EP2398602B1 - Method for making a hot rolled thin cast strip product - Google Patents
Method for making a hot rolled thin cast strip product Download PDFInfo
- Publication number
- EP2398602B1 EP2398602B1 EP10743332.8A EP10743332A EP2398602B1 EP 2398602 B1 EP2398602 B1 EP 2398602B1 EP 10743332 A EP10743332 A EP 10743332A EP 2398602 B1 EP2398602 B1 EP 2398602B1
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- EP
- European Patent Office
- Prior art keywords
- hot rolled
- steel strip
- steel
- strip
- reduction
- Prior art date
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- 238000000034 method Methods 0.000 title description 4
- 229910000831 Steel Inorganic materials 0.000 claims description 82
- 239000010959 steel Substances 0.000 claims description 82
- 230000009467 reduction Effects 0.000 claims description 47
- 239000000203 mixture Substances 0.000 claims description 36
- 238000005266 casting Methods 0.000 claims description 33
- 238000005098 hot rolling Methods 0.000 claims description 26
- 239000011572 manganese Substances 0.000 claims description 15
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 14
- 229910052748 manganese Inorganic materials 0.000 claims description 14
- 238000004519 manufacturing process Methods 0.000 claims description 11
- 229910052751 metal Inorganic materials 0.000 claims description 11
- 239000002184 metal Substances 0.000 claims description 11
- 229910052799 carbon Inorganic materials 0.000 claims description 9
- 229910000859 α-Fe Inorganic materials 0.000 claims description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 8
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 8
- 229910052760 oxygen Inorganic materials 0.000 claims description 8
- 239000001301 oxygen Substances 0.000 claims description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 7
- 229910001563 bainite Inorganic materials 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- 239000010955 niobium Substances 0.000 claims description 5
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 239000011733 molybdenum Substances 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 4
- 229910052710 silicon Inorganic materials 0.000 claims description 4
- 239000010703 silicon Substances 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 4
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 3
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 239000011574 phosphorus Substances 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 38
- 229910052802 copper Inorganic materials 0.000 description 38
- 239000010949 copper Substances 0.000 description 38
- 239000011248 coating agent Substances 0.000 description 10
- 238000000576 coating method Methods 0.000 description 10
- 230000000694 effects Effects 0.000 description 10
- 229910000975 Carbon steel Inorganic materials 0.000 description 8
- 229910000617 Mangalloy Inorganic materials 0.000 description 8
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 8
- 238000001816 cooling Methods 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 7
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 6
- 238000010891 electric arc Methods 0.000 description 6
- QFGIVKNKFPCKAW-UHFFFAOYSA-N [Mn].[C] Chemical compound [Mn].[C] QFGIVKNKFPCKAW-UHFFFAOYSA-N 0.000 description 5
- 238000007792 addition Methods 0.000 description 4
- 239000010962 carbon steel Substances 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 3
- 229910001297 Zn alloy Inorganic materials 0.000 description 3
- 229910052681 coesite Inorganic materials 0.000 description 3
- 229910052906 cristobalite Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 239000000377 silicon dioxide Substances 0.000 description 3
- 229910052682 stishovite Inorganic materials 0.000 description 3
- 229910052905 tridymite Inorganic materials 0.000 description 3
- 239000011701 zinc Substances 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- 229910000611 Zinc aluminium Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 239000011651 chromium Substances 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 230000000704 physical effect Effects 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- HGOMLSWXJIICBL-UHFFFAOYSA-F dialuminum;zinc;tetrasulfate;tetracosahydrate Chemical compound O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.O.[Al+3].[Al+3].[Zn+2].[O-]S([O-])(=O)=O.[O-]S([O-])(=O)=O.[O-]S([O-])(=O)=O.[O-]S([O-])(=O)=O HGOMLSWXJIICBL-UHFFFAOYSA-F 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000005499 meniscus Effects 0.000 description 1
- 239000003595 mist Substances 0.000 description 1
- 230000000116 mitigating effect Effects 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
- -1 used in bar mills Chemical compound 0.000 description 1
Images
Classifications
-
- 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
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
-
- 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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
- C21D8/0215—Rapid solidification; Thin strip casting
-
- 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
- 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
- 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
- C21D2211/002—Bainite
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12785—Group IIB metal-base component
- Y10T428/12792—Zn-base component
- Y10T428/12799—Next to Fe-base component [e.g., galvanized]
Definitions
- molten metal is introduced between a pair of counter-rotated, internally cooled casting rolls so that metal shells solidify on the moving roll surfaces, and are brought together at the nip between them to produce a solidified strip product, delivered downwardly from the nip between the casting rolls.
