Method for Producing Thermo-Mechanically Produced Hot-Rolled Strip Products

Abstract

The invention relates to a method for producing thermomechanically produced hot strip products in which a steel alloy is melted; the steel alloy is adjusted so that a recrystallization during the hot rolling is suppressed; the final rolling temperature is greater than 800° C.; the melted steel alloy is cast into slab ingots and after being heated to a temperature above Ac.sub.3, the slab ingots are hot rolled until they reach a desired degree of deformation and a desired strip thickness; after the rolling, the strip is cooled to room temperature and for hardening purposes, is briefly heated to a temperature >Ac3 and cooled again, characterized in that the heating takes place with a temperature increase of more than 5 K/s, more than 10 K/s, more than 50 K/s, or more than 100 K/s, and is kept at a desired target temperature for a period of 0.5 to 60 s before cooling to yield improved mechanical properties.

Claims

1. A method for producing thermomechanically produced hot strip products, comprising the steps of: providing a steel alloy including the following elements, in percent by weight: 0.03 to 0.22% carbon, 0.0 to 2.0% silicon, 0.5 to 3.0% manganese, 0.02 to 1.2% aluminum, 0 to 2.0% chromium, 0 to 2.0% nickel, 0.0 to 1.0% molybdenum, 0.0 to 1.5% copper, 0 to 0.02% phosphorus, 0 to 0.01% sulfur, 0 to 0.008% nitrogen, 0 to 0.005% boron, 0.0 to 0.2% niobium, 0.0 to 0.3% titanium, 0.0 to 0.5% vanadium the remainder being comprised of iron and smelting-related impurities; melting the steel alloy; adjusting the steel alloy so that a recrystallization during hot rolling is suppressed; casting the melted steel alloy into slab ingots; heating the slab ingots to a temperature above Ac3, hot rolling the slab ingots using a final rolling temperature greater that 800° C. until they reach a desired degree of deformation and a desired strip thickness to form steel strips; cooling the steel strips to room temperature; and hardening the steel strips by heating the steel strips to a temperature >Ac3 and cooling them again to form hardened steel strips; wherein the heating of the steel strips is performed using a temperature increase of more than 5° K/s, and the heated steel strips are kept at a desired target temperature for a holding period of about 0.5 to about 60 seconds prior to cooling them again.

2. The method according to claim 1, wherein the steel alloy comprises the following elements in percent by weight: 0.055 to 0.195 carbon, 0.0 to 0.3% silicon, 1.4 to 2.3% manganese, 0.02 to 0.6% aluminum, 0 to 2% chromium, 0 to 2% nickel, 0.0 to 0.42% molybdenum, 0.0 to 0.5% copper, 0 to 0.008% phosphorus, 0 to 0.0015% sulfur, 0 to 0.007% nitrogen 0 to 0.005% boron, 0.0 to 0.2% niobium, 0.0 to 0.3% titanium, 0.0 to 0.5% vanadium the remainder being comprised of iron and smelting-related impurities

3. The method according to claim 1, wherein the heating of the steel strips comprises inductive heating.

4. The method according to claim 1, wherein the heating of the steel strips to a temperature >Ac3 comprises heating the steel strips to between about 800° C. and about 1000° C.

5. The method according to claim 1, further comprising the step of annealing the hardened steel strips at a temperature of about 300° C. to about 700° C.

6. The method according to claim 1, wherein the holding period is about 0.5 to about 10 seconds.

7. The method according to claim 1, wherein the step of cooling the steel strips after the heating step takes place at a cooling rate of >10° K/s.

8. The method according to claim 7 wherein the cooling rate is >30K/s.

9. The method according to claim 1, wherein the heating of the steel strips during hardening is performed using rolling heat.

10. The method according to claim 1, wherein the hardening of the steel strips is performed inline and continuously.

11. The method according to claim 1, further comprising the steps of welding the hardened steel strips by forming a weld seam, and heat treating the welded steel strips to homogenize the weld seam.

