CN118176310A - Method for producing hot-rolled strips from fine-grained steel - Google Patents

Method for producing hot-rolled strips from fine-grained steel Download PDF

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Publication number
CN118176310A
CN118176310A CN202280073259.1A CN202280073259A CN118176310A CN 118176310 A CN118176310 A CN 118176310A CN 202280073259 A CN202280073259 A CN 202280073259A CN 118176310 A CN118176310 A CN 118176310A
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CN
China
Prior art keywords
hot
rolled strip
hot rolled
strip
temperature
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Pending
Application number
CN202280073259.1A
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Chinese (zh)
Inventor
C·哈塞尔
C·克林肯贝格
G·帕德贝格
M·彼得斯
A·斯普罗科
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SMS Group GmbH
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SMS Group GmbH
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Publication of CN118176310A publication Critical patent/CN118176310A/en
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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
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The invention relates to a method for producing hot-rolled strip from fine-grained steel having a thickness d WB < 1.75mm and an average ferrite grain size g s < 5 mu m. By means of the optimized rolling and cooling strategy, the heat treatment that had to be carried out on the hot-rolled strip before in order to adjust the mechanical properties was avoided.

Description

Method for producing hot-rolled strips from fine-grained steel
Technical Field
The invention relates to a method for producing hot-rolled strip from fine-grained steel having a thickness d WB < 1.75mm and an average ferrite grain size g s < 5 mu m.
Background
Strip steel made of fine grain steel is typically manufactured in a multi-step process. A hot-rolled strip is first produced from a slab by means of various thermoforming and then wound into a coil. The hot-rolled strip thus produced is subsequently heat-treated and/or cold-rolled, and the thickness, the structure and the desired mechanical properties of the strip are adjusted accordingly. However, from the consumer's perspective, it is desirable to design the known multi-step process to be less expensive and simpler. One possibility is to adjust the thickness and structure of the strip after hot rolling for the possible end use.
It is known from the prior art to roll slabs, in particular thin slabs, to hot-rolled strips with a thickness d WB < 1.5 mm. For this purpose, the slab or sheet-metal blank is heated to a material-specific forming temperature and rolled into a strip in a strip hot rolling mill by means of a series of reduction passes (Abnahmestich). The hot rolled strip is then wound into a coil. The microstructure of the hot-rolled strip and the mechanical properties obtained are adjusted by the cooling conditions after hot forming and cooling of the hot-rolled strip in the coil.
A disadvantage of this known method is that the cooling in the coil is so slow that an applicable microstructure state cannot be reached immediately, as the strip is wound tightly, and the microstructure state must first be produced or adjusted by a subsequent additional annealing treatment. It is therefore an object of the present invention to further improve the known methods for manufacturing fine grain steel such that the hot rolled steel sheet is directly applicable in terms of its thickness and its microstructure.
Disclosure of Invention
The object of the invention is achieved by a method having the features of claim 1 and a hot rolled strip having the features of claim 10 or claim 11. A hot rolled strip made of fine grain steel material is subjected to at least the following processing steps:
Heating the blank, in particular the slab or sheet blank, to a forming temperature;
Hot rolling the blank into a strip in a hot strip mill having more than two reduction passes, in particular having more than five reduction passes;
Winding the hot rolled strip into a coil;