- nip is used herein to refer to the general region at which the casting rolls are closest together.
- the molten metal is poured from a ladle through a metal delivery system comprising a tundish and a core nozzle located above the nip to form a casting pool of molten metal, supported on the casting surfaces of the rolls above the nip and extending along the length of the nip.
- This casting pool is usually confined between refractory side plates or dams held in sliding engagement with the end surfaces of the rolls so as to dam the two ends of the casting pool against outflow.
- the cast strip is typically directed to a hot rolling mill where the strip is hot reduced by 10% or more.
- plain low carbon steels have been continuously cast on a twin roll caster, including plain carbon-manganese steel.
- the physical properties of these plain carbon-manganese steels typically were affected by increasing hot rolling reduction. For example, yield strength and tensile strength decreased with increasing amount of hot rolling, while total elongation typically increased with increasing amount of hot rolling.
- the steel compositions had to be tailored for the amount of hot rolling reduction that was applied to provide desired mechanical properties. This resulted in inefficiency and operational problems as melt shops had to provide different molten compositions for different hot rolled strip thickness to provide desired hot rolled steel properties.
- the steel compositions may have included copper from scrap products incorporated into the molten steel.
- copper levels over about 0.2 weight % were generally avoided because of concerns over "hot shortness" during hot rolling reduction, which causes cracks or extremely roughened surfaces on the strip, sometimes referred to as "checking".
- copper levels were higher than 0.2% (such as in steels with improved atmospheric weathering resistance)
- expensive additions such as nickel had to be added to reduce the risk of hot shortness.
- Scrap with less than 0.15% copper is generally useful in electric arc furnaces for certain commercial methods of making steel, adding considerably to the cost of the steel sheet produced.
- Scrap grades with copper content up to 0.5% have been useful in bar mills serviced by electric arc furnaces, or in other processes at considerable expense by mixing with scrap of lower copper content to reduce the overall copper content of the scrap to less than 0.15%.
- Dainelli P et AL “Des Aciers De Construction Plis Facilement Soudables" Soudage et Techniques Connexes, Institut De Soudure ISSN 0246-0963 , which is considered to represent the closest prior art, discloses a method of making hot rolled steel strip having a composition consisting of, by weight, less than 0.25% carbon, greater than 0.01% and less than or equal to 0.15% phosphorus, between 1.0 and 2.0% manganese, between 0.05 and 0.50% silicon, less than 0.01% aluminium.
- the mechanical properties are preferably within 10% throughout the range from 15% to 35% reduction for yield strength, tensile strength and total elongation.
- the molten steel composition may have a free oxygen content between 30 and 60 ppm.
- the total oxygen content of the molten metal for the hot rolled steel strip may be between 70 ppm and 150 ppm.
- the molten steel may have a composition such that the manganese content of the composition of the hot rolled steel strip is between 0.9 and 1.3% by weight.
- the molten steel may have a composition such that the composition of the hot rolled steel strip may have in addition between 0.01% and 0.20% niobium by weight.
- the composition of molten steel may have a composition such that the composition of the hot rolled steel strip further comprises at least one element selected from the group consisting of molybdenum between about 0.05% and about 0.50%, vanadium between about 0.01% and about 0.20%, and a mixture thereof by weight.
- a hot rolled steel strip may additionally be provided with a coating of zinc or a zinc alloy or aluminum.
- the hot rolled steel strip may also have a yield strength of at least 440 MPa after hot rolling reductions of at least 35%.
- FIG. 1 illustrates successive parts of a strip caster for continuously casting steel strip.
- FIGS. 1 and 2 illustrate a twin roll caster 11 that continuously produces a cast steel strip 12, which passes in a transit path 10 across a guide table 13 to a pinch roll stand 14 having pinch rolls 14A.
