largely prevented by a rapid cooling.
  • the occurrence of grain boundary carbides as well as embrittlement (grain boundary segregation) of the steel structure caused by high phosphorus contents can be prevented by a rapid cooling.
  • the higher the cooling rate the better and more uniformly can carbon and phosphorus be kept in solution. Cooling rates of over 100 ° C / s to 400 ° C / s were used. Cooling rates of more than 400 ° C / s to even more than 600 ° C / s are also possible. If necessary, before the rapid cooling an intermediate phase of several seconds, in particular 1 to 4 seconds, persist, in which the steel strip slowly cools in air to improve the recrystallization of the phosphorus-alloyed steel strip.
  • the hot rolled steel strip is cold rolled and then annealed for recrystallization.
  • the annealing temperature may be between 750 ° C and 1150 ° C and in particular greater than 900 ° C.
  • the grain size can be changed again, after annealing, a grain size of about 15 ⁇ m, especially about 20 microns may be provided to achieve a high elongation at break and possibly an improvement in the solid solubility of carbon, phosphorus and optionally nitrogen , A high tensile strength can be ensured in particular by a relatively high proportion of phosphorus (and carbon).
  • the rolled steel strip is cooled at a rate of 20 ° C / s or higher.
  • rapid cooling of the cold-rolled steel strip is conducted at a rate of 50 ° C / sec or higher, more preferably 200 ° C / sec or higher.
  • a rapid cooling also contributes to effecting a high and uniform solid solubility of carbon, phosphorus and nitrogen in the grains and thereby to achieve a high tensile strength even with large grains. Cooling rates of over 100 ° C / s to 400 ° C / s were used. Cooling rates of more than 400 ° C / s to even more than 600 ° C / s are also possible. If necessary, before the rapid cooling an intermediate phase of several seconds, in particular 1 to 6 seconds, persist, in which the steel strip slowly cools in air to improve the recrystallization of the phosphorus-alloyed steel strip.
  • pig iron is produced in the blast furnace or with a smelting reduction process such as Corex or Finex.
  • the Tecnored process is also possible.
  • the pig iron is then converted into steel, for example, in an oxygen inflation process (eg in an LD (Linz-Donawitz) / BOF (Bottom Oxygen Furnace) process).
  • a vacuum degassing eg according to the Ruhrstahl-Heraeus process (RH)
  • RSH Ruhrstahl-Heraeus process
  • a second production route which may be particularly suitable for manganese steels, uses an electric arc furnace (EAF) for steelmaking and an AOD converter for decarburizing the liquid steel. Again, prior to casting the steel, a ladle furnace can be used to heat and alloy the molten metal.
  • EAF electric arc furnace
  • AOD converter AOD converter
  • the steel thus produced can be further processed by means of various casting techniques such as block casting, casting rolls, thin strip casting or continuous casting.
  • the steel body produced during casting is called semifinished and may e.g. be realized in the form of slabs, billets or blocks.
  • the slab is further processed in hot strip mills to hot strip.
  • rolling mills for narrow strip width less than 100 mm
  • middle strip width between 100 mm and 600 mm
  • broadband width greater 600 mm
  • blocks and billets to profiles, pipes or wires is possible.
  • a rolling temperature between about 1100 ° C and 1300 ° C, optionally also higher, can be used.
  • the rolling end temperature may for example be between 750 ° C and 1050 ° C and in particular between 800 ° C and 900 ° C.
  • Different rolling end temperatures result in different average particle sizes of the hot-rolled steel strip according to the dynamic recrystallization at the prevailing temperature. The lower the final rolling temperature, the smaller the average particle size obtained for a given chemical composition. With a reduction of the mean grain size, the tensile strength decreases and the breaking strength of the hot-rolled steel strip, the elongation at break decreases.
  • roller end temperature is too low, however, there is the risk that the high grain refining in manganese steels causes a loss of plastic deformability as a result of the increased strength. Furthermore, due to the phase stability, low cementation temperatures increasingly lead to the formation of cementite ((Fe, Mn) 3 C), which may affect the mechanical properties. The cementite precipitates reached a particle size at rolling end temperatures below 740 ° C., which significantly impaired the mechanical properties.
