CA2529837C - Method and installation for the production of hot-rolled strip with a dual-phase microstructure - Google Patents
Method and installation for the production of hot-rolled strip with a dual-phase microstructure Download PDFInfo
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- CA2529837C CA2529837C CA2529837A CA2529837A CA2529837C CA 2529837 C CA2529837 C CA 2529837C CA 2529837 A CA2529837 A CA 2529837A CA 2529837 A CA2529837 A CA 2529837A CA 2529837 C CA2529837 C CA 2529837C
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
-
- 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
- C21D11/00—Process control or regulation for heat treatments
- C21D11/005—Process control or regulation for heat treatments for cooling
-
- 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
-
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
- B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials 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)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
The aim of the invention is to be able to produce dual-phase steels under local conditions even in the existing cooling section of a continuous casting and rolling plant by means of controlled cooling of the hot-rolled strip in two cooling stages following the forming process. Said aim is achieved by respecting the chemical composition of the initial steel within precisely defined limits and cooling in two stages from a finished rolled strip temperature Tfinish of A3 -100K < Tfinish < A3 -50K to a coiling strip temperature Tcoiling of < 300 ~C (< initial martensite temperature), the cooling speed V1,2 in both cooling stages ranging between 30 and 150 K/s, preferably between 50 and 90 K/s. The first cooling stage is carried out until the cooling curve enters the ferrite range, whereupon the heat released by the transformation of the austenite into ferrite is used for isothermally holding the obtained strip temperature Tconst during a holding time of = 5 s until the beginning of the second cooling stage.
Description
METHOD AND INSTALLATION FOR THE PRODUCTION OF HOT-ROLLED
STRIP WITH A DUAL-PHASE MICROSTRUCTURE
The invention concerns a method for producing hot-rolled strip with a dual-phase microstructure consisting of ferrite and martensite, wherein at least 70?, of the austenite is transformed to ferrite from the hot-rolled state by a controlled two-stage cooling operation after the finish rolling to a strip temperature below the martensite start temperature in a cooling line that consists of successive, spaced water cooling units.
Systematic microstructural transformation by controlled cooling is steels is well known, and to produce dual-phase steels, this controlled cooling is carried out after the working of the hot strip is complete. The adjustment of the attainable dual-phase microstructure depends essentially on the cooling rates that are technically possible in the installation and on the chemical composition of the steel. In this regard, it is important in any case to achieve sufficient ferrite formation of at least 70: in the first cooling stage. During this first cooling stage, transformation of the austenite in the pearlite stage should be avoided.
The cooling capacity of the second cooling stage following the first cooling stage must be sufficiently high that coiling temperatures below the martensite start temperature are reached.
Only then is the formation of a dual-phase microstructure with ferritic and martensitic constituents ensured.
The previously known production of dual-phase steels is unproblematic at low strip speeds or with sufficiently long cooling lines. However, at very high strip speeds, the beginning of the second cooling stage can. be shifted so far in the present cooling line that the subsequent martensite formation remains incomplete or does not occur at all. This results in a mixed microstructure consisting of ferrite, bainite and some martensite, so that the desired mechanical properties of a pure dual-phase microstructure are not obtained.
EP 0 747 495 Bl describes a method for producing high-strength steel plate with a microstructure consisting of 75%
ferrite, at least loo martensite and possibly bainite and retained austenite. Accordingly, this is not a microstructure of pure dual-phase steels. A steel microalloyed with niobium is used as the alloy. It is produced by systematically cooling the hot-rolled steel plate, wherein a rapid cooling follows a slow cooling or, alternatively, a rapid cooling precedes the slow cooling. A cooling rate of 2-15 C/s within a cooling time of 8-40 s is given for the first cooling stage to a final temperature between the AR1 point and 730 C. In the second cooling stage, the steel is cooled to a temperature of 300 C at a cooling rate of 20-150 C/s. In the alternative method, in which the rapid cooling stage precedes the slow cooling stage, rapid cooling is carried out to a temperature below the Ar.3 point at a cooling rate of 20-150 C/s.
EP 1 108 072 Bl describes a method for producing dual-phase steels, in which a dual-phase microstructure consisting of 70-90% ferrite and 30-10% martensite is achieved with a two-stage cooling operation (first slow, then rapid) carried out after the finish rolling. The first (slow) cooling is carried out in a cooling line in which the hot-rolled strip is cooled in a well-defined way by successive, spaced water cooling zones at a cooling rate of 20-30 K/s. In this connection, the cooling is adjusted in such a way that the cooling curve enters the ferrite range at a temperature that is still so high that ferrite formation can occur rapidly. The first cooling is continued until at least 70% of the austenite has transformed to ferrite.
STRIP WITH A DUAL-PHASE MICROSTRUCTURE
The invention concerns a method for producing hot-rolled strip with a dual-phase microstructure consisting of ferrite and martensite, wherein at least 70?, of the austenite is transformed to ferrite from the hot-rolled state by a controlled two-stage cooling operation after the finish rolling to a strip temperature below the martensite start temperature in a cooling line that consists of successive, spaced water cooling units.