- the strip passes into a hot rolling mill 16 having a pair of reduction rolls 16A and backing rolls 16B where the cast strip is hot rolled to reduce a desired thickness.
- the hot rolled strip passes onto a run-out table 17 where the strip may be cooled by convection and contact with water supplied via water jets 18 (or other suitable means) and by radiation.
- the rolled and cooled strip then passes through a pinch roll stand 20 comprising a pair of pinch rolls 20A and then to a coiler 19. Final cooling of the cast strip takes place after coiling.
- twin roll caster 11 comprises a main machine frame 21, which supports a pair of laterally positioned casting rolls 22 having casting surfaces 22A.
- Molten metal is supplied during a casting operation from a ladle (not shown) to a tundish 23, through a refractory shroud 24 to a distributor or moveable tundish 25, and then from the distributor 25 through a metal delivery nozzle 26 between the casting rolls 22 above the nip 27.
- the molten metal delivered between the casting rolls 22 forms a casting pool 30 above the nip.
- the casting pool 30 is restrained at the ends of the casting rolls by a pair of side closure dams or plates 28, which are pushed against the ends of the casting rolls by a pair of thrusters (not shown) including hydraulic cylinder units (not shown) connected to the side plate holders.
- the upper surface of casting pool 30 (generally referred to as the "meniscus" level) usually rises above the lower end of the delivery nozzle 26 so that the lower end of the delivery nozzle is immersed within the casting pool 30.
- Casting rolls 22 are internally water cooled so that shells solidify on the moving roller surfaces as they pass through the casting pool, and are brought together at the nip 27 between them to produce the cast strip 12, which is delivered downwardly from the nip between the casting rolls.
- the twin roll caster may be of the kind that is illustrated and described in some detail in U.S. Patent. Nos. 5,184,668 and 5,277,243 or U.S. Patent. No. 5,488,988 , or U.S. Patent Application 12/050,987 . Reference may be made to the patent specifications of those patents and patent application for appropriate construction details of a twin roll caster appropriate for use in an embodiment of the present invention.
- the steel composition of the present invention By employing rapid solidification rates with control of certain parameters in twin roll strip casting, the steel composition of the present invention generates liquid deoxidation products of MnO and SiO 2 in a fine and uniform distribution of globular inclusions.
- the MnO.SiO 2 inclusions present are also not significantly elongated by the in-line hot rolling process, due to limited hot reduction.
- the inclusion/particle populations are tailored to stimulate nucleation of acicular ferrite.
- the MnO.SiO 2 inclusions may be about 10 ⁇ m down to very fine particles of less than 0.1 ⁇ m, and a majority being between about 0.5 ⁇ m and 5 ⁇ m.
- the larger 0.5-10 ⁇ m size non-metallic inclusions are provided for nucleating acicular ferrite, and may include a mixture of inclusions, for example including MnS, and CuS.
- the austenite grain size is significantly larger than the austenite grain size produced in conventional hot rolled strip steel.
- the coarse austenite grain size in conjunction with the population of tailored inclusion/particles, assists with the nucleation of acicular ferrite and bainite.
- the in-line hot rolling mill 16 is typically used for reductions of 10 to 50%.
- the cooling may include water cooling section and air mist cooling to control cooling rates of austenite transformation to achieve desired microstructure and material properties at a temperature between 300 and 700°C.
- the coiling temperature may be between about 450 and 550°C.
- the resulting microstructure comprises a majority acicular ferrite and bainite.
- the effect of hot reduction on yield strength, tensile strength, and total elongation in the present elevated copper and elevated manganese steels results in a steel properties where the tensile strength, yield strength and total elongation are relatively stable with different levels of hot reduction.
- a coiling temperature below 550°C may be used in conjunction with a high degree of hot rolling to mitigate the hot reduction affect on the mechanical properties.
- Hot reductions larger than about 15% can induce recrystallization of austenite, which reduces the grain size and volume fraction of acicular ferrite and bainite.
- the molten composition of Steels J and L in TABLE 1 had a free oxygen content between 41 and 54 ppm and the compositions of Steel J and L had a greater than 0.01% and less than or equal to 0.15% phosphorus.