  • the mean grain size of the hot strip steel strip is further influenced by the content of aluminum and nitrogen. It is known that manganese increases the solubility of nitrogen in liquid iron. Nitrogen dissolved in liquid iron forms aluminum nitride precipitates with aluminum, which hinder the migration of grain boundaries and thus grain growth. Aluminum nitride may further cause hot working cracking. It has been found that by targeted control of the aluminum and nitrogen content in steel low Endwalztemperaturen well below 950 ° C and especially below 900 ° C down to 750 ° C are possible without causing cracking occurs. However, the formation of large cementite particles, which begins with a lowering of the final rolling temperature below about 740 ° C to 800 ° C, to avoid. Particularly preferred final rolling temperatures in the hot rolling process can therefore be in the range of 800 ° C to 900 ° C.
  • the avoidance of cracking has been achieved at said final rolling temperatures in the range of 800 ° C to 900 ° C with chemical compositions in which an extremely small amount of aluminum up to 0.008% or 0.010% in combination with a low content of nitrogen to eg 0.030% or 0.036% were used.
  • the respective concentrations of the elements are interdependent. If less nitrogen is used, more aluminum is allowed and vice versa. In this respect, higher nitrogen contents than stated above are possible with a low aluminum content.
  • rapid cooling of the hot strip is performed at as high a cooling rate as possible (e.g., above 50 ° C / s or higher).
  • the cooling can be done by applying the hot strip with water.
  • the hot strip is then removed in a continuous pickling plant e.g. cleaned with sulfuric acid (descaled).
  • the hot strip may have a thickness of 1.5 to 2.0 mm, for example.
  • An annealing step is usually not carried out in the hot strip products produced here. In a particular embodiment, however, such an annealing step is carried out and causes a grain coarsening as well as an increase in the elongation at break.
  • the hot strip produced in the manner described above can be further processed by cold rolling and annealing to the cold strip product.
  • cold rolling the hot strip is further reduced in thickness and the mechanical and technological properties of the band are set.
  • low strip thicknesses in the range of about 0.7 mm to 1.75 mm of the cold strip can be produced.
  • Cold-strip products with such small thicknesses are of particular interest in the automotive sector for crash-absorbing components.
  • the cold rolling is preferably carried out using high rolling forces.
  • Roll stands with 2 to 20 rolls can be used.
  • a Sendzimir rolling mill with 12 rolls consists for example of a symmetrical arrangement of each of 3 back rolls, 2 intermediate rolls and 1 roller defining the nip pressure roller.
  • a Sendzimir rolling mill with 20 rolls for example, consists of a symmetrical arrangement of 4 back rolls, 3 outer intermediate rolls, 2 inner intermediate rolls and 1 roller defining the nip pressure roller. It showed a surprisingly good rolling and low cracking compared to other manganese steels.
  • the percent reduction in thickness (cold rolling degree) achieved during cold rolling may be above 40%, e.g. between 40% and 60%.
  • Cold rolling was also carried out with cold rolling degrees above 60%, especially above 80%. It was cold rolled with and without train.
  • the steel strip is annealed for recrystallization.
  • the annealing may e.g. be carried out after the continuous annealing or annealing process.
  • the solidification of the microstructure occurring during cold rolling is reduced again. It comes here about nucleation and grain growth to a rebuilding of the structure.
  • the annealing can be carried out at temperatures between 750 ° C and 1250 ° C, in particular 750 ° C to 1150 ° C and about 5 seconds to 5 minutes, in particular 2 to 5 minutes to annealing temperature persist.
  • the annealing time is sufficient to heat the band substantially full volume to the respective annealing temperature.
  • the hot steel strip is rapidly cooled, preferably quenched by exposure to water or in the gas stream (Gasjet). It has been found that a particularly rapid cooling is helpful to a high solids solubility of the elements C, N and P in the grains too cause. In particular, the embrittlement (grain boundary segregation) critical with a high phosphorus content could be largely or completely prevented by increasing the cooling rate. Cooling rates of over about 50 ° C or over 100 ° C per second are advantageous. Furthermore, cooling rates of more than 200 ° C., 300 ° C. or 400 ° C. per second may preferably also be provided, whereby experiments with cooling rates above 500 ° C. and above 600 ° C. per second have also been successfully carried out.