Systematic microstructural transformation by controlled cooling is steels is well known, and to produce dual-phase steels, this controlled cooling is carried out after the working of the hot strip is complete. The adjustment of the attainable dual-phase microstructure depends essentially on the cooling rates that are technically possible in the installation and on the chemical composition of the steel. In this regard, it is important in any case to achieve sufficient ferrite formation of at least 70: in the first cooling stage. During this first cooling stage, transformation of the austenite in the pearlite stage should be avoided.
The cooling capacity of the second cooling stage following the first cooling stage must be sufficiently high that coiling temperatures below the martensite start temperature are reached.
Only then is the formation of a dual-phase microstructure with ferritic and martensitic constituents ensured.
The previously known production of dual-phase steels is unproblematic at low strip speeds or with sufficiently long cooling lines. However, at very high strip speeds, the beginning of the second cooling stage can. be shifted so far in the present cooling line that the subsequent martensite formation remains incomplete or does not occur at all. This results in a mixed microstructure consisting of ferrite, bainite and some martensite, so that the desired mechanical properties of a pure dual-phase microstructure are not obtained.
EP 0 747 495 Bl describes a method for producing high-strength steel plate with a microstructure consisting of 75%
ferrite, at least loo martensite and possibly bainite and retained austenite. Accordingly, this is not a microstructure of pure dual-phase steels. A steel microalloyed with niobium is used as the alloy. It is produced by systematically cooling the hot-rolled steel plate, wherein a rapid cooling follows a slow cooling or, alternatively, a rapid cooling precedes the slow cooling. A cooling rate of 2-15 C/s within a cooling time of 8-40 s is given for the first cooling stage to a final temperature between the AR1 point and 730 C. In the second cooling stage, the steel is cooled to a temperature of 300 C at a cooling rate of 20-150 C/s. In the alternative method, in which the rapid cooling stage precedes the slow cooling stage, rapid cooling is carried out to a temperature below the Ar.3 point at a cooling rate of 20-150 C/s.
EP 1 108 072 Bl describes a method for producing dual-phase steels, in which a dual-phase microstructure consisting of 70-90% ferrite and 30-10% martensite is achieved with a two-stage cooling operation (first slow, then rapid) carried out after the finish rolling. The first (slow) cooling is carried out in a cooling line in which the hot-rolled strip is cooled in a well-defined way by successive, spaced water cooling zones at a cooling rate of 20-30 K/s. In this connection, the cooling is adjusted in such a way that the cooling curve enters the ferrite range at a temperature that is still so high that ferrite formation can occur rapidly. The first cooling is continued until at least 70% of the austenite has transformed to ferrite.
This cooling stage is immediately followed by the other (rapid) cooling stage without any holding time.
Proceeding from the aforementioned prior art with the various possible means that have been described for producing dual-phase microstructure, the objective of the invention is to specify a method by which and an installation in which the production of hot-rolled strip with dual-phase microstructure can be carried out in a conventional continuous casting and rolling installation with the local limitations that exist there and thus with the given time constraints. The cooling line of an installation of this.type is characterized by the fact that the total length generally does not exceed 50 m and that compact cooling is not provided.
The objective with respect to the method is achieved with the method steps described herein. The method is characterized by the fact that, to obtain a hot-rolled strip with a dual-phase microstructure consisting of 70-95% ferrite and 30-5% martensite with high mechanical strength and high formability (tensile strength greater than 600 MPa, elongation after fracture at least 25%) in the cooling line of a continuous casting and rolling installation, starting from a steel with the following chemical composition: 0.01-0.08% C, 0.9% Si, 0.5-1.6%
Proceeding from the aforementioned prior art with the various possible means that have been described for producing dual-phase microstructure, the objective of the invention is to specify a method by which and an installation in which the production of hot-rolled strip with dual-phase microstructure can be carried out in a conventional continuous casting and rolling installation with the local limitations that exist there and thus with the given time constraints. The cooling line of an installation of this.type is characterized by the fact that the total length generally does not exceed 50 m and that compact cooling is not provided.
The objective with respect to the method is achieved with the method steps described herein. The method is characterized by the fact that, to obtain a hot-rolled strip with a dual-phase microstructure consisting of 70-95% ferrite and 30-5% martensite with high mechanical strength and high formability (tensile strength greater than 600 MPa, elongation after fracture at least 25%) in the cooling line of a continuous casting and rolling installation, starting from a steel with the following chemical composition: 0.01-0.08% C, 0.9% Si, 0.5-1.6%
Mn, 1.2% Al, 0.3-1.2o Cr, with the remainder consisting of Fe and customary trace elements, the two-stage controlled cooling is carried out from a finish rolling strip temperature Tfinietõ
such that A3 - 100 K < Tfinish < A3 - 50 K, to a coiling strip temperature Tcc,1iiõuu < 300 C (< martensite start temperature) , wherein the cooling rate V1,2 in both cooling stages is V = 30-150 K/s, and preferably V = 50-90 K/s, the first cooling stage is carried out until the cooling curve enters the ferrite range, and then the heat of transformation liberated by the transformation of the austenite to ferrite is used for isothermally holding the strip temperature thereby reached for a holding time of 5 s until the beginning of the second cooling stage.