12. The method according to claim 1, wherein the hardened steel strips have a sheet thickness of about 1.5 mm to about 20 mm.

13. The method according to claim 1, wherein the step of hardening the steel strips is performed using a Hollomon-Jaffee parameter of about 18000 to about 23000.

14. A hot strip produced with a method according to claim 1, wherein the hot strip comprises at least one of the following mechanical properties: tensile strength (Rm)>=1000 MPa notched bar impact bending work (KV)>=50 J, measured at −40° C. and the following condition is satisfied
Rm×KV>=75000 MPa-J

15. A use of a hot strip according to claim 14 for producing at least one of support structures in steel construction, machinery construction, automobile manufacture, and crane construction; security plates; and wear protection applications.

16. A thermomechanically-produced hot strip product, comprising a steel alloy including the following elements in percent by weight: 0.03 to 0.22% carbon, 0.0 to 2.0% silicon, 0.5 to 3.0% manganese, 0.02 to 1.2% aluminum, 0 to 2.0% chromium, 0 to 2.0% nickel, 0.0 to 1.0% molybdenum, 0.0 to 1.5% copper, 0 to 0.04% total of phosphorus, sulfur, nitrogen and boron, 0.0 to 1.0% total of niobium, titanium and vanadium, the remainder being comprised of iron and smelting-related impurities; wherein the hot strip product has a tensile strength Rm in excess of 1000 MPa, a notched bar impact bending work (KV) in excess of 50 J at −40° C., and a Rm×KV in excess of 75000 MPa-J.

17. The hot strip product of claim 16, wherein the notched bar impact bending work (KV) is at least about 165,000 MPa-J.

18. The hot strip product of claim 16, comprising the following elements in percent by weight: 0.055 to 0.195 carbon, 0.0 to 0.3% silicon, 1.4 to 2.3% manganese, 0.02 to 0.6% aluminum, 0 to 2% chromium, 0 to 2% nickel, 0.0 to 0.42% molybdenum, 0.0 to 0.5% copper, 0 to 0.008% phosphorus, 0 to 0.0015% sulfur, 0 to 0.007% nitrogen 0 to 0.005% boron, 0.0 to 0.2% niobium, 0.0 to 0.3% titanium, 0.0 to 0.5% vanadium the remainder being comprised of iron and smelting-related impurities.

19. A thermo-mechanically-produced hot-rolled steel strip, comprising a steel alloy including the following elements in percent by weight: 0.03 to 0.22% carbon, 0.0 to 2.0% silicon, 0.5 to 3.0% manganese, 0.02 to 1.2% aluminum, 0 to 2.0% chromium, 0 to 2.0% nickel, 0.0 to 1.0% molybdenum, 0.0 to 1.5% copper, 0 to 0.04% total of phosphorus, sulfur, nitrogen and boron, 0.0 to 1.0% total of niobium, titanium and vanadium, the remainder being comprised of iron and smelting-related impurities; wherein the hot strip product has a tensile strength Rm in excess of 1000 MPa, a notched bar impact bending work (KV) in excess of 50 J at −40° C., and a Rm×KV in excess of 75000 MPa-J.

20. The steel strip of claim 19, wherein the notched bar impact bending work (KV) is at least about 165,000 MPa-J.

21. The steel strip of claim 19, comprising the following elements in percent by weight: 0.055 to 0.195 carbon, 0.0 to 0.3% silicon, 1.4 to 2.3% manganese, 0.02 to 0.6% aluminum, 0 to 2% chromium, 0 to 2% nickel, 0.0 to 0.42% molybdenum, 0.0 to 0.5% copper, 0 to 0.008% phosphorus, 0 to 0.0015% sulfur, 0 to 0.007% nitrogen 0 to 0.005% boron, 0.0 to 0.2% niobium, 0.0 to 0.3% titanium, 0.0 to 0.5% vanadium the remainder being comprised of iron and smelting-related impurities.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0158] The invention will be explained by way of example based on the drawings. In the drawings:

[0159] FIG. 1 shows the influence of conventional hot rolling on the structure;

[0160] FIG. 2 shows the influence of the thermomechanical rolling on the structure;

[0161] FIG. 3 shows the difference in the microstructure between recrystallized austenite and non-recrystallized austenite;

[0162] FIG. 4 shows the steel phases based on the temperature curves produced;

[0163] FIG. 5 shows the comparison of heat treatment routes in a thermomechanically rolled and conventionally quenched and tempered product, in a thermomechanically rolled product, and in a thermomechanically rolled product according to the invention;

[0164] FIGS. 6a/6b show the temperature/time curves for the treatment routes in FIG. 5 that are not according to the invention and the structures that are finally established;

[0165] FIG. 7 shows a detail of the structure in a thermomechanically rolled and annealed steel after the short-term heat treatment according to the invention;

[0166] FIG. 8 shows the product of the tensile strength Rm and the notched bar impact work KV as a function of the Hollomon-Jaffee parameter of the hardening process for short-term hardening procedures according to the invention and for conventional hardening of the steel (material A in Table 1);

[0167] FIG. 9 shows the product of the tensile strength Rm and the notched bar impact work KV as a function of the Hollomon-Jaffee parameter of the hardening process for short-term hardening procedures according to the invention and for conventional hardening of the steel (material B in Table 2);

[0168] FIG. 10a shows the possible temperature/time curves in the method according to the invention with the structure that is established in the individual production steps;

[0169] FIG. 10b shows the possible temperature/time curves in the method according to the invention with the structure in welded connections that is established in the individual production steps.

DETAILED DESCRIPTION OF THE INVENTION

[0170] According to the invention, steel is thermomechanically rolled in order to increase the properties of toughness and isotropy as well as other properties.

[0171] According to FIG. 1, conventionally hot rolled steels, steels in which the rolled product is first heated to the hot-forming temperature and then rolled, by means of which the non-deformed grain is deflected in the rolling direction; already during the rolling, a recrystallization takes place after each roll pass, at the end of which the respective austenite grain has a globular form.

[0172] By contrast with this, thermomechanically rolled steels contain higher concentrations of carbide-forming elements, which form precipitation already during the hot rolling. The precipitation and the dissolved micro-alloying elements delay or suppress the recrystallization after the roll passes. Correspondingly, a recrystallization and a corresponding grain growth do not occur so that according to FIG. 2, a globular structure according to FIG. 1 is not formed and instead, the austenite is in an elongated form.

[0173] In FIG. 3 the different austenite embodiments are shown, on the one hand, the globular recrystallized austenite (top) and on the other, the elongated, non-recrystallized austenite (bottom).

[0174] The difference between the normalized rolled steels with the globular recrystallized austenite grain on the one hand and the thermomechanically rolled steels with the non-globular, elongated, and deformed austenite grain is that the austenite grain of the thermomechanically rolled steel exhibits a much finer structure after the transformation.

[0175] Correspondingly, the forming has significant effects on the structure and properties; the properties cannot be achieved by means of the heat treatment alone.

[0176] The thermomechanically rolled steels used are so-called micro-alloyed steels.

[0177] FIG. 4 schematically depicts how from the austenite range, by means of different cooling curves, it is also possible to achieve different structures or microstructures. It shows that by means of different cooling paths, martensitic steels, complex-phase steels, dual-phase steels, and ferritic-bainitic steels can be achieved.

[0178] Prior conventional heat treatment routes are shown in FIG. 5, lines 1 and 2. For example, the thermomechanical rolling and a conventional quenching and tempering step (a slab quenching and tempering), which is used for sheets, and the thermomechanical rolling, which can be combined with a direct hardening step (DQ) and an annealing step (A).

