WO2008137898A1 - Produit en bande, moulé, mince contenant des ajouts de microalliage, et son procédé de fabrication - Google Patents

Produit en bande, moulé, mince contenant des ajouts de microalliage, et son procédé de fabrication Download PDF

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Publication number
WO2008137898A1
WO2008137898A1 PCT/US2008/062776 US2008062776W WO2008137898A1 WO 2008137898 A1 WO2008137898 A1 WO 2008137898A1 US 2008062776 W US2008062776 W US 2008062776W WO 2008137898 A1 WO2008137898 A1 WO 2008137898A1
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WO
WIPO (PCT)
Prior art keywords
steel
steel product
strip
niobium
less
Prior art date
Application number
PCT/US2008/062776
Other languages
English (en)
Inventor
James Geoffery Williams
Harold Roland Kaul
Daniel Geoffrey Edelman
Christopher Ronald Killmore
Original Assignee
Nucor Corporation
Bluescope Steel Limited
Ihi Corporation
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from US11/744,881 external-priority patent/US20070212249A1/en
Application filed by Nucor Corporation, Bluescope Steel Limited, Ihi Corporation filed Critical Nucor Corporation
Priority to PL08747712T priority Critical patent/PL2152451T3/pl
Priority to JP2010507600A priority patent/JP5385899B2/ja
Priority to AU2008247365A priority patent/AU2008247365B2/en
Priority to EP08747712.1A priority patent/EP2152451B1/fr
Priority to CN200880023167A priority patent/CN101765470A/zh
Priority to NZ581424A priority patent/NZ581424A/en
Priority to BRPI0811554A priority patent/BRPI0811554B1/pt
Priority to CA2686495A priority patent/CA2686495C/fr
Publication of WO2008137898A1 publication Critical patent/WO2008137898A1/fr

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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
    • 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
    • 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
    • B22D11/124—Accessories for subsequent treating or working cast stock in situ for cooling
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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

Definitions

  • This invention relates to making of high strength thin cast strip, and the method for making such cast strip by a twin roll caster.
  • 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.
  • the term "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 comprised of 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.
  • V, Ti or Mo elements to produce high strength thin strip could not be commercially produced economically because of the high alloying costs, relative inefficiency of element additions, difficulties with high rolling loads in hot rolling and cold rolling, and the high recrystallization annealing temperatures required.
  • a steel product comprising, by weight, less than 0.25% carbon, between 0.20 and 2.0% manganese, between 0.05 and 0.50% silicon, less than 0.01% aluminum, and niobium between about 0.01% and about 0.20% and having a majority of the microstructure comprised of bainite and acicular ferrite and having more than 70% niobium in solid solution.
  • the niobium may be less than 0.1%.
  • the steel product may further comprise 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.
  • the steel product may have a yield strength of at least 340 MPa, and may have a tensile strength of at least 410 MPa.
  • the steel product may have a yield strength of at least 485 MPa and a tensile strength of at least of at least 520 MPa.
  • the steel product has a total elongation of at least 6%. Alternately, the total elongation may be at least 10%.
  • the steel product may be a thin cast steel strip.
  • the thin cast steel strip may have fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers
  • the thin cast steel strip may have a thickness of less than 2.5 mm. Alternately, the thin cast steel strip may have a thickness of less than 2.0 mm. In yet another alternative, the thin cast steel strip may have a thickness in the range from about 0.5 mm to about 2 mm.
  • the hot rolled steel product of less than 3 millimeters thickness is also disclosed comprised, by weight, of less than 0.25% carbon, between 0.20 and 2.0% manganese, between 0.05% and 0.50% silicon, less than 0.01% aluminum, and niobium between about 0.01% and about 0.20%, and have a majority of the microstructure comprised of bainite and acicular ferrite and capable of providing a yield strength of at least 410 MPa with a reduction of between 20% and 40%.
  • the steel product may have a yield strength of at least 485 MPa and a tensile strength of at least of at least 520 MPa. Alternately, the niobium may be less than 0.1%.
  • the hot rolled steel product may have fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers.
  • the hot rolled steel product has a total elongation of at least 6%. Alternately, the total elongation may be at least 10%.
  • the hot rolled steel product may have a thickness of less than 2.5 mm. Alternately, the hot rolled steel product may have a thickness of less than 2.0 mm. In yet another alternative, the hot rolled steel product may have a thickness in the range from about 0.5 mm to about 2 mm.