  • cold-rolling After cold-rolling, annealing and cooling, cold-rolling can be carried out to set a suitable flatness of the cold-rolled strip.
  • thickness reductions e.g. 0.5%, 1.5%, 5%, 25% and more than 40%, or appropriate intermediate values.
  • galvanizing for example hot-dip galvanizing or electrolytic galvanizing
  • the chemical composition of the steel may vary over a wide range in other alloying elements. As upper limit values are provided: 0.5% ⁇ V, 0.5% ⁇ Nb, 0.5% ⁇ Ti, 10% ⁇ Cr, 10% ⁇ Ni, 1% ⁇ W, 1% ⁇ Mo, 3% ⁇ Cu, 0.02% ⁇ B, the rest as mentioned iron and production-related impurities.
  • Table 1 shows the chemical composition of four steel strips X80Mn16-0.01P, X80Mn16-0.03P, X80Mn16-0.08P and X80Mn16-0.1.0P with a phosphorus concentration between 0.011 and 0.102% by weight.
  • the hot strip process was carried out in each case as described above.
  • the used final rolling temperatures (between 750 ° C and 1030 ° C) as well as the obtained mechanical properties of the produced hot rolled products X80Mn16-0.01P, X80Mn16-0.03P, X80Mn16-0.08P and X80Mn16-0.10P are given in Table 2.
  • the mechanical values obtained in the tensile tests were determined according to European standard "EUROPEAN STANDARD EN 10002-1, July 2001", which is hereby incorporated by reference into the disclosure of this document. All values given in Table 2 are also disclosed as lower limits on the size to which they relate.
  • the hot strip (WB) can optionally be further processed into a cold strip (KB).
  • the cold strip processing was carried out with the processing parameters given in Table 3.
  • Table 3 The mechanical properties of the cold-rolled products of the chemical compositions X80Mn16-0.01P, X80Mn16-0.03P, X80Mn16-0.08P and X80Mn16-0.10P prepared in this way are given in Table 3. All values given in Table 3 are also disclosed as lower limits on the size to which they relate.
  • the cold-rolled products with the KB numbers 1 to 3 are therefore based on approximately the hot-rolled product with the WB number 2 (the final rolling temperatures differ only by 10 ° C) and the cold-rolled products with the KB numbers 4 to 6 is approximately based on the hot-rolled product with the WB number 5 (the final rolling temperatures differ only by 30 ° C).
  • Table 3 shows that tensile strengths Rm over 1100 MPa and even above 1200 MPa are attained, and that even with large average particle sizes (15 ⁇ m in the case of X80Mn16-0.03P (KB no. 6) and X80Mn16-0.10P (KB No. 10) as well as over 20 ⁇ m or possibly even 25 ⁇ m in the case of the other samples), tensile strengths Rm above 1000 MPa can still be achieved.
  • the tensile strength Rm is defined as the stress occurring at maximum tensile force on the workpiece.
  • the elongation at break A 50 given in Table 3 is the percentage permanent change in length after breakage of the tensile test specimen (according to EN 10002-1), based on the initial measuring length, based on an initial measuring length of 50 mm.
  • EN 10002-1 the percentage permanent change in length after breakage of the tensile test specimen
  • Another important parameter for the mechanical properties of steel strips is the product of tensile strength and elongation at break. Especially with large average particle sizes, high product values are achieved. The reason for this is that large grains lead to higher elongation at break values and the tensile strength, which usually decreases markedly with increasing grain size, is maintained as far as possible according to the invention by the relatively high carbon and / or phosphorus content.