[0179] The method according to the invention (FIG. 5, last line) provides a thermomechanical rolling, an optional direct hardening (with an optional annealing step), and then at least one very short-term, for example inductive, hardening step or quenching and tempering step.

[0180] The temperature/time curves according to the prior art are shown in FIGS. 6a and 6b.

[0181] Before this short-term inductive hardening step or quenching and tempering step, the hot strip is allowed to cool or is cooled to room temperature (e.g. after the direct hardening). A further processing from the rolling heat does not take place.

[0182] The differences in the structures are clear when known structures shown in FIG. 6a and FIG. 6b are compared to the structure produced according to the invention shown in FIG. 10a. The structure of the thermomechanically rolled and short-term heat-treated steel according to the invention differs significantly from the conventionally treated steels; the smaller size and more isotropic form of the grain structure are particularly conspicuous.

[0183] Basically, the quenching and tempering step should be explained once again; the conventional quenching and tempering step is shown in FIG. 6a. In the conventional quenching and tempering, a product is first heated in a reheating furnace and is then thermomechanically rolled and completely cooled.

[0184] After the quenching and tempering, it is heated again to approx. 900° C. and then a rapid cooling in water is performed, followed by an annealing step at approx. 600° C. with a subsequent cooling in air.

[0185] The conventional heat treatments that are not according to the invention are thus the conventional hardening (H) or slab hardening, the conventional quenching and tempering (H+A) or slab quenching and tempering, and the conventional annealing (A) in the form of slab annealing or bell annealing.

[0186] In the conventional hardening or quenching and tempering, it is only possible to treat piece goods, which is relatively costly. In conventional thermomechanical rolling, the elongation of the structure produces an anisotropy of the properties; a slab annealing can achieve very good strength/toughness ratios, but it is only possible to heat treat slabs and not strips.

[0187] The solution according to the invention provides a thermomechanically produced hot strip (TM+DQ), which results in an elongated austenite grain and a homogeneous carbon distribution in the microstructure.

[0188] By contrast with conventional methods, however, the subsequent heat treatments (H.sub.ST, A.sub.ST) are performed as short-term heat treatments.

[0189] By contrast with the prior art, in the heating according to the invention, as shown in the figures described above, a rapid short-term heating is performed; for example, the heat source can be an inductive heating, but does not have to be.

[0190] According to the invention, hardening can be performed at least once and annealing can optionally be performed once. This yields a globular, fine austenite grain with a maximized strength and a maximized toughness.

[0191] According to the invention, the hardening can be performed once or twice; at 100 K/s to 1000° K/s, the heating rates can be very high; the maximum temperature is set to >Ac.sub.3.

[0192] According to the invention, this temperature is 800° C. to 1000° C., in particular between 820° C. and 970° C. The holding time is extremely short compared to the prior art and can be from 0.5 to 60 seconds, in particular from 0.5 to 5 seconds.

[0193] According to the invention, however, the heating rate can also be lower and can, for example, be 5 K/s, 10 K/s, or 15 K/s.

[0194] Preferably, but necessarily, the low holding times can be from 0.5 to 60 seconds, more preferably 0.5 to 20 seconds, in particular 0.5 to 5 seconds.

[0195] The subsequent cooling rates are set anywhere from >10° K/s up to greater than 60° K/s.

[0196] The optional annealing is performed at a maximum temperature below A.sub.c1, which is normally from 300° C. to 700° C. In order to avoid a softening zone in subsequent welding processes, an annealing temperature of between 500° C. and 700° C. can be advantageous, but in order to increase the yield strength, a lower annealing temperature of 300° C. to 450° C. can be particularly advantageous.

[0197] The short-term heat treatments according to the invention are thus one the one hand hardening treatments or quenching and tempering treatments.

[0198] FIG. 7 shows that a thermomechanically rolled, directly hardened and annealed steel has an elongated structure, whereas the steel produced according to the invention (TM+DQ+A+H.sub.ST/H.sub.ST+A.sub.ST) exhibits an isotropic globular structure.