Due to the short length of conventional cooling lines in existing continuous casting and rolling installation, the production of hot-rolled strip with a dual-phase microstructure is possible only with a special cooling strategy. To allow a special cooling strategy of this type to be carried out, it is absolutely necessary to maintain certain limits of chemical composition, such as those listed above, so that the desired degree of transformation can be achieved with the short total cooling time that is available.
The cooling strategy involves two cooling stages that have selectively variable cooling rates and are interrupted by an isothermal holding time of a maximum of 5 s. The beginning of the holding time, which corresponds to the end of the first cooling stage, is determined by the entrance of the cooling curve into the ferrite range, i.e., the point at which the austenite starts to transform to ferrite. The entire desired transformation of the austenite to at least 700 ferrite occurs in the short isothermal cooling interruption of a maximum of 5 s, during which, in accordance with the invention, the liberated heat of transformation holds the temperature at a constant value by compensating unavoidable air cooling. This holding time is then immediately followed by the second cooling stage, during which the hot-rolled strip is cooled to a temperature below 300 C. Since this temperature is below the martensite start temperature, the desired level of martensite, which is the second constituent of the dual-phase microstructure, is thus obtained.
In addition to the use of a short holding time, the cooling strategy is defined by an exactly defined, predetermined cooling rate for both cooling stages. This cooling rate is V = 30-150 K/s, and preferably V = 50-90 K/s. It depends on the geometry of the hot-rolled strip and on the chemical composition of the grade of steel that is used. In regard to these cooling rates, it should be noted that a cooling rate of less than 30 K/s is not possible due to the small amount of time available in the conventional cooling line of a continuous casting and rolling installation, and cooling rates greater than 150 K/s also cannot be attained in conventional cooling lines.
Compared to prior-art methods for producing dual-phase hot-rolled strip, the method of the invention is characterized not only by the fact that the initial steel has a different chemical composition but also by the fact that (a) the finish rolling temperature is well below the A3 temperature, (b) cooling is carried out to a temperature below 300 C in the second cooling stage, (c) the cooling rates are below 150 K/s and above 30 K/s, (d) there is a very short holding time of a maximum of 5 seconds, during which no cooling occurs, between the two cooling stages, and (e) the transformation to ferrite occurs isothermally.
A continuous casting and rolling installation for carrying out the method of the invention is characterized by a conventional cooling line that is' installed after the last finishing stand and has several successive, spaced water cooling units, which can be automatically controlled. The spray bars present in each cooling unit are arranged in such a way that a specific amount of water is uniformly sprayed onto the upper and lower surfaces of the hot-rolled strip. The total amount of water can be automatically controlled by turning individual spray bars on or off during rolling. The number and arrangement of the water spray bars that are turned on can be variably adjusted in advance to obtain an optimum adjustment of the entire cooling line to the cooling conditions that are to be established.
Further details, features and characteristic of the invention are explained in greater detail below with reference to the specific embodiment of the invention that is illustrated in the schematic drawings.
-- Figure 1 shows a time-temperature cooling curve of a hot-rolled strip.
-- Figure 2 shows a layout of a cooling line in a continuous casting and rolling installation with a 6-stand finishing train.
-- Figure 3 shows a layout of a cooling line in a continuous casting and rolling installation with a 7-stand finishing train.
-- Figure 1 shows an example of a time-temperature cooling curve of a hot-rolled strip that was cooled by the method of the invention on the-runout roller table in a cooling line 1. The hot-rolled strip, which had the following composition: 0.060 C, 0.10 Si, 1.2% Mn, 0.0150 P, 0.06% S, 0.036% Al, 0.150 Cu, 0.0540 Ni, 0.71% Cr, the remainder consisting of Fe and customary trace elements, was cooled in a first cooling stage at a cooling rate V1 of 54 K/s from an adjusted finish rolling temperature Tflnisn of 800 C to a hot-rolled strip temperature of 670 C, at which the cooling curve entered the ferrite range. During a holding time of about 4 s, the temperature of the hot-rolled strip remained at this holding temperature and then the final cooling was carried out in a second cooling stage, in which the strip was cooled to a temperature below 300 C (about 250 C coiling temperature) at a cooling rate V2 of 84 K/s. Tests on the hot-rolled strip produced by this method, which had a dual-phase microstructure in the desired range of at least 700 ferrite and less than 200 martensite, yielded a tensile strength of 620 MPa combined with a ratio of yield stress to tensile strength of 0.52.
Figure 2 shows an example of a layout of a cooling line 1 of a conventional continuous casting and rolling installation.
The cooling line 1, through which the hot-rolled strip passes in direction of conveyance 8, is located between the last finishing stand 2 and the coiler 5. A temperature-measuring point 6 for monitoring the temperature of the hot-rolled strip 10 entering the cooling line 1 is located between the last finishing stand 2 and the first water cooling unit 31. The cooling line 1 shown in Figure 2 comprises a total of eight cooling units 31-7 and 4.