  • Table 4 gives the results of a study of the weldability of the steels of the chemical compositions X80Mn16-0.01P, X80Mn16-0.03P, X80Mn16-0.08P and X80Mn16-0.10P: Table 4 - Investigation of weldability - composition Imine (n / a) Imax (n / a) deltaI (n / a) X80Mn16-0.01P 5.2 6.3 1.1 X80Ma16-0.03P 4.7 5.8 1.1 X80Mn16-0.08P 5.2 6.4 1.2 X80Mn16-0.08P 5.3 6.6 1.3 X80Mn16-0.10P 5.2 6.4 1.2 X80Mn16-0.10P 5.1 6.6 1.5
  • Fig. 1 the mean grain size of the aluminum nitride-poor cold-rolled steel strips specified in Table 3 with the chemical compositions X80Mn16-0.01P, X80Mn16-0.03P, X80Mn16-0.08P and X80Mn16-0.10P is shown as a function of the annealing temperature during the cold strip process.
  • the cold-rolled strip products shown here were based on a final rolling temperature of 900 ° C in the hot strip process.
  • the graph it can be seen that the steel bands and X80Mn16-0.01P X80Mn16-0.03P at annealing temperatures of about 920 ° C achieve average grain sizes more than 15 ⁇ m.
  • the phosphorus-rich steel strips of the chemical compositions X80Mn16-0.08P and X80Mn16-0.10P achieved even larger average particle sizes at comparable annealing temperatures.
  • the mean particle sizes were determined by light microscopic investigations on micrographs.
  • Fig. 2 shows a graph in which the work hardening n (here the n 10/20 value) of the steel strips mentioned above, which is also referred to as solidification exponent , compared with the vertical anisotropy (r 0/15 -, r 45/15 -, and r 90/15 value) is shown.
  • the n value was determined in accordance with standard ISO 10275, issue 2006-07, which is hereby incorporated by reference into the disclosure of this document.
  • the vertical anisotropy is in accordance with standard ISO 10113, edition 2006-09 which is hereby incorporated by reference into the disclosure of this document. Since the mechanical properties of a larger dispersion than those in Fig. 1 having shown average grain size, several samples of said steel strips were examined.
  • n 10/20 values above 0.5 can be achieved at a r 0/15 , r 45/15 and r 90/15 value in the range from 0.6 to 1.5 .
  • the phosphorus-rich steel strips of the chemical compositions X80Mn16-0.08P and X80Mn16-0.10P achieve slightly higher n-values than the steel strips of the chemical compositions X80Mn16-0.01P and X80Mn16-0.03P.
  • the steel strips according to the invention have a good cold workability, which is particularly important for further processing in drawing and deep drawing processes.
  • FIGS. 3A-C show schematic representations of microstructures observed in electron beam microscopic studies on reshaped samples of the steels of the invention.
  • Fig. 3A shows one direction activated System with conventional twinning, where lines 1 represent the mirror lines of the twins.
  • Fig. 3B shows a unidirectional system with micro- or nano-twins 2.
  • the micro- or nano-twins 2 are lath-shaped and often arranged side by side in larger numbers.
  • the lath thickness is referred to as the thickness d of the micro- or nano-twins 2 and is typically much smaller than the thickness of common twins.
  • Fig. 3C shows a bi-directionally activated micro- or nano-twin system 2. It can be seen that bi-directional micro- or nano-twins 2 occur.
  • Fig. 4 shows an electron micrograph of a steel structure according to the invention after a deformation or tensile stress. A large number of pale-shaped micro- and nano-twins are recognizable in the bright field.
  • Fig. 5 shows a microsection of the weld nugget of a steel structure according to the invention after a weld.
  • X80Mn16-0.10P samples were used. It can be seen that the basic hardness as well as the maximum hardness in the heat-affected zones and the hardness in the weld nugget agree well and have only slight deviations. These deviations are in the range of the measuring tolerance. It is further recognized that there are no cracks or martensite in the structure.
  • the n-value is largely determined by the chemical composition. That is, the strength of the final product that can be achieved by deformation depends on how easily dislocations can travel in the crystal. In the fcc crystal lattice, the solid solubility of C and N is greater than in the bcc crystal lattice.
  • the increase in tensile strength caused by solid solution of C and P is utilized, whereby in recent investigations tensile strength values of 1100 MPa could be measured with an extremely high breaking elongation of 95%.