- a typical composition for plain carbon-manganese steel such as the Base composition in TABLE 1, includes a manganese content of about 0.60% - 0.90% by weight.
- a steel composition having a substantially elevated manganese content (steel L in TABLE 1) to increase the hardenability of the steel.
- the elevated manganese content provides desired strength levels due to microstructural hardening.
- manganese in solid solution acted to suppress static recrystallization of the deformed austenite after hot rolling mitigating the affect of hot reduction on mechanical properties. This suppression is made possible by the short time scale and minimal hot reduction relative to conventional slab-based production.
- the present elevated manganese steel composition is relatively stable with the degree of hot rolled reduction for hot reductions up to at least 35%.
- the yield strength for 1.28% manganese steel is less influenced by hot rolling reduction than a plain 0.8% carbon-manganese grade. Additionally, the yield strength of the 1.28% manganese was significantly higher than that of the base 0.8% manganese steel, exceeding 440 MPa for hot rolling reductions greater than 35%.
- the steel strip After hot rolling, the steel strip is cooled to a coiling temperature between about 300°C and 700°C to provide a majority of the microstructure comprising bainite and acicular ferrite. Alternatively, the steel strip is cooled to a coiling temperature between about 450°C and 550°C to provide a majority of the microstructure comprising bainite and acicular ferrite.
- the mechanical properties at 15% and 35% reduction are within 10% for yield strength, tensile strength and total elongation of the hot rolled strip. Alternatively, mechanical properties may be within 10% throughout the range from 15% to 35% reduction for yield strength, tensile strength and total elongation of the hot rolled strip.
- the composition according to the invention includes, by weight, less than 0.25% carbon, between 0.05 and 0.50% silicon, and less than 0.01% aluminum.
- the manganese content may be between about 1.0% and 1.3% by weight.
- composition of the elevated manganese steel may include at least one element selected from the group consisting of niobium between about 0.01% and 0.2%, molybdenum between about 0.05% and about 0.50%, vanadium between about 0.01% and about 0.20%, and a mixture thereof.
- the hot rolled steel strip also may be hot dip coated to provide a coating of zinc or a zinc alloy or aluminum.
- the desired microstructural hardening to reduce the effect of the hot rolling reduction on the mechanical properties can be provided by addition of between 0.20 and 0.60% copper and the manganese levels kept the same as the minimum described above or reduced to as low as 0.08%, with less than 0.03% tin and less than 0.20% nickel by weight.
- This elevated copper steel enables use of steel scrap that is higher in copper, such as used in bar mills, to be used in the steel making without hot shortness.
- a number of trial heats were cast having copper levels in the range of 0.2% to 0.4%, and one trial heat of about 0.6% copper was cast without incurring hot shortness while also avoiding special practices or alloy additions.
- the composition with copper may include, by weight, less than 0.25% carbon, between 0.2 and 2.0% manganese, between 0.05 and 0.50% silicon, less than 0.01% aluminum less than 0.03% tin, less than 0.10% nickel, and between 0.20 and 0.60% copper.
- the copper content may be between about 0.2% and 0.5% by weight, and alternatively, may be between about 0.3% and 0.4%.
- the molten steel cast has a free oxygen content between 20 and 75 ppm and the free oxygen content may be between 30 and 60 ppm. Again, the total oxygen levels were between 70 ppm and 150 ppm.
- the hot rolled steel strip may have, in addition, a chromium content between about 0.4% and 0.75% by weight. Alternatively, the chromium content may be between about 0.4% and 0.5%.
- the present steel with elevated copper may provide physical properties similar to plain carbon-manganese steel with low copper content.
- the present steel composition having elevated copper levels can be made in electric arc furnaces with high copper scrap, as discussed above, at a considerable cost savings over low copper scrap.
- the present elevated copper steel is hot dip coated with one or both of a zinc coating or a zinc alloy coating or an aluminum coating, such as a galvanized coating, Galvalume® and Zincalum® coating, aluminized coating or other coating.
- a zinc coating or a zinc alloy coating or an aluminum coating such as a galvanized coating, Galvalume® and Zincalum® coating, aluminized coating or other coating.