[0199] This structure consists of 90% martensite (non-annealed or annealed), with the remainder being composed of austenite and bainite. The former austenite grain is globular, with the grain size being less than 20 μm and in particular less than 10 μm.

[0200] FIGS. 8 and 9 show examples of the properties that can be achieved as a function of the heat treatment routes and parameters for two respective alloy compositions A and B described in Tables 1 and 2 below. Table 1 shows selected properties of a steel (Material A) that has been heat treated according to the invention in contrast to conventionally heat treated steels. Table 2 shows selected propertied of a steel (Material B) that has been heat treated according to the invention in contrast to conventionally heat treated steels.

TABLE-US-00001 TABLE 1 Alloy Composition, Material A, Represented by FIG. 8 Material C Si Mn P S Al Cr Ni Mo Cu V Nb Ti B N Material 0.09 0.12 1.64 0.008 0.001 0.051 0.92 0.47 0.22 0.02 0.11 0.002 0.026 0.0023 0.0051 A R.sub.p.02 R.sub.m KV@ −40° C. Rm .Math. KV@ −40° C. Material Production process [MPa] [MPa] [J] [MPa .Math. J] Material Prior art TM + DQ + H 907 1,174 23  27,002 A H: 920° C., 10′, HJ = 23,380 TM + DQ + H + A 879 934 23  21,482 H: 920° C., 10′, A = 570° C., 35′ TM + DQ + A 983 1,013 53  53,689 Invention TM + DQ + (A) + H.sub.ST 1,031 1,235 209 258,115 H.sub.ST: 850° C., 3″, HJ = 19,458 TM + DQ + (A) + H.sub.ST + A.sub.ST 1,074 1,201 138 165,738 H.sub.ST: 850° C., 3″, A.sub.ST: 400° C., TM + DQ + (A) + H.sub.ST + A.sub.ST 918 1,038 154 159,852 H.sub.ST: 850° C., 3″, A.sub.ST: 550° C.,

TABLE-US-00002 TABLE 2 Alloy Composition, Material B, Represented by FIG. 9 Material C Si Mn P S Al Cr Ni Mo Cu V Nb Ti B N Material 0.18 0.29 1.44 0.008 0.001 0.052 0.73 1.02 0.39 0.46 0.04 0.038 0.020 0.0003 0.0051 B R.sub.p.02 R.sub.m KV@ −40° C. Rm .Math. KV@ −40° C. Material Production process [MPa] [MPa] [J] [MPa .Math. J] Material Prior art TM + DQ + H 1012 1371 55 75,405 B H: 920° C., 10′, HJ = 23,380 TM + DQ + H + A 1039 1064 44 46,816 H: 920° C., 10′, A = 570° C., 35′ TM + DQ + A 1169 1213 46 55,798 Invention TM + DQ + (A) + H.sub.ST 1269 1628 80 130,240  H.sub.ST: 850° C., 3″, HJ = 19,458 TM + DQ + (A) + H.sub.ST + A.sub.ST 1450 1480 50 74,000 H.sub.ST: 850° C., 3″, A.sub.ST: 400° C., 1″ TM + DQ + (A) + H.sub.ST + A.sub.ST 1280 1297 60 77,820 H.sub.ST: 850° C., 3″, A.sub.ST: 550° C., 1″

[0201] If a steel with the chemical composition shown in Table 1 is conventionally hardened, i.e. austenitized at 920° C. for 10 minutes, this yields an HJ parameter of 23380. The mechanical properties are an R.sub.p0.2 of 907 MPa, R.sub.m of 1174 MPa, and a notched bar impact work KV of 23 joule. The product of Rm and KV is 27,002 MPaJ. If the same steel grade is quenched and tempered (austenitized again at 920° C. for 10 minutes and additionally annealed at 570° C. for 35 minutes), then the R.sub.p0.2 is 879 MPa, the R.sub.m is 934 MPa, and the notched bar impact work is 23 joule. The product of Rm and KV is 21,482 MPaJ. In the thermomechanically rolled, directly hardened, and annealed production route, the mechanical characteristic values are 983 MPa for R.sub.p0.2, 1013 MPa for R.sub.m, and 53 joule for the notched bar impact bending work and the product Rm*KV=53,689 MPaJ.