The latter is often realized as a trimming zone 4. More generally, a conventional cooling line comprises six to nine cooling units, depending on the particular continuous casting and rolling installation.
The example illustrated in Figure 2 is the typical layout of a cooling line for a 6-stand continuous casting and rolling installation, as is apparent from the gap between cooling units 3-7 and 4. Subsequent conversion to a 7-stand finishing train often requires that, for example, the first cooling unit (cooling zone) 31 be moved to the rear into the structural gap between the cooling units 37 and 4. In this case, the cooling line 1' has a layout of the type shown in Figure 3, which differs from the layout of the cooling line 1 in Figure 2 only by the elimination of this sturctural gap between the cooling units 37 and 4. Therefore, the reference numbers of the individual structural parts and assemblies of Figure 3 are the same as the reference numbers of Figure 2. An exception to this is the first cooling unit 31', whose upper spray bar, in contrast to the spray bar of cooling unit 31 in Figure 2, is designed with the standard length of the cooling units 32 to 37.
In most cases, each cooling unit has four spray bars on both the upper side and the lower side. Each spray bar in turn consists of two rows of small water pipes for cooling the upper surface of the strip 10' and the lower surface of the strip 10".
As a special feature, the cooling unit 31 in Figure 2 is shortened by one spray bar on the upper side due to limited space.
In contrast to the upstream cooling units 31-7, which have one switchable valve 7 per spray bar, the trimming zone 4 has two valves 7 for each spray bar. This means that in the trimming zone, each row of small cooling pipes can be individually controlled, and thus the amount of water can be more finely controlled.
The delivery speed of the strip from the finishing train varies with the rolled thickness of the finished strip.
Accordingly, the mode of operation of the cooling line must be adjusted to be able to adjust the time-temperature control necessary for the adjustment of the strip properties. For a strip thickness of 3 mm, for example, the first required cooling level is attained with the cooling units 31 and 32, while the second cooling level is realized with cooling units 3,,, 36, 37, and 4. Due to the altered boundary conditions for a finished strip with a thickness of 2.0 mm, only cooling units 3h, 37, and 4 need to be used for the second cooling stage.
List of Reference Numbers 1 cooling line 2 last finishing stand 31-7 water cooling units 4 water cooling unit (trimming zone) coiler 6 temperature-measuring point 7 switchable valve 8 direction of conveyance hot-rolled strip 10' upper surface of the strip 10" lower surface of the strip V1 cooling rate of the first cooling stage VZ cooling rate of the second cooling stage Til,l::i, strip temperature after the last finishing stand T,.),,at. strip temperature after the holding time T,7,,111õg strip temperature at the end of cooling (coil temperature)
such that A3 - 100 K < Tfinish < A3 - 50 K, to a coiling strip temperature Tcc,1iiõuu < 300 C (< martensite start temperature) , wherein the cooling rate V1,2 in both cooling stages is V = 30-150 K/s, and preferably V = 50-90 K/s, the first cooling stage is carried out until the cooling curve enters the ferrite range, and then the heat of transformation liberated by the transformation of the austenite to ferrite is used for isothermally holding the strip temperature thereby reached for a holding time of 5 s until the beginning of the second cooling stage.
Due to the short length of conventional cooling lines in existing continuous casting and rolling installation, the production of hot-rolled strip with a dual-phase microstructure is possible only with a special cooling strategy. To allow a special cooling strategy of this type to be carried out, it is absolutely necessary to maintain certain limits of chemical composition, such as those listed above, so that the desired degree of transformation can be achieved with the short total cooling time that is available.
The cooling strategy involves two cooling stages that have selectively variable cooling rates and are interrupted by an isothermal holding time of a maximum of 5 s. The beginning of the holding time, which corresponds to the end of the first cooling stage, is determined by the entrance of the cooling curve into the ferrite range, i.e., the point at which the austenite starts to transform to ferrite. The entire desired transformation of the austenite to at least 700 ferrite occurs in the short isothermal cooling interruption of a maximum of 5 s, during which, in accordance with the invention, the liberated heat of transformation holds the temperature at a constant value by compensating unavoidable air cooling. This holding time is then immediately followed by the second cooling stage, during which the hot-rolled strip is cooled to a temperature below 300 C. Since this temperature is below the martensite start temperature, the desired level of martensite, which is the second constituent of the dual-phase microstructure, is thus obtained.
In addition to the use of a short holding time, the cooling strategy is defined by an exactly defined, predetermined cooling rate for both cooling stages. This cooling rate is V = 30-150 K/s, and preferably V = 50-90 K/s. It depends on the geometry of the hot-rolled strip and on the chemical composition of the grade of steel that is used. In regard to these cooling rates, it should be noted that a cooling rate of less than 30 K/s is not possible due to the small amount of time available in the conventional cooling line of a continuous casting and rolling installation, and cooling rates greater than 150 K/s also cannot be attained in conventional cooling lines.