After the final reduction pass, the hot rolled strip is cooled from the hot rolling temperature T w to a temperature below the transformation temperature T H of the steel using a rapid cooling system, in particular a compact cooling system, before being coiled into a coil. The transformation temperature T H is the temperature at which austenite starts to decompose. The approximate transition temperature T H can be read from the average chemical analysis and associated ZTU or ZTA charts. Alternatively, a balance model may also be used for the simulation of the transition temperature T H. The transition temperature T H thus determined must also be adjusted if necessary, since segregation of the chemical elements during hardening can lead to local deviations in the chemical analysis. This will change the local decomposition temperature and may thus change it to a higher or lower local transition temperature. The transition temperature T H is adjusted so that the core and transition region of the slab are preferably considered in the transition temperature T H.
The cooling of the hot strip by the rapid cooling system is carried out at a relative cooling rate a R of a R. Gtoreq.600K/(s.mm), more preferably a R. Gtoreq.800K/(s.mm). Furthermore, after the final reduction pass, the hot strip is cooled by the rapid cooling system beginning within a period of time t.ltoreq.0.2 s, preferably t.ltoreq.0.1 s.
The combination of the features of cooling speed, thickness of the hot-rolled strip and cooling to a temperature below the transformation temperature T H of pearlite, bainite and/or martensite gives a hot-rolled strip with a yield limit of 300MPa to 400MPa at a thickness d WB < 1.5mm and with a yield limit of 400MPa to 500MPa at a thickness d WB. Gtoreq.1.5 mm and. Gtoreq.1.75 mm.
Preferred embodiments of the method are shown in claims 2 to 9 when dependent on claim 1. The hot strip is cooled from the hot rolling temperature T w to a temperature below the transition temperature T H in a pass of 6m or less, preferably 4m or less after the final reduction pass. The more recently the rapid cooling starts after the final reduction pass, the better grain growth can be reduced or prevented by rapid cooling according to the invention. In particular for fine grain steels, emphasis must be placed herein on inhibiting undesirable grain growth.
Preferably, water is used as coolant to cool to a temperature below the transition temperature T H. Here, water is a standardized coolant, which is easy to transport and easy to provide in terms of process technology. The cooling water used may also contain additives that alter the cooling properties of the water. In the sense of the present invention, gas, in particular air, is also understood to be an additive to cooling water. It is irrelevant whether the gas is used for conveying or atomizing the cooling water after or by means of a spray nozzle, for example. Additives in the sense of the present invention may also be chemical substances suitable for modifying the boiling point or other physical or chemical properties of the cooling water.
During cooling, the relative water volume flow V.gtoreq.0.002 m 3/kg, preferably V.gtoreq.0.004 m 3/kg, is preferably set based on the mass flow of the hot strip. In this range, sufficient water is provided to achieve the desired cooling effect without introducing undue cost pressure on the water economy of the strip hot rolling mill.
The control and regulation steps of the at least one process model define a target value for the cooling rate before the last reduction pass and/or adjust the target value for the cooling rate before the last reduction pass during hot forming of the hot strip. The process model simulates the development of the microstructure during the hot rolling process, preferably on-line, on the basis of chemical analysis of the hot rolled strip to be rolled and further process parameters. In the sense of the present invention, process parameters are understood to be all process parameters which are directly or indirectly relevant for the production of hot rolled strip in a strip hot rolling mill. The direct process parameters include, for example, rolling