  • a coiled steel product comprised, by weight, of less than
  • niobium between about 0.01% and about 0.20%, vanadium between about 0.01% and about 0.20%, and a mixture thereof, and having more than 70% niobium and/or vanadium in solid solution after coiling and cooling.
  • the niobium may be less than 0.1%.
  • the coiled steel product may have fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers.
  • the coiled steel product may have a yield strength of at least 340 MPa, and may have a tensile strength of at least 410 MPa.
  • the coiled steel product has a thickness of less than 3.0 mm.
  • the steel product may have a yield strength of at least 485 MPa and a tensile strength of at least of at least 520 MPa.
  • the coiled steel product has a thickness of less than 2.5 mm.
  • the coiled steel product may have a thickness of less than 2.0 mm. In yet another alternative, the coiled steel product may have a thickness in the range from about 0.5 mm to about 2 mm.
  • the coiled steel product has a total elongation of at least 6%. Alternately, the total elongation may be at least 10%.
  • An age hardened steel product comprising, by weight, less than 0.25% carbon, between 0.20 and 2.0% manganese, between 0.05 and 0.50% silicon, less than 0.01% aluminum, at least one element from the group consisting of niobium between about 0.01% and about 0.20%, vanadium between about 0.01% and about 0.20%, and a mixture thereof, and having a majority of the microstructure comprised of bainite and acicular ferrite and having an increase in elongation and an increase in yield strength after age hardening. Alternately, the niobium may be less than 0.1%.
  • the age hardened steel product may comprise, in addition, fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers.
  • the steel product may have a yield strength of at least 340 MPa, or at least
  • the steel product may have a tensile strength of at least 410 MPa, or at least 450 MPa, or at least 500 MPa, or at least 550 MPa, or at least 600 MPa, or at least 650 MPa, or at least 700 MPa, as desired.
  • the age hardened steel product has a thickness of less than 3.0 mm. Alternately, the age hardened steel product has a thickness of less than 2.5 mm. Alternately, the age hardened steel product may have a thickness of less than 2.0 mm.
  • the age hardened steel product may have a thickness in the range from about 0.5 mm to about 2 mm.
  • the age hardened steel product has a total elongation of at least 6%. Alternately, the total elongation may be at least 10%.
  • a steel product comprising, by weight, less than 0.25% carbon, between 0.20 and 2.0% manganese, between 0.05 and 0.50% silicon, less than 0.01% aluminum, and at least one element selected from the group consisting of niobium between about 0.01% and about 0.20% and vanadium between about 0.01% and about 0.20%, and having a majority of the microstructure comprised of bainite and acicular ferrite and comprising fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers.
  • the niobium may be less than 0.1%.
  • the steel product may comprise molybdenum between about 0.05% and 0.50%.
  • the steel product may have a yield strength of at least 340 MPa, and may have a tensile strength of at least 410 MPa.
  • the steel product may have a yield strength of at least 485 MPa and a tensile strength of at least of at least 520 MPa.
  • the steel product has a total elongation of at least 6%. Alternately, the total elongation may be at least 10%.
  • An age hardened steel product comprising, by weight, less than 0.25% carbon, between 0.20 and 2.0% manganese, between 0.05 and 0.50% silicon, less than 0.01% aluminum, and niobium between about 0.01% and about 0.20%, and having a majority of the microstructure comprised of bainite and acicular ferrite and having niobium carbonitride particles with an average particle size of less than 10 nanometers.
  • Carbonitride particles in the present specification and appended claims, includes carbides, nitrides, carbonitrides, and combinations thereof. Alternately, the niobium may be less than 0.1%.
  • the age hardened steel product may have substantially no niobium carbonitride particles greater than 50 nanometers.
  • the age hardened steel product may have a yield strength of at least 340 MPa, and may have a tensile strength of at least 410 MPa.
  • the age hardened steel product has a total elongation of at least 6%. Alternately, the total elongation may be at least 10%.
  • a method for preparing coiled thin cast steel strip comprising the steps of: assembling internally a cooled roll caster having laterally positioned casting rolls forming a nip between them, and forming a casting pool of molten steel supported on the casting rolls above the nip and confined adjacent the ends of the casting rolls by side dams, counter rotating the casting rolls to solidify metal shells on the casting rolls as the casting rolls move through the casting pool, and forming from the metal shells downwardly through the nip between the casting rolls a steel strip, and cooling the steel strip at a rate of at least 10 0 C per second to provide a composition comprising by weight, less than 0.25% carbon, between 0.20 and 2.0% manganese, between 0.05 and 0.50% silicon, less than 0.01% aluminum, and at least one element selected from the group consisting of niobium between about 0.01% and about 0.20%, vanadium between about 0.01% and about 0.20%, and a mixture thereof, and having a majority of
  • the method may provide in the steel strip as coiled fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers. Further, the method may comprise the steps of hot rolling the steel strip, and coiling the hot rolled steel strip at a temperature between about 450 and 700 0 C. Alternately, the coiling of the hot rolled steel strip may be at a temperature less than 650 0 C.