Compared to prior-art methods for producing dual-phase hot-rolled strip, the method of the invention is characterized not only by the fact that the initial steel has a different chemical composition but also by the fact that (a) the finish rolling temperature is well below the A3 temperature, (b) cooling is carried out to a temperature below 300 C in the second cooling stage, (c) the cooling rates are below 150 K/s and above 30 K/s, (d) there is a very short holding time of a maximum of 5 seconds, during which no cooling occurs, between the two cooling stages, and (e) the transformation to ferrite occurs isothermally.
A continuous casting and rolling installation for carrying out the method of the invention is characterized by a conventional cooling line that is' installed after the last finishing stand and has several successive, spaced water cooling units, which can be automatically controlled. The spray bars present in each cooling unit are arranged in such a way that a specific amount of water is uniformly sprayed onto the upper and lower surfaces of the hot-rolled strip. The total amount of water can be automatically controlled by turning individual spray bars on or off during rolling. The number and arrangement of the water spray bars that are turned on can be variably adjusted in advance to obtain an optimum adjustment of the entire cooling line to the cooling conditions that are to be established.
Further details, features and characteristic of the invention are explained in greater detail below with reference to the specific embodiment of the invention that is illustrated in the schematic drawings.
-- Figure 1 shows a time-temperature cooling curve of a hot-rolled strip.
-- Figure 2 shows a layout of a cooling line in a continuous casting and rolling installation with a 6-stand finishing train.
-- Figure 3 shows a layout of a cooling line in a continuous casting and rolling installation with a 7-stand finishing train.
-- Figure 1 shows an example of a time-temperature cooling curve of a hot-rolled strip that was cooled by the method of the invention on the-runout roller table in a cooling line 1. The hot-rolled strip, which had the following composition: 0.060 C, 0.10 Si, 1.2% Mn, 0.0150 P, 0.06% S, 0.036% Al, 0.150 Cu, 0.0540 Ni, 0.71% Cr, the remainder consisting of Fe and customary trace elements, was cooled in a first cooling stage at a cooling rate V1 of 54 K/s from an adjusted finish rolling temperature Tflnisn of 800 C to a hot-rolled strip temperature of 670 C, at which the cooling curve entered the ferrite range. During a holding time of about 4 s, the temperature of the hot-rolled strip remained at this holding temperature and then the final cooling was carried out in a second cooling stage, in which the strip was cooled to a temperature below 300 C (about 250 C coiling temperature) at a cooling rate V2 of 84 K/s. Tests on the hot-rolled strip produced by this method, which had a dual-phase microstructure in the desired range of at least 700 ferrite and less than 200 martensite, yielded a tensile strength of 620 MPa combined with a ratio of yield stress to tensile strength of 0.52.
Figure 2 shows an example of a layout of a cooling line 1 of a conventional continuous casting and rolling installation.
The cooling line 1, through which the hot-rolled strip passes in direction of conveyance 8, is located between the last finishing stand 2 and the coiler 5. A temperature-measuring point 6 for monitoring the temperature of the hot-rolled strip 10 entering the cooling line 1 is located between the last finishing stand 2 and the first water cooling unit 31. The cooling line 1 shown in Figure 2 comprises a total of eight cooling units 31-7 and 4.
The latter is often realized as a trimming zone 4. More generally, a conventional cooling line comprises six to nine cooling units, depending on the particular continuous casting and rolling installation.
The example illustrated in Figure 2 is the typical layout of a cooling line for a 6-stand continuous casting and rolling installation, as is apparent from the gap between cooling units 3-7 and 4. Subsequent conversion to a 7-stand finishing train often requires that, for example, the first cooling unit (cooling zone) 31 be moved to the rear into the structural gap between the cooling units 37 and 4. In this case, the cooling line 1' has a layout of the type shown in Figure 3, which differs from the layout of the cooling line 1 in Figure 2 only by the elimination of this sturctural gap between the cooling units 37 and 4. Therefore, the reference numbers of the individual structural parts and assemblies of Figure 3 are the same as the reference numbers of Figure 2. An exception to this is the first cooling unit 31', whose upper spray bar, in contrast to the spray bar of cooling unit 31 in Figure 2, is designed with the standard length of the cooling units 32 to 37.
In most cases, each cooling unit has four spray bars on both the upper side and the lower side. Each spray bar in turn consists of two rows of small water pipes for cooling the upper surface of the strip 10' and the lower surface of the strip 10".
As a special feature, the cooling unit 31 in Figure 2 is shortened by one spray bar on the upper side due to limited space.
In contrast to the upstream cooling units 31-7, which have one switchable valve 7 per spray bar, the trimming zone 4 has two valves 7 for each spray bar. This means that in the trimming zone, each row of small cooling pipes can be individually controlled, and thus the amount of water can be more finely controlled.
The delivery speed of the strip from the finishing train varies with the rolled thickness of the finished strip.