speed, slab temperature, chemical analysis or pass reduction (Stichabnahme), and the indirect process parameters are, for example, roll age (Walzenalter), cooling water composition or plant status. Simulation models for simulating tissue structures based on chemical analysis and known temperature profiles are known in the art. The control and regulation units of the rolling mill train determine the possible temperature profile of the hot-rolled strip on the basis of the existing target specifications or actual values by means of a known temperature model. This is preferably done cyclically during the ongoing process. The actual structure of the hot strip is simulated from these temperature distributions by means of the structure model in the same cycle. If the actual microstructure deviates from the target microstructure, the target specification, for example the cooling intensity or the pass reduction at different points in the rolling mill train, is adjusted by means of a control or regulation element.
Furthermore, the process model determines a target value of the cooling rate to be set by means of an optimization algorithm, with which the target structure, in particular the ferrite grain size, is achieved. Such control or regulation elements improve the regulation of the mechanical properties of the finished hot strip by targeted regulation of the microstructure development during the hot rolling process. The control unit can better compensate and optimize possible fluctuations by means of the process model.
Preferably, the microstructure sensor determines the microstructure composition of the hot strip and the process model takes into account the measured actual microstructure composition when determining the target value for the cooling rate. The use of a texture sensor at a location inside the strip mill not only enables the determination of the possible texture development from chemical analysis, but also enables the actual state of the texture to be taken into account when precalculating the texture development. Thus, the target value of the cooling rate is determined more accurately and the deviation is smaller.
The hot-rolled strip is preferably made of a steel material having the following analytical composition:
C (carbon): 0.05% to 0.20%, preferably 0.05% to 0.10%
Si (silicon): 0.01% to 0.50%, preferably 0.05% to 0.20%
Mn (manganese): 0.30% to 2.20%, preferably 0.40% to 1.80%
Al (aluminum): 0.015 to 0.075%, preferably 0.015 to 0.035%
N (nitrogen): 0.000 to 0.050%, preferably 0.001 to 0.025%
Nb (niobium): 0.00% to 0.10%, preferably 0.01% to 0.06%
Ti (titanium): 0.00% to 0.12%, preferably 0.01% to 0.10%
V (vanadium): 0.00% to 0.10%, preferably 0.01% to 0.06%
Mo (molybdenum): 0.00% to 0.35%, preferably 0.01% to 0.10%
Ca (calcium): 0.005% to 0.035%, preferably 0.005% to 0.025%
The balance being Fe (iron) and unavoidable impurities in the manufacture.
Such steels are particularly suitable due to their transformation behaviour and basic mechanical properties.
The Al/N ratio is between 1 and 10, preferably between 1 and 8. The Al/N ratio thus set reduces both edge cracking during hardening of the slab and edge cracking sensitivity in the first forming pass in the rolling train.
The hot strip temperature of the hot strip prior to the final reduction pass prior to the rapid cooling system is preferably at least 50 ℃, more preferably at least 30 ℃ and at most 100 ℃, above the Ae3 temperature of the alloy of the hot strip. It is thereby ensured that ferrite is not formed in the hot-rolled strip until the rapid cooling system starts and that more easily deformed austenite is present when the hot-rolled strip is formed in the rolling stand.
The object of the invention is furthermore achieved by a hot rolled strip manufactured according to the method of any one of claims 1 to 9. The finished hot-rolled strip has a hot-rolled strip thickness d WB of d WB < 1.5mm, preferably d WB < 1.2mm, and a tensile strength R m of 300MPa to 400MPa and a yield limit R e of R e > 340 MPa. The object of the invention is also achieved by a hot rolled strip manufactured according to the method of any one of claims 1 to 7, wherein the hot rolled strip has a hot rolled strip thickness d WB of d WB +.1.75 mm, preferably d WB < 1.4mm, and a tensile strength R m of 400MPa to 500MPa and a yield limit R e of R e +.340 MPa.