  • the method may further comprise the step of age hardening the steel strip to increase the tensile strength at a temperature of at least 550 °C.
  • the age hardening may occur at a temperature between 625 0 C and 800 0 C.
  • the age hardening may occur at a temperature between 650 0 C and 750 0 C.
  • a method of preparing a thin cast steel strip comprised the steps of: assembling internally a cooled roll caster having laterally positioned casting rolls forming a nip between them, and forming a casting pool of molten steel supported on the casting rolls above the nip and confined adjacent the ends of the casting rolls by side dams, counter rotating the casting rolls to solidify metal shells on the casting rolls as the casting rolls move through the casting pool, and forming steel strip from the metal shells cast downwardly through the nip between the casting rolls, and cooling the steel strip at a rate of at least 10 0 C per second to provide a composition comprising by weight, less than 0.25% carbon, less than 0.01% aluminum, and at least one element from the group consisting of niobium between about 0.01% and about 0.20%, vanadium between about 0.01% and about 0.20%, and a mixture thereof, and having a majority of the microstructure comprised of bainite and acicular ferrite and having more than
  • the method may further comprise the step of age hardening the steel strip to increase the tensile strength.
  • the age hardening may occur at a temperature between 650 0 C and 750 0 C.
  • the method may provide the age hardened steel strip having niobium carbonitride particles with an average particle size of less than 10 nanometers.
  • the age hardened steel strip has substantially no niobium carbonitride particles greater than 50 nanometers.
  • the method may provide in the steel strip as coiled fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers. Further, the method may comprise the steps of hot rolling the steel strip, and coiling the hot rolled steel strip at a temperature less than 700 0 C. Alternately, the coiling of the hot rolled steel strip may be at a temperature less than 650 0 C.
  • the method may provide in the steel strip as coiled fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers. Further, the method may provide the age hardened steel strip having niobium carbonitride particles with an average particle size of less than 10 nanometers. Alternately, the age hardened steel strip has substantially no niobium carbonitride particles greater than 50 nanometers.
  • the method may comprise the steps of hot rolling the steel strip, and coiling the hot rolled steel strip at a temperature less than 750 0 C.
  • the coiling of the hot rolled steel strip may be at a temperature less than 700 0 C.
  • FIG. 1 illustrates a strip casting installation incorporating an in-line hot rolling mill and coiler
  • FIG. 2 illustrates details of the twin roll strip caster
  • FIG. 3 illustrates the effect of coiling temperature on strip yield strength with and without niobium or vanadium additions
  • FIG. 4a is an optical micrograph of a niobium steel strip
  • FIG. 4b is an optical micrograph of a standard UCS SS Grade 380 steel strip
  • FIG. 5 is graph showing the effect of post coil age hardening on yield strength of the present steel strip
  • FIG. 6 is a graph showing the effect of post coiling simulated age hardening cycle on yield and tensile strength of the present steel strip
  • FIG. 7 is a graph showing the effect of hot rolling reduction on the yield strength.
  • FIG. 8 is a graph showing the effect of yield strength on elongation
  • FIG. 9 is a graph showing the effect of niobium amount on the yield strength at low levels of niobium
  • FIG. 10a shows micrographs of the microstructure of a first sample of 0.065% niobium steel after hot rolling
  • FIG. 10b shows micrographs of the microstructure of a second sample of
  • FIG. 11 is a graph showing the effect of niobium amount on the yield strength
  • FIG. 12 is a graph showing the effect of coiling temperature on the yield strength
  • FIG. 13 is a graph showing the effect of coiling temperature on the yield strength at low niobium levels
  • FIG. 14 is a graph showing the effect of heat treating conditions on the yield strength
  • FIG. 15 is a graph showing the effect of age hardening heat treating temperature on the yield strength of 0.026% niobium steel
  • FIG. 16 is a graph showing the effect of peak aging temperature on the yield strength of 0.065% niobium steel
  • FIG. 17 is a graph showing the effect of peak aging temperature and hold time on the yield strength of 0.065% niobium steel
  • FIG. 18 is a graph showing the effect of peak aging temperature and hold time on the yield strength for 0.084% niobium steel
  • FIG. 19 is a graph showing the effect of yield strength on elongation before and after age hardening
  • FIG. 20 is a graph showing heat treating results continuous annealing
  • FIG. 21 is a graph showing age hardened condition
  • FIG. 22 is a graph showing the effect of temperature and time on hardness
  • FIG. 23 is a graph showing the effect of heat treating on the yield strength for the present vanadium steel.
