US20070175548A1 - Method and installation for the production of hot-rolled strip having a dual-phase structure - Google Patents
Method and installation for the production of hot-rolled strip having a dual-phase structure Download PDFInfo
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- US20070175548A1 US20070175548A1 US10/561,385 US56138504A US2007175548A1 US 20070175548 A1 US20070175548 A1 US 20070175548A1 US 56138504 A US56138504 A US 56138504A US 2007175548 A1 US2007175548 A1 US 2007175548A1
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- Prior art keywords
- cooling
- strip
- hot
- temperature
- ferrite
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- 238000000034 method Methods 0.000 title claims abstract description 12
- 238000009434 installation Methods 0.000 title claims description 19
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 238000001816 cooling Methods 0.000 claims abstract description 156
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 25
- 238000005096 rolling process Methods 0.000 claims abstract description 24
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 18
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 16
- 238000009749 continuous casting Methods 0.000 claims abstract description 16
- 239000010959 steel Substances 0.000 claims abstract description 16
- 230000009466 transformation Effects 0.000 claims abstract description 11
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 10
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 239000000126 substance Substances 0.000 claims abstract description 7
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 19
- 239000007921 spray Substances 0.000 claims description 13
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 235000013619 trace mineral Nutrition 0.000 claims description 3
- 239000011573 trace mineral Substances 0.000 claims description 3
- 230000015572 biosynthetic process Effects 0.000 description 4
- 238000009966 trimming Methods 0.000 description 4
- 238000010583 slow cooling Methods 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000000712 assembly Effects 0.000 description 1
- 238000000429 assembly Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 238000012544 monitoring process Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000010955 niobium Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 230000009897 systematic effect Effects 0.000 description 1
- 238000011144 upstream manufacturing Methods 0.000 description 1
Images
Classifications
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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
-
- 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
-
- 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
Abstract
Description
- 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 B1 describes a method for producing high-strength steel plate with a microstructure consisting of 75% ferrite, at least 10% 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 AR, 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 Ar3 point at a cooling rate of 20-150° C./s. -
EP 1 108 072 B1 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 characterizing features of
claim 1. 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, 0.3-1.2% 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 Tfinish, such that A3=100 K<Tfinish<A3=50 K, to a coiling strip temperature Tcoiling<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 in
claim 1, 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 70% 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.
-
FIG. 1 shows a time-temperature cooling curve of a hot-rolled strip. -
FIG. 2 shows a layout of a cooling line in a continuous casting and rolling installation with a 6-stand finishing train. -
FIG. 3 shows a layout of a cooling line in a continuous casting and rolling installation with a 7-stand finishing train. -
FIG. 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 acooling line 1. The hot-rolled strip, which had the following composition: 0.06% C, 0.1% Si, 1.2% Mn, 0.015% P, 0.06% S, 0.036% Al, 0.15% Cu, 0.054% 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 Tfinish 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 Tconst., 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 70% ferrite and less than 20% martensite, yielded a tensile strength of 620 MPa combined with a ratio of yield stress to tensile strength of 0.52. -
FIG. 2 shows an example of a layout of acooling line 1 of a conventional continuous casting and rolling installation. Thecooling line 1, through which the hot-rolled strip passes in direction ofconveyance 8, is located between thelast finishing stand 2 and thecoiler 5. A temperature-measuring point 6 for monitoring the temperature of the hot-rolledstrip 10 entering thecooling line 1 is located between thelast finishing stand 2 and the firstwater cooling unit 3 1. Thecooling line 1 shown inFIG. 2 comprises a total of eightcooling units 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
FIG. 2 is the typical layout of a cooling line for a 6-stand continuous casting and rolling installation, as is apparent from the gap betweencooling units cooling units cooling line 1′ has a layout of the type shown inFIG. 3 , which differs from the layout of thecooling line 1 inFIG. 2 only by the elimination of this structural gap between thecooling units FIG. 3 are the same as the reference numbers ofFIG. 2 . An exception to this is thefirst cooling unit 3 1′, whose upper spray bar, in contrast to the spray bar ofcooling unit 3 1 inFIG. 2 , is designed with the standard length of thecooling units 3 2 to 3 7. - 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 thestrip 10″. As a special feature, thecooling unit 3 1 inFIG. 2 is shortened by one spray bar on the upper side due to limited space. - In contrast to the