- the microstructure of the present hot dipped elevated copper steel was not significantly altered as the strip temperatures remained well below the A c1 temperature of the steel. Consequently, the mechanical properties of uncoated elevated copper steel in the hot rolled condition are similar to the mechanical properties after coating on a continuous hot dip galvanizing line.
- the high copper composition may include at least one element selected from the group consisting of niobium between about 0.01% and 0.2%, molybdenum between about 0.05% and about 0.50%, vanadium between about 0.01% and about 0.20%, and a mixture thereof.
- carbon levels of about 0.20% and greater may also be used for applications where microalloying is not desired. Additionally, higher carbon levels, in the range of 0.30 - 0.50%, may be used in certain applications for material in the thickness range of 1.0 - 1.5 mm. In the past, these elevated carbon steels required multiple annealing and cold rolling steps to achieve this thickness.
- the composition of a 0.19% carbon steel is given in TABLE 1 (steel J) and the mechanical properties are presented in FIG. 4 as a function of the hot rolling reduction applied.
- the strength levels of the present 0.19% carbon steel are higher than current plain low carbon steels.
- the yield strength is over 380 MPa over the full range of hot reductions applied, while being processed with conventional coiling temperatures. This is in contrast to low carbon steels (0.02-0.05% C), where lower coiling temperatures and limited hot reductions are applied to provide yield strengths over 380 MPa.
- FIGS. 5 and 6 Additional samples of the present steel were prepared with manganese between about 0.88% and 1.1% and carbon amount between about 0.02% and 0.04%, shown in FIGS. 5 and 6 . As shown in FIG. 5 , tensile strength, yield strength and total elongation are relatively stable over different levels of manganese amount between 0.88% and 1.1%
- the effect of hot reduction on yield strength, tensile strength, and total elongation in the present steels results in a steel properties where the tensile strength, yield strength and total elongation are relatively stable with different levels of hot reduction, as shown in FIG. 6 .
- the present steel is relatively stable with the degree of hot rolled reduction for reductions up to at least 45%.
- the hot rolled cast strip to provide after cooling at a temperature between 300 and 700°C, alternatively between about 450 and 550°C, a microstructure comprising a majority bainite and acicular ferrite and having properties such that mechanical properties at 10% and 35% reduction are within 10% for yield strength, tensile strength and total elongation.
- mechanical properties are within 10% throughout the range from 10% to 35% reduction for yield strength, tensile strength and total elongation.
- mechanical properties at 15% and 35% reduction are within 10% for yield strength, tensile strength and total elongation.
- mechanical properties are within 10% throughout the range from 15% to 35% reduction for yield strength, tensile strength and total elongation.
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- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Continuous Casting (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
- Coating With Molten Metal (AREA)
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP18190655.3A EP3431201A3 (en) | 2009-02-20 | 2010-02-20 | A hot rolled thin cast strip product and method for making the same |
PL10743332T PL2398602T3 (pl) | 2009-02-20 | 2010-02-20 | Sposób wytwarzania produktu walcowanej na gorąco cienkiej odlewanej taśmy |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US15423309P | 2009-02-20 | 2009-02-20 | |
PCT/AU2010/000189 WO2010094076A1 (en) | 2009-02-20 | 2010-02-20 | A hot rolled thin cast strip product and method for making the same |