Accordingly, the mode of operation of the cooling line must be adjusted to be able to adjust the time-temperature control necessary for the adjustment of the strip properties. For a strip thickness of 3 mm, for example, the first required cooling level is attained with the cooling units 31 and 32, while the second cooling level is realized with cooling units 3,,, 36, 37, and 4. Due to the altered boundary conditions for a finished strip with a thickness of 2.0 mm, only cooling units 3h, 37, and 4 need to be used for the second cooling stage.
List of Reference Numbers 1 cooling line 2 last finishing stand 31-7 water cooling units 4 water cooling unit (trimming zone) coiler 6 temperature-measuring point 7 switchable valve 8 direction of conveyance hot-rolled strip 10' upper surface of the strip 10" lower surface of the strip V1 cooling rate of the first cooling stage VZ cooling rate of the second cooling stage Til,l::i, strip temperature after the last finishing stand T,.),,at. strip temperature after the holding time T,7,,111õg strip temperature at the end of cooling (coil temperature)
Claims (5)
1. Method for producing hot-rolled strip (10) with a dual-phase microstructure consisting of ferrite and martensite, wherein at least 70% of the austenite is transformed to ferrite from the hot-rolled state by a controlled two-stage cooling operation after the finish rolling to a strip temperature below the martensite start temperature in a cooling line (1, 1') that consists of successive, spaced water cooling units (3 1-7, 4) characterized by the fact that, to obtain a hot-rolled strip (10) with a dual-phase microstructure consisting of 70-95%
ferrite and 30-5% martensite with high mechanical strength and high formability (tensile strength greater than 600 MPa, elongation after fracture at least 25%) in the cooling line of a continuous casting and rolling installation, starting from a steel with the following chemical composition: 0.01-0.08% C, 0.9% Si, 0.5-1.6% Mn, 1.2% Al, 0.3-1.2% Cr, remainder Fe and customary trace elements:
(a) the two-stage controlled cooling is carried out from a finish rolling strip temperature T finish, such that A3 - 100 K <
T finish < A3 - 50 K, to a coiling strip temperature T coiling < 300°C
(< martensite start temperature), wherein the cooling rate V1,2 in both cooling stages is V = 30-150 K/s, 90 K/s, and (b) the first cooling stage is carried out until the cooling curve enters the ferrite range, and then the heat of transformation liberated by the transformation of the austenite to ferrite is used for isothermally holding the strip temperature thereby reached T const. for a holding time of 5 s until the beginning of the second cooling stage.
ferrite and 30-5% martensite with high mechanical strength and high formability (tensile strength greater than 600 MPa, elongation after fracture at least 25%) in the cooling line of a continuous casting and rolling installation, starting from a steel with the following chemical composition: 0.01-0.08% C, 0.9% Si, 0.5-1.6% Mn, 1.2% Al, 0.3-1.2% Cr, remainder Fe and customary trace elements:
(a) the two-stage controlled cooling is carried out from a finish rolling strip temperature T finish, such that A3 - 100 K <
T finish < A3 - 50 K, to a coiling strip temperature T coiling < 300°C
(< martensite start temperature), wherein the cooling rate V1,2 in both cooling stages is V = 30-150 K/s, 90 K/s, and (b) the first cooling stage is carried out until the cooling curve enters the ferrite range, and then the heat of transformation liberated by the transformation of the austenite to ferrite is used for isothermally holding the strip temperature thereby reached T const. for a holding time of 5 s until the beginning of the second cooling stage.
2. Continuous casting and rolling installation for producing hot-rolled strip (10) with a dual-phase microstructure from the hot-rolled state, with a cooling line (1, 1'), which is installed after the last finishing stand (2) and has several successive, spaced water cooling units (3 1-7, 4), for carrying out the method in accordance with Claim 1, characterized by the fact that the cooling line (1, 1') has a standard length (< 50 m) for conventional continuous casting and rolling installations, within which a suitable number of automatically controllable water cooling units (3 1-7, 4) are arranged in such a way that the required cooling rate (V1,2) of each cooling stage can be adjusted and the required holding time at the strip temperature T const. between the two cooling stages can be realized by an adapted mode of operation of the entire cooling line as a function of the strip thickness and the strip speed.
3. Continuous casting and rolling installation in accordance with Claim 2, characterized by the fact that each water cooling unit (3 1-7, 4) contains several spray bars that can be automatically controlled by switchable valves (7), that the spray bars are arranged in such a way that the upper surface (10') and the lower surface (10") of the hot-rolled strip (10) passing through the cooling line are uniformly sprayed with a certain amount of water, and that the amounts of water for the upper surface (10') and the lower surface (10") of the strip can be trimmed even relative to each other.
4. Continuous casting and rolling installation in accordance with Claim 3, characterized by the fact that the last water cooling unit (4) for cooling the upper surface (10') and the lower surface (10") of the strip has eight switchable valves (7) for each four spray bars on the top and on the bottom to allow more exact adjustment of the amount of water.