upstream cooling units 3 1-7, which have oneswitchable valve 7 per spray bar, the trimmingzone 4 has twovalves 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 units units -
- 1 cooling line
- 2 last finishing stand
- 3 1-7 water cooling units
- 4 water cooling unit (trimming zone)
- 5 coiler
- 6 temperature-measuring point
- 7 switchable valve
- 8 direction of conveyance
- 10 hot-rolled strip
- 10′ upper surface of the strip
- 10″ lower surface of the strip
- V1 cooling rate of the first cooling stage
- V2 cooling rate of the second cooling stage
- Tfinish strip temperature after the last finishing stand
- Tconst. strip temperature after the holding time
- Tcoiling strip temperature at the end of cooling (coil temperature)
Claims (4)
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE10327383A DE10327383C5 (en) | 2003-06-18 | 2003-06-18 | Plant for the production of hot strip with dual phase structure |
DE10327383.2 | 2003-06-18 | ||
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 (1)
Publication Number | Publication Date |
---|---|
US20070175548A1 true US20070175548A1 (en) | 2007-08-02 |
Family
ID=33546580
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10/561,385 Abandoned US20070175548A1 (en) | 2003-06-18 | 2004-06-08 | Method and installation for the production of hot-rolled strip having a dual-phase structure |
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) |
Cited By (3)
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US20140007992A1 (en) * | 2011-01-11 | 2014-01-09 | Thyssenkrupp Steel Europe Ag | Method for Producing a Hot-Rolled Flat Steel Product |
EP3050992A4 (en) * | 2013-09-26 | 2017-10-11 | Peking University Founder Group Co., Ltd | Production process for non-quenched and tempered steel |
US10220425B2 (en) | 2010-02-26 | 2019-03-05 | Primetals Technologies Germany Gmbh | Method for cooling sheet metal by means of a cooling section, cooling section and control device for a cooling section |
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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 |
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 |
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 ultrahigh-strength steel by direct cryogenic treatment after austenite and ferrite two-phase region isothermal heat treatment |
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 |
US3905216A (en) * | 1973-12-11 | 1975-09-16 | Gen Electric | Strip temperature control system |
US4159218A (en) * | 1978-08-07 | 1979-06-26 | National Steel Corporation | Method for producing a dual-phase ferrite-martensite steel strip |
US4561910A (en) * | 1981-02-20 | 1985-12-31 | Kawasaki Steel Corporation | Dual phase-structured hot rolled high-tensile strength steel sheet and a method of producing the same |
US4790889A (en) * | 1984-11-08 | 1988-12-13 | Thyssen Stahl Ag | Hot-rolled strip having a dual-phase structure |
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- 2004-06-08 JP JP2006515855A patent/JP5186636B2/en not_active Expired - Fee Related
- 2004-06-08 WO PCT/EP2004/006170 patent/WO2004111279A2/en active Application Filing
- 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 RU RU2006101338/02A patent/RU2346061C2/en active
- 2004-06-08 CN CNB2004800167574A patent/CN100381588C/en not_active Expired - Fee Related
- 2004-06-08 CA CA2529837A patent/CA2529837C/en not_active Expired - Fee Related
- 2004-06-16 MY MYPI20042336A patent/MY136875A/en unknown
- 2004-06-16 TW TW093117287A patent/TWI300443B/en not_active IP Right Cessation
- 2004-08-06 UA UAA200600445A patent/UA81329C2/en unknown
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- 2005-12-06 ZA ZA200509876A patent/ZA200509876B/en unknown
- 2005-12-17 EG EGNA2005000837 patent/EG23893A/en active
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Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10220425B2 (en) | 2010-02-26 | 2019-03-05 | Primetals Technologies Germany Gmbh | Method for cooling sheet metal by means of a cooling section, cooling section and control device for a cooling section |
US20140007992A1 (en) * | 2011-01-11 | 2014-01-09 | Thyssenkrupp Steel Europe Ag | Method for Producing a Hot-Rolled Flat Steel Product |
EP3050992A4 (en) * | 2013-09-26 | 2017-10-11 | Peking University Founder Group Co., Ltd | Production process for non-quenched and tempered steel |
Also Published As
Publication number | Publication date |
---|---|
CN100381588C (en) | 2008-04-16 |
MY136875A (en) | 2008-11-28 |
KR20060057538A (en) | 2006-05-26 |
CA2529837C (en) | 2012-08-21 |
EP1633894B1 (en) | 2017-04-26 |
WO2004111279A3 (en) | 2005-05-06 |
CA2529837A1 (en) | 2004-12-23 |
JP5186636B2 (en) | 2013-04-17 |
EP1633894A2 (en) | 2006-03-15 |
ZA200509876B (en) | 2006-11-29 |
CN1820086A (en) | 2006-08-16 |
EG23893A (en) | 2007-12-13 |
RU2006101338A (en) | 2006-06-10 |
DE10327383B4 (en) | 2010-10-14 |
UA81329C2 (en) | 2007-12-25 |
TWI300443B (en) | 2008-09-01 |
WO2004111279A2 (en) | 2004-12-23 |
DE10327383C5 (en) | 2013-10-17 |
DE10327383A1 (en) | 2005-02-10 |
RU2346061C2 (en) | 2009-02-10 |
TW200502405A (en) | 2005-01-16 |
JP2006527790A (en) | 2006-12-07 |
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