Related Child Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP18190655.3A Division EP3431201A3 (en) | 2009-02-20 | 2010-02-20 | A hot rolled thin cast strip product and method for making the same |
EP18190655.3A Division-Into EP3431201A3 (en) | 2009-02-20 | 2010-02-20 | A hot rolled thin cast strip product and method for making the same |
Publications (3)
Publication Number | Publication Date |
---|---|
EP2398602A1 EP2398602A1 (en) | 2011-12-28 |
EP2398602A4 EP2398602A4 (en) | 2014-09-24 |
EP2398602B1 true EP2398602B1 (en) | 2018-10-31 |
Family
ID=42631240
Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP18190655.3A Withdrawn EP3431201A3 (en) | 2009-02-20 | 2010-02-20 | A hot rolled thin cast strip product and method for making the same |
EP10743332.8A Active EP2398602B1 (en) | 2009-02-20 | 2010-02-20 | Method for making a hot rolled thin cast strip product |
Family Applications Before (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP18190655.3A Withdrawn EP3431201A3 (en) | 2009-02-20 | 2010-02-20 | A hot rolled thin cast strip product and method for making the same |
Country Status (10)
Country | Link |
---|---|
US (1) | US20100215981A1 (pl) |
EP (2) | EP3431201A3 (pl) |
JP (1) | JP5509222B2 (pl) |
KR (1) | KR101715086B1 (pl) |
CN (2) | CN102325608B (pl) |
AU (2) | AU2010215077B2 (pl) |
MY (1) | MY173389A (pl) |
PL (1) | PL2398602T3 (pl) |
RU (1) | RU2532794C2 (pl) |
WO (1) | WO2010094076A1 (pl) |
Families Citing this family (7)
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DE102010010536B4 (de) * | 2010-03-05 | 2017-01-05 | Theodor Stuth | Verfahren zur Herstellung von Nickelband |
US20140261905A1 (en) * | 2013-03-15 | 2014-09-18 | Castrip, Llc | Method of thin strip casting |
CN104959561B (zh) * | 2015-07-09 | 2017-12-01 | 东北大学 | 一种提高双辊连铸低碳微合金钢针状铁素体含量的方法 |
CN112522629B (zh) * | 2019-09-19 | 2022-06-24 | 宝山钢铁股份有限公司 | 一种Nb微合金化高强高扩孔钢及其生产方法 |
CN112522588B (zh) * | 2019-09-19 | 2022-06-28 | 宝山钢铁股份有限公司 | 一种薄带连铸生产高强薄规格花纹钢板/带的方法 |
WO2023062643A1 (en) * | 2021-10-13 | 2023-04-20 | Stephen Fernandes | Slip planes in metal and mechanical strength in materials |
CN115478203A (zh) * | 2022-09-27 | 2022-12-16 | 张家港中美超薄带科技有限公司 | 一种基于薄带铸轧生产热轧薄带钢的方法及超高强零件 |
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- 2010-02-20 RU RU2011138463/02A patent/RU2532794C2/ru not_active IP Right Cessation
- 2010-02-20 KR KR1020117018562A patent/KR101715086B1/ko active IP Right Grant
- 2010-02-20 AU AU2010215077A patent/AU2010215077B2/en not_active Ceased
- 2010-02-20 MY MYPI2011700114A patent/MY173389A/en unknown
- 2010-02-20 CN CN201080008606.XA patent/CN102325608B/zh active Active
- 2010-02-20 JP JP2011550383A patent/JP5509222B2/ja active Active
- 2010-02-20 CN CN201510522890.7A patent/CN105215299A/zh active Pending
- 2010-02-20 EP EP18190655.3A patent/EP3431201A3/en not_active Withdrawn
- 2010-02-20 PL PL10743332T patent/PL2398602T3/pl unknown
- 2010-02-20 EP EP10743332.8A patent/EP2398602B1/en active Active
- 2010-02-20 WO PCT/AU2010/000189 patent/WO2010094076A1/en active Application Filing
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2017
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Also Published As
Publication number | Publication date |
---|---|
JP2012518539A (ja) | 2012-08-16 |
EP3431201A2 (en) | 2019-01-23 |
JP5509222B2 (ja) | 2014-06-04 |
AU2017202997B2 (en) | 2019-01-17 |
CN102325608A (zh) | 2012-01-18 |
AU2010215077B2 (en) | 2017-05-25 |
AU2017202997A1 (en) | 2017-06-01 |
MY173389A (en) | 2020-01-22 |
WO2010094076A1 (en) | 2010-08-26 |
EP2398602A4 (en) | 2014-09-24 |
KR101715086B1 (ko) | 2017-03-10 |
PL2398602T3 (pl) | 2019-04-30 |
KR20110117142A (ko) | 2011-10-26 |
EP2398602A1 (en) | 2011-12-28 |
CN105215299A (zh) | 2016-01-06 |
US20100215981A1 (en) | 2010-08-26 |
RU2532794C2 (ru) | 2014-11-10 |
AU2010215077A1 (en) | 2011-07-28 |
RU2011138463A (ru) | 2013-03-27 |
CN102325608B (zh) | 2015-11-25 |
EP3431201A3 (en) | 2019-03-13 |
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