  • FIG. 24 is a graph showing the effect of hot rolling reduction on the yield strength for the present vanadium steel.
  • FIG. 1 illustrates successive parts of 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 is then passes through a pinch roll stand 20 comprising a pair of pinch rolls 2OA 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 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. Reference may be made to those patents for appropriate construction details of a twin roll caster appropriate for use in an embodiment of the present invention.
  • a high strength thin cast strip product can be produced using the twin roll caster that overcomes the shortcomings of conventional light gauge steel products and produces a high strength, light gauge, steel strip product.
  • the invention utilizes the elements including niobium (Nb), vanadium (V), titanium (Ti), or molybdenum (Mo), or a combination thereof.
  • Microalloying elements in steel are commonly taken to refer to the elements titanium niobium, and vanadium. These elements were usually added in the past in levels below 0.1%, but in some cases levels as high as 0.2%. These elements are capable of exerting strong effects on the steel microstructure and properties via a combination of hardenability, grain refining and strengthening effects (in the past as carbonitride formers). Molybdenum has not normally been regarded as a microalloying element since on its own it is a relatively weak carbonitride former, but may be effective in the present circumstances and may form complex carbonitride particles along with niobium and vanadium. Carbonitride formation is inhibited in the hot rolled strip with these elements as explained below.
  • the high strength thin cast strip product combines several attributes to achieve a high strength light gauge cast strip product by microalloying with these elements.
  • Strip thicknesses may be less than 3 mm, less than 2.5 mm, or less than 2.0 mm, and may be in a range of 0.5 mm to 2.0 mm.
  • the cast strip is produced by hot rolling without the need for cold rolling to further reduce the strip to the desired thickness.
  • the high strength thin cast strip product overlaps both the light gauge hot rolled thickness ranges and the cold rolled thickness ranges desired.
  • the strip may be cooled at a rate of 10 0 C per second and above, and still form a microstructure that is a majority and typically predominantly bainite and acicular ferrite.
  • the present high strength thin cast steel strip product comprising, by weight, less than 0.25% carbon, between 0.20 and 2.00% manganese, between 0.05 and 0.50% silicon, less than 0.06% aluminum, and at least one element selected from the group consisting of titanium between about 0.01% and about 0.20%, niobium between about 0.01% and about 0.20%, molybdenum between about 0.05% and about 0.50%, and vanadium between about 0.01% and about 0.20%, and having a microstructure comprising a majority bainite.
  • the steel product may further comprising fine oxide particles of silicon and iron distributed through the steel microstructure having an average particle size less than 50 nanometers.
  • the steel product may further comprise a more even distribution of microalloys through the microstructure than previously produced with conventional slab cast product.
  • the high strength thin cast steel strip product may comprise, by weight, less than 0.25% carbon, between 0.20 and 2.0% manganese, between 0.05 and 0.50% silicon, less than 0.01% aluminum, and niobium between about 0.01% and about 0.20%, and having a majority of the microstructure comprising bainite and acicular ferrite and having more than 70% soluble niobium.
  • a coiled steel product may comprise, by weight, less than
  • the coiled high strength thin cast steel strip product may have more than 70% soluble niobium and vanadium, as selected, particularly after hot rolling reduction and subsequent coiling and before age hardening.
  • the microstructure may be a mixture of bainite and acicular ferrite.
  • the microstructure of the hot rolled and subsequently coiled and cooled steel may comprise bainite and acicular ferrite with more than 80% niobium and/or vanadium remaining in solid solution, and alternately may have more than 90% remaining in solid solution.
  • the steel product may have a total elongation greater than 6% or greater than 10%.
  • the steel product may have a yield strength of at least 340 MPa (about 49 ksi) or a tensile strength of at least 410 MPa, or both, exhibiting satisfactory ductility.
  • the relationship between yield strength and total elongation in the hot rolled product is shown in FIG. 8.
  • the hot rolled steel strip may be coiled at a temperature in the range from about 500-700 0 C.
  • the thin cast steel strip may also be further processed by age hardening the