5. The method for producing hot-rolled strip as claimed in Claim 1 wherein the cooling rate V1,2 in both cooling stages is V = 50 - 90 K/s.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE10327383.2 | 2003-06-18 | ||
| DE10327383A DE10327383C5 (en) | 2003-06-18 | 2003-06-18 | Plant for the production of hot strip with dual phase structure |
| PCT/EP2004/006170 WO2004111279A2 (en) | 2003-06-18 | 2004-06-08 | Method and installation for the production of hot-rolled strip having a dual-phase structure |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2529837A1 CA2529837A1 (en) | 2004-12-23 |
| CA2529837C true CA2529837C (en) | 2012-08-21 |
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ID=33546580
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA2529837A Expired - Fee Related CA2529837C (en) | 2003-06-18 | 2004-06-08 | Method and installation for the production of hot-rolled strip with a dual-phase microstructure |
Country Status (14)
| Country | Link |
|---|---|
| US (1) | US20070175548A1 (en) |
| EP (1) | EP1633894B1 (en) |
| JP (1) | JP5186636B2 (en) |
| KR (1) | KR20060057538A (en) |
| CN (1) | CN100381588C (en) |
| CA (1) | CA2529837C (en) |
| DE (1) | DE10327383C5 (en) |
| EG (1) | EG23893A (en) |
| MY (1) | MY136875A (en) |
| RU (1) | RU2346061C2 (en) |
| TW (1) | TWI300443B (en) |
| UA (1) | UA81329C2 (en) |
| WO (1) | WO2004111279A2 (en) |
| ZA (1) | ZA200509876B (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN100447260C (en) * | 2006-06-23 | 2008-12-31 | 宝山钢铁股份有限公司 | Quick cooling test plant for disk type band steel, and method of use |
| EP2361699A1 (en) | 2010-02-26 | 2011-08-31 | Siemens Aktiengesellschaft | Method for cooling sheet metal with a cooling section, cooling section and control and/or regulating device for a cooling section |
| DE102011000089A1 (en) * | 2011-01-11 | 2012-07-12 | Thyssenkrupp Steel Europe Ag | Method for producing a hot rolled flat steel product |
| CN103215420B (en) * | 2012-12-31 | 2015-02-04 | 西安石油大学 | Obtaining method of large deformation pipe line steel double phase structure |
| CN104043660B (en) * | 2013-09-26 | 2015-09-30 | 北大方正集团有限公司 | A kind of production technology of non-hardened and tempered steel |
| DE102017206540A1 (en) * | 2017-04-18 | 2018-10-18 | Sms Group Gmbh | Apparatus and method for cooling metal strips or sheets |
| DE102017127470A1 (en) * | 2017-11-21 | 2019-05-23 | Sms Group Gmbh | Chilled beams and cooling process with variable cooling rate for steel sheets |
| DE102017220891A1 (en) * | 2017-11-22 | 2019-05-23 | Sms Group Gmbh | Method for cooling a metallic material and cooling beam |
| CN109576581A (en) | 2018-11-30 | 2019-04-05 | 宝山钢铁股份有限公司 | A kind of great surface quality, low yield strength ratio hot-rolled high-strength steel plate and manufacturing method |
| CN110724801B (en) * | 2019-10-28 | 2021-02-12 | 重庆科技学院 | Method for improving strength and toughness of Cr-Mo ultra-high strength steel by direct cryogenic treatment after isothermal heat treatment in austenite and ferrite two-phase region |
| RU2724217C1 (en) * | 2020-02-04 | 2020-06-22 | Антон Владимирович Шмаков | Method of producing rolled steel |
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| US3533261A (en) * | 1967-06-15 | 1970-10-13 | Frans Hollander | Method and a device for cooling hot-rolled metal strip on a run-out table after being rolled |
| FR223577A (en) * | 1973-12-11 | |||
| US4159218A (en) * | 1978-08-07 | 1979-06-26 | National Steel Corporation | Method for producing a dual-phase ferrite-martensite steel strip |
| SE430902B (en) * | 1979-05-09 | 1983-12-19 | Svenskt Stal Ab | SET TO HEAT TREAT A STALBAND WITH 0.05 - 0.20% CARBON CONTENT AND LOW CONTENTS |
| JPS57137426A (en) * | 1981-02-20 | 1982-08-25 | Kawasaki Steel Corp | Production of low yield ratio, high tensile hot rolled steel plate by mixed structure |
| JPS57137452A (en) * | 1981-02-20 | 1982-08-25 | Kawasaki Steel Corp | Hot rolled high tensile steel plate having composite structure and its manufacture |
| DE3440752A1 (en) * | 1984-11-08 | 1986-05-22 | Thyssen Stahl AG, 4100 Duisburg | METHOD FOR PRODUCING HOT TAPE WITH A TWO-PHASE TEXTURE |