Drawings
The description of the invention is accompanied by three figures.
FIG. 1 shows an example of a casting and rolling plant;
FIG. 2 shows an exemplary temperature profile of a hot rolled strip made of fine grain material during a process; and
FIG. 3 shows the degree of formation during the process;
FIG. 4 shows a) a conventional microstructure of fine grain steel; b) Tissue structure after application of the method according to the invention.
Detailed Description
The present invention is described in detail below with reference to the accompanying drawings. Like technical elements are labeled with like reference numerals throughout the drawings.
Fig. 1 shows a schematic structure of a casting and rolling apparatus for manufacturing a hot rolled strip. The continuous casting plant 1 produces slabs or thin slabs from a liquid melt. In the first furnace 2, the slab is heated to a temperature before the first initial pass in the roughing train 3. Between the roughing train 3 and the finishing stand 5 there is a further compensation furnace 4. A compact cooling system 6 according to the invention is arranged after the last finishing stand 4, 5. The compact cooling system is capable of providing sufficient cooling fluid to adjust the desired cooling rate of the strip. After cooling, the strip is wound into a coil on a reel 7.
Fig. 2 shows a graph of the temperature profile a of the hot rolled strip from the first initial pass in the roughing stand to the coiling into a coil in the coiler. Starting from a start pass temperature of, for example, 1120 ℃, the hot rolled strip is rolled in several steps to a thickness of 1.6mm or less. Without further influence, a temperature profile, for example according to the curve a, is present here. The furnace between the first initial pass of the roughing stand and the finishing stand is not used for heating the strip blank, but rather for homogenizing the temperature between the core and the outer layer of the strip blank. After the final shaping step in the final finishing stand, the finished hot rolled strip is cooled to a temperature of 520 ℃ or less by means of a compact cooling system. Followed by laminar cooling (Laminark u hlung) to an exemplary coiling temperature of, for example, 150 ℃.
Table 1: analysis of Fine grained Material (weight percent)
Table 1 shows an exemplary fine grain material analysis. The technically possible shaping levels for this analysis in the individual reduction passes are shown in the graph of fig. 3, together with exemplary actual shaping levels. It can be seen here that the shaping process can basically take place in the first four frames. The possible degree of formation is then reduced, which has a positive effect on the tolerances of the finished hot strip. Thus, the method can adjust and maintain fine grains from the start of molding.
Fig. 4 a) and 4 b) show microstructure microtomes of the hot rolled strip after rolling. Both hot rolled strips are made of the same alloy, i.e. they are rolled from the same batch of slabs. Figure a) shows a microtome of a hot rolled strip manufactured conventionally. Drawing b) shows a microtome of a hot rolled strip manufactured according to the invention. In this case, the two hot-rolled strips are each wound into a coil after hot rolling. As can be seen by comparing microstructure microtablets, the method according to the invention yields significantly finer grains directly after hot rolling. The average grain boundary in FIG. a) was 5.5. Mu.m, and the average grain boundary in FIG. b) was 4.4. Mu.m. The structure adjusted in fig. b) allows the hot rolled strip to be applied directly without additional subsequent heat treatments.
List of reference numerals:
1. Continuous casting equipment
2. Furnace and method for producing the same
3. Roughing mill set
4. Furnace and method for producing the same
5. Finish rolling frame
6. Compact cooling system
7. And (5) a coiling machine.