  • the hardening achieved by solid solution of said elements makes it possible to increase the n-value considerably. As a result, the highest reported product values of tensile strength and elongation at break are achieved. This is particularly due to the use of high phosphorus concentrations and the associated increase in strength - especially at relatively large mean particle sizes - attributed.
  • the hot strip or cold strip is cut in further processing into steel sheets, e.g. be used in automotive technology for the production of body parts.
  • steel according to the invention can also be used in rails, switches, in particular switch hearts, rod material, pipes, hollow profiles or high-strength wires.
  • the steel sheets are brought by forming processes such as deep drawing in the desired shape and then further processed into the final products (eg body part).
  • the forming process at least portions of the steel sheets are subjected to a mechanical stress (usually tensile stress), so that in these areas, the deformation mechanisms described above are effective.
  • a mechanical stress usually tensile stress

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Claims (15)

  1. Bande d'acier austénitique au manganèse laminée à chaud, présentant une composition chimique, en données pondérales, de 0 , 4 % ≤ C ≤ 1 , 2 %
    Figure imgb0033
     12 , 0 % ≤ Mn ≤ 25 , 0 %
    Figure imgb0034
     P ≥ 0 , 03 %
    Figure imgb0035
     Si ≤ 2 %
    Figure imgb0036
     Al ≤ 0,05%, V ≤ 0,5%, Nb ≤ 0,5%, Ti ≤ 0,5%, Cr ≤ 10%, Ni ≤ 10%, W ≤ 1%, Mo ≤ 1%, Cu ≤ 3%, B ≤ 0,02%, N ≤ 0,04%, le reste étant du fer et des impuretés liées à la production, et présentant une grosseur moyenne de grain supérieure à 13 µm, un produit de l'allongement à la rupture en % et de la résistance à la traction en MPa supérieur à 65.000, en particulier supérieur à 70.000 MPa% étant obtenu.
  2. Bande d'acier austénitique au manganèse laminée à chaud selon la revendication 1, présentant comme propriété qu'un échantillon de la bande d'acier au manganèse, après avoir été soumis à un procédé de formage, présente, dans sa structure, des micromacles présentant une épaisseur moyenne inférieure à 30 nm, en particulier inférieure à 20 nm, en particulier inférieure à 10 nm.
  3. Bande d'acier austénitique au manganèse, laminée à chaud selon l'une quelconque des revendications précédentes, présentant une teneur en P ≥ 0,05%, en particulier P ≥ 0,06%, en particulier P ≥ 0,08%, plus particulièrement P ≥ 0,10%.
  4. Bande d'acier austénitique au manganèse, laminée à chaud selon l'une quelconque des revendications précédentes, présentant une teneur en Si ≤ 1,0%, en particulier Si ≤ 0,2%, plus particulièrement Si ≤ 0,05%.
  5. Bande d'acier austénitique au manganèse, laminée à chaud selon l'une quelconque des revendications précédentes, présentant une grosseur moyenne de grain supérieure à 18 µm, en particulier supérieure à 20 µm.
  6. Bande d'acier austénitique au manganèse laminée à froid, présentant une composition chimique, en données pondérales, de 0 , 4 % ≤ C ≤ 1 , 2 %
    Figure imgb0037
     12 , 0 % ≤ Mn ≤ 25 , 0 %
    Figure imgb0038
     P ≥ 0 , 03 %
    Figure imgb0039
     Si ≤ 2 %
    Figure imgb0040
     Al ≤ 0,05%, V ≤ 0,5%, Nb ≤ 0,5%, Ti ≤ 0,5%, Cr ≤ 10%, Ni ≤ 10%, W ≤ 1%, Mo ≤ 1%, Cu ≤ 3%, B ≤ 0,02%, N ≤ 0,04%, le reste étant du fer et des impuretés liées à la production, et présentant une grosseur moyenne de grain supérieure à 5 µm, un produit de l'allongement à la rupture en % et de la résistance à la traction en MPa supérieur à 75.000, en particulier supérieur à 80.000 MPa% étant obtenu.