| JPS63207410A (en) | 1987-02-24 | 1988-08-26 | Kawasaki Steel Corp | Method for preventing variation of sheet width of hot rolled steel strip |
| JPH0763749B2 (en) | 1988-11-15 | 1995-07-12 | 日本鋼管株式会社 | Cooling method after hot rolling |
| JPH0390206A (en) * | 1989-08-31 | 1991-04-16 | Kobe Steel Ltd | Control method for cooling of hot rolled steel plate |
| JPH04167916A (en) | 1990-10-30 | 1992-06-16 | Sumitomo Metal Ind Ltd | Water supply pressure control device for spray |
| JPH06190419A (en) | 1992-12-24 | 1994-07-12 | Kawasaki Steel Corp | Method for cooling strip |
| JPH06238312A (en) * | 1993-02-18 | 1994-08-30 | Sumitomo Metal Ind Ltd | Cooling control method for hot rolled steel sheet |
| DE19513999C2 (en) | 1995-04-13 | 1999-07-29 | Sundwig Gmbh | Production line and its use for the production of steel strip |
| FR2735148B1 (en) * | 1995-06-08 | 1997-07-11 | Lorraine Laminage | HIGH-STRENGTH, HIGH-STRENGTH HOT-ROLLED STEEL SHEET CONTAINING NIOBIUM, AND METHODS OF MAKING SAME. |
| EP0750049A1 (en) * | 1995-06-16 | 1996-12-27 | Thyssen Stahl Aktiengesellschaft | Ferritic steel and its manufacture and use |
| CN1161378A (en) * | 1996-01-16 | 1997-10-08 | 艾利格汉尼·勒德鲁姆公司 | Process for producing dual phase ferritic stainless steel strip |
| EP2314729B2 (en) * | 1997-03-17 | 2017-03-08 | Nippon Steel & Sumitomo Metal Corporation | Dual-phase type high-strength steel sheets having high impact energy absorption properties |
| DE19833321A1 (en) * | 1998-07-24 | 2000-01-27 | Schloemann Siemag Ag | Method and installation to produce dual phase steels out of hot-rolled strip, with cooling rate at first cooling stage set sufficiently low to obtain temperature which is sufficiently high for rapid transformation of austenite into ferrite |
| DE19963186B4 (en) | 1999-12-27 | 2005-04-14 | Siemens Ag | Method for controlling and / or regulating the cooling section of a hot strip mill for rolling metal strip and associated device |
| DE10129565C5 (en) | 2001-06-20 | 2007-12-27 | Siemens Ag | Cooling method for a hot-rolled rolling stock and corresponding cooling line model |
| US20080178972A1 (en) | 2006-10-18 | 2008-07-31 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd) | High strength steel sheet and method for producing the same |
-
2003
- 2003-06-18 DE DE10327383A patent/DE10327383C5/en not_active Expired - Fee Related
-
2004
- 2004-06-08 US US10/561,385 patent/US20070175548A1/en not_active Abandoned
- 2004-06-08 KR KR1020057023848A patent/KR20060057538A/en not_active Application Discontinuation
- 2004-06-08 WO PCT/EP2004/006170 patent/WO2004111279A2/en active Application Filing
- 2004-06-08 CN CNB2004800167574A patent/CN100381588C/en not_active Expired - Fee Related
- 2004-06-08 JP JP2006515855A patent/JP5186636B2/en not_active Expired - Fee Related
- 2004-06-08 EP EP04739698.1A patent/EP1633894B1/en not_active Revoked
- 2004-06-08 RU RU2006101338/02A patent/RU2346061C2/en active
- 2004-06-08 CA CA2529837A patent/CA2529837C/en not_active Expired - Fee Related
- 2004-06-16 TW TW093117287A patent/TWI300443B/en not_active IP Right Cessation
- 2004-06-16 MY MYPI20042336A patent/MY136875A/en unknown
- 2004-08-06 UA UAA200600445A patent/UA81329C2/en unknown
-
2005
- 2005-12-06 ZA ZA200509876A patent/ZA200509876B/en unknown
- 2005-12-17 EG EGNA2005000837 patent/EG23893A/en active
Also Published As
| Publication number | Publication date |
|---|---|
| DE10327383C5 (en) | 2013-10-17 |
| DE10327383B4 (en) | 2010-10-14 |
| UA81329C2 (en) | 2007-12-25 |
| TW200502405A (en) | 2005-01-16 |
| WO2004111279A2 (en) | 2004-12-23 |
| MY136875A (en) | 2008-11-28 |
| ZA200509876B (en) | 2006-11-29 |
| US20070175548A1 (en) | 2007-08-02 |
| CN100381588C (en) | 2008-04-16 |
| CN1820086A (en) | 2006-08-16 |
| EG23893A (en) | 2007-12-13 |
| TWI300443B (en) | 2008-09-01 |
| RU2006101338A (en) | 2006-06-10 |
| KR20060057538A (en) | 2006-05-26 |
| EP1633894A2 (en) | 2006-03-15 |
| WO2004111279A3 (en) | 2005-05-06 |
| JP2006527790A (en) | 2006-12-07 |
| CA2529837A1 (en) | 2004-12-23 |
| EP1633894B1 (en) | 2017-04-26 |
| JP5186636B2 (en) | 2013-04-17 |
| RU2346061C2 (en) | 2009-02-10 |
| DE10327383A1 (en) | 2005-02-10 |
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