Claims (11)

1. Method for manufacturing a hot rolled strip from a fine grain steel having a thickness d WB and an average ferrite grain size g s +.5 μm, wherein the manufactured hot rolled strip has a yield limit of 300MPa to 400MPa with a thickness d WB < 1.5mm and a yield limit of 400MPa to 500MPa with a thickness d WB +.1.5 mm and +.1.75 mm, in which method at least the following steps are performed:
-heating the blank, in particular the slab or sheet blank, to a forming temperature;
-hot rolling the blank into a hot rolled strip in a hot strip mill with more than two reduction passes, in particular with more than five reduction passes, the hot rolled strip having a thickness d WB < 1.5mm or a thickness d WB ∈1.5mm and ∈1.75 mm;
-coiling said hot rolled strip into a coil;
it is characterized in that the method comprises the steps of,
-After the final reduction pass, before coiling into coils, cooling the hot rolled strip from a hot rolling temperature T w to a temperature below the transformation temperature T H of the hard phase, in particular pearlite, bainite and/or martensite, using a rapid cooling system, in particular a compact cooling system; and
-Cooling the hot rolled strip by the rapid cooling system at a relative cooling speed a R of a R ≡600K/(s·mm), preferably a R ≡800K/(s·mm);
-after the final reduction pass, starting to cool the hot strip by the rapid cooling system for a period of time equal to or less than 0.2s, preferably equal to or less than 0.1 s.
2. Method according to claim 1, characterized in that the hot rolled strip is cooled from the hot rolling temperature T w to a temperature below the transition temperature T H in a pass of 6m or less, preferably 4m or less after the last reduction pass.
3. The method according to any of the preceding claims, characterized in that the cooling to a temperature below the transition temperature T H is achieved using water as coolant.
4. A method according to claim 3, characterized in that during cooling, the relative water volume flow V is set to be equal to or greater than 0.002m 3/kg, preferably V is equal to or greater than 0.004m 3/kg, based on the mass flow of the hot rolled strip.
5. A method according to any of the preceding claims, characterized in that
The method has a control and regulation unit with a process model, which predefines and/or adjusts the target value of the cooling rate before the last reduction pass during thermoforming; and
-The process model simulates the development of the microstructure during the hot rolling process based on chemical analysis of the hot rolled strip and further process parameters; and
The process model determines a target value for the cooling rate by means of an optimization algorithm, with which the target structure, in particular the ferrite grain size, is achieved.
6. The method of claim 5, wherein the step of determining the position of the probe is performed,
-A texture sensor determines the texture composition of the hot rolled strip; and
-The process model takes into account the measured actual tissue structure composition when determining the target value of the cooling rate.
7. Method according to any one of the preceding claims, characterized in that the hot rolled strip is made of a steel material having the following analytical composition:
C (carbon): 0.05% to 0.20%, preferably 0.05% to 0.10%
Si (silicon): 0.01% to 0.50%, preferably 0.05% to 0.20%
Mn (manganese): 0.30% to 2.20%, preferably 0.40% to 1.80%
Al (aluminum): 0.015 to 0.075%, preferably 0.015 to 0.035%
N (nitrogen): 0.000 to 0.050%, preferably 0.001 to 0.025%
Nb (niobium): 0.00% to 0.10%, preferably 0.01% to 0.06%
Ti (titanium): 0.00% to 0.12%, preferably 0.01% to 0.10%
V (vanadium): 0.00% to 0.10%, preferably 0.01% to 0.06%
Mo (molybdenum): 0.00% to 0.35%, preferably 0.01% to 0.10%
Ca (calcium): 0.005% to 0.035%, preferably 0.005% to 0.025%
The balance being Fe (iron) and unavoidable impurities in the manufacture.
8. The method according to claim 7, characterized in that the Al/N ratio is between 1 and 10, preferably between 1 and 8.
9. Method according to any one of the preceding claims, characterized in that the hot strip temperature of the hot strip before the final reduction pass before the rapid cooling system is at least 50 ℃, preferably at least 30 ℃ and at most 100 ℃, above the Ae3 temperature of the alloy of the hot strip.
10. A hot rolled strip produced by a process according to any one of claims 1 to 9, characterized in that,
-The hot-rolled strip has a hot-rolled strip thickness d WB < 1.5mm, preferably +.1.2 mm; and
-The hot rolled strip has a tensile strength R m of 300MPa to 400MPa and a yield limit of R e ≡340 MPa.
11. A hot rolled strip produced by a process according to any one of claims 1 to 9, characterized in that,
-The hot rolled strip has a hot rolled strip thickness d WB ∈1.75mm, preferably d WB ∈1.4 mm; and
-The hot rolled strip has a tensile strength R m of 400MPa to 500MPa and a yield limit of R e ≡340 MPa.
CN202280073259.1A 2021-11-17 2022-11-17 Method for producing hot-rolled strips from fine-grained steel Pending CN118176310A (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE102021212902.1A DE102021212902A1 (en) 2021-11-17 2021-11-17 Process for producing a hot strip from a fine-grain steel material
DE102021212902.1 2021-11-17
PCT/EP2022/082238 WO2023089012A1 (en) 2021-11-17 2022-11-17 Method for the production of a hot-rolled strip from a fine-grained steel material

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DE (1) DE102021212902A1 (en)
WO (1) WO2023089012A1 (en)

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WO2001020051A1 (en) * 1999-09-16 2001-03-22 Nkk Corporation Steel thin plate having high strength and method for production thereof
JP4062118B2 (en) * 2002-03-22 2008-03-19 Ｊｆｅスチール株式会社 High-tensile hot-rolled steel sheet with excellent stretch characteristics and stretch flange characteristics and manufacturing method thereof
CN102242307B (en) * 2005-08-03 2013-03-27 住友金属工业株式会社 Hot-rolled steel sheet and cold-rolled steel sheet and manufacturing method thereof

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