  7. Bande d'acier austénitique au manganèse laminée à froid selon la revendication 6, présentant comme propriété qu'un échantillon de la bande d'acier au manganèse, après avoir été soumis à un procédé de formage, présente, dans sa structure, des micromacles présentant une épaisseur moyenne inférieure à 30 nm, en particulier inférieure à 20 nm, en particulier inférieure à 10 nm.
  8. Bande d'acier austénitique au manganèse, laminée à froid selon l'une quelconque des revendications 6 ou 7, présentant une teneur en P ≥ 0,06%, en particulier P ≥ 0,06%, en particulier P ≥ 0,08%, plus particulièrement P ≥ 0,10%.
  9. Bande d'acier austénitique au manganèse, laminée à froid selon l'une quelconque des revendications 6 à 8, présentant une teneur en Si ≤ 1,0%, en particulier Si ≤ 0,2%, plus particulièrement Si ≤ 0,05%.
  10. Bande d'acier austénitique au manganèse, laminée à froid selon l'une quelconque des revendications 6 à 9, présentant une grosseur moyenne de grain supérieure à 15 µm, en particulier supérieure à 20 µm.
  11. Bande d'acier au manganèse, présentant une composition chimique, en données pondérales, de 0 , 4 % ≤ C ≤ 1 , 2 %
    Figure imgb0041
     12 , 0 % ≤ Mn ≤ 25 , 0 %
    Figure imgb0042
     P ≥ 0 , 03 %
    Figure imgb0043
     Si ≤ 2 %
    Figure imgb0044
     Al ≤ 0,05%, V ≤ 0,5%, Nb ≤ 0,5%, Ti ≤ 0,5%, Cr ≤ 10%, Ni ≤ 10%, W ≤ 1%, Mo ≤ 1%, Cu ≤ 3%, B ≤ 0,02%, N ≤ 0,04%, le reste étant du fer et des impuretés provoquées par la production et présentant une section en tôle d'acier étirée sur forme ou emboutie, dont la structure présente des micromacles présentant une épaisseur inférieure à 30 nm, en particulier inférieure à 20 nm.
  12. Procédé pour la production d'une bande d'acier austénitique au manganèse laminée à chaud, présentant une composition chimique, en données pondérales, de 0 , 4 % ≤ C ≤ 1 , 2 %
    Figure imgb0045
     12 , 0 % ≤ Mn ≤ 25 , 0 %
    Figure imgb0046
     P ≥ 0 , 03 %
    Figure imgb0047
     Si ≤ 2 %
    Figure imgb0048
     Al ≤ 0 , 05 % , V ≤ 0 , 5 % , Nb ≤ 0 , 5 % , Ti ≤ 0 , 5 % , Cr ≤ 10 % , Ni ≤ 10 % , W ≤ 1 % , Mo ≤ 1 % , Cu ≤ 3 % , B ≤ 0 , 02 % , N ≤ 0 , 04 % ,
    Figure imgb0049
     le reste étant du fer et des impuretés provoquées par la production, présentant les étampes :
    coulée d'un produit semi-fini en acier ;
    chauffage du produit semi-fini à une température supérieure à 1100°C ;
    laminage du produit semi-fini à une température de fin de laminage entre 750°C et 1050°C, la grosseur moyenne de grain après le laminage à chaud étant supérieure à 13 µm ;
    et refroidissement de la bande d'acier laminée à une vitesse de 20°C/s ou plus.
  13. Procédé selon la revendication 12, la grosseur moyenne de grain après le laminage à chaud étant supérieure à 20 µm.
  14. Procédé pour la production d'une bande d'acier austénitique au manganèse laminée à froid, présentant les étapes :
    mise à disposition d'une bande d'acier laminée à chaud produite selon un procédé des revendications 12 ou 13 ;
    laminage à froid de la bande d'acier ; et
    recuit de la bande d'acier laminée à froid pour sa recristallisation.
  15. Procédé selon la revendication 14, la température de recuit étant située entre 750°C et 1150°C et en particulier supérieure à 900°C.
EP09760726.1A 2008-11-12 2009-11-12 Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication Not-in-force EP2366035B1 (fr)

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