[0202] By contrast, with the same material, but using the short-term heat treatment (HST) according to the invention with a holding step at 850° C. for 3 seconds and subsequent cooling to room temperature (HJ=19458), an R.sub.p0.2 value of 1031 MPa with a tensile strength of 1235 MPa and a notched bar impact bending work of 209 joule are achieved. These extremely good mechanical properties yield a product of Rm*KV of 258,115 MPaJ and represent an almost ten-fold increase over the value according to the prior art.

[0203] Even with an additional short-term annealing (AST) after the hardening treatment and cooling to room temperature, for example at 400° C. for only 1 second, an R.sub.p0.2 value of 1074 MPa is achieved with a simultaneously high tensile strength of 1201 MPa and a notched bar impact bending work of 138 joule (product 165,738 MPaJ). With an AST at 550° C. likewise maintained for one second, similar values are achieved; it being possible to slightly increase the notched bar impact bending work.

[0204] This means that it has been possible to achieve an extreme increase in the properties in all ranges.

[0205] In FIG. 9, the HJ parameter is plotted for different hardening temperatures and holding times. The light point corresponds to the above-described example A according to the invention with an HJ of 19,348 and the dark point corresponds to the comparison to the prior art. The HJ value should be above 18000 since otherwise, no hardening can be achieved, but must not be selected too high and in particular must be below 23000 since otherwise, the mechanical properties (especially the product of Rm and KV) can decrease drastically.

[0206] It is clear from Table 2 and from the comparison of the achievable values, though, that with a different alloy situation, the short-term heat treatment results in optimal combinations of properties.

[0207] In this case, different heat treatment temperatures were selected so that the quenching and tempering was performed once at 850° C. for 3 seconds and then at 550° C. for 1 second and after this, quenching and tempering was performed at 850° C. and at 400° C. for 1 second each. With the lower second short-term heat treatment, the notch impact strength does in fact decrease, but the values for R.sub.p0.2 and Rm increase. Here, too, there is a clear relationship between a low HJ value and the good mechanical properties; this is not as dramatically pronounced with material B as it is with material A.

[0208] FIG. 9 once again shows the HJ parameter for heat treatments according to the invention compared to the prior art. FIG. 10a shows the temperature/time curve according to a possible embodiment of the invention together with the structures that are established.

[0209] First of all, it is clear that with the thermomechanical rolling, an elongated austenite grain is achieved, which is transformed by the direct hardening into a martensitic grain; optionally, an annealing treatment is performed.

[0210] By means of the possible short-term heat treatments, this grain, which is elongated and enriched with dislocations because of the thermomechanical treatment and direct hardening, is transformed into a fine, globular grain.

[0211] With the thermomechanical rolling according to the invention, in which the subsequent heat treatments are performed as short-term heat treatments, it is advantageous that a structure with improved properties is achieved; the short-term heat treatments also permit these heat treatment methods to be performed inline.

[0212] By means of the processing step or production step of welding, the introduced energy (heat and/or pressure) causes a local change in the structure and the mechanical properties. Products therefore have nonhomogeneous properties in the region of the weld seam.

[0213] If after production, the short-term heat treatment according to the invention is used after a processing step of “welding,” then as shown in FIG. 10b for a fusion welding process, a homogenization of the microstructure occurs in the weld seam region. The microstructure of the weld seam region and also its mechanical properties are thus brought into line with those of the rest of the product.

[0214] This is true for both fusion-welded connections such as laser welds and for pressure-welded connections such as high-frequency welds.

[0215] The invention will be explained in greater detail based on an example:

[0216] The product according to the invention is produced in that first, a steel melt with the composition according to the invention, particularly the chemical composition indicated in Table 1 or Table 2, is melted in the steel mill and after the secondary metallurgical treatment, is cast into a slab ingot in a continuous casting machine.

[0217] The slab ingot is then heated to a temperature in the range from 1100° C. to 1300° C., in particular 1200° C. to 1260° C., descaled, and then thermomechanically hot rolled into a steel strip; in the hot rolling of the slab ingot, the initial rolling temperature is in the range from 1000° C. to 1250° C. and the final rolling temperature is greater than 800° C. and in particular, is between 830° C. and 930° C. In this case, a significant part of the forming takes place below the recrystallization stop temperature as a result of which, the austenite is elongated, as shown in FIG. 2. After the hot rolling, the steel strip is cooled from the final rolling temperature to the coiling temperature by means of water exposure and is coiled. In the present example, the coiling temperature is below the martensite start temperature, i.e. less than 500° C., in particular less than 250° C., and is achieved at a cooling rate of greater than 25° C./s, in particular between 40° C./s and 100° C./s.

[0218] The steel strip, with or without a preceding blank cutting (e.g. cross-cutting or longitudinal cutting), is optionally subjected to a heat treatment; the temperature assumes values below the A1 temperature, in particular below 700° C. Blanks made of the steel strip produced according to the invention can optionally be connected by means of a welding process. In this case, these blanks can have different dimensions or chemical compositions. According to the invention, the steel strip, the blank, or the welded blank is subjected to a short-term heat treatment. In this case, the product is first heated at least once to a maximum temperature above Ac3; typically, this is 800° C. to 1000° C., in particular however 820° C. to 970° C., briefly kept at this temperature, and then rapidly cooled. The heating rates, depending on the cross-section of the product to be heated, are greater than 5 K/s, preferably greater than 10 K/s, particularly preferably greater than 50 K/s, in particular greater than 100 K/s. The holding time at the maximum temperature is 0.5 to 60 seconds, for example 1-10 s; then, a cooling is performed at cooling rates between 10 K/s and up to greater than 60 K/s.

[0219] After the hardening, the material can be subjected to another annealing treatment. In the latter, the material is heated at a heating rate of up to 1000 K/s, in particular 400 to 800° C./s, to a maximum temperature below Ac1, which usually means 300° C. to 700° C., for example 550° C. The holding time at the maximum temperature is 0.5 to 60 seconds, for example 1 to 10 s; then, a cooling is performed at cooling rates between 10 K/s and up to greater than 60 K/s.

[0220] The invention will be explained in greater detail based on a specific example: The product according to the invention is produced in that first, a steel melt with the composition according to the invention, in particular the chemical composition indicated in Table 1, is melted in the steel mill and after secondary metallurgical treatment, is cast into a slab ingot in a continuous casting machine.

[0221] The slab ingot is then heated to a temperature of 1220° C., descaled, and then conventionally hot-rolled into a steel strip; in the hot rolling of the slab ingot, the initial rolling temperature is 1100° C. and the final rolling temperature is 870° C. In this case, a significant part of the forming takes place below the recrystallization stop temperature as a result of which, the austenite is elongated, as shown in FIG. 2. After the hot rolling, the steel strip is cooled from the final rolling temperature to the coiling temperature by means of water exposure and is coiled. In the present example, the coiling temperature is 120° C. and is achieved at a cooling rate of 50° C./s.

[0222] According to the invention, a cut blank of the steel strip with a thickness of 4 mm is subjected to a short-term heat treatment. In this case, the product is initially heated to a maximum temperature above Ac.sub.3, to 850° C. in the present example, is briefly held at this temperature, and is then rapidly cooled. The heating rate is 25 K/s.

[0223] The holding time at the maximum temperature is 3 seconds; finally, a cooling at a cooling rate of 140 K/s is performed. The Hollomon-Jaffee parameter of the short-term hardening that is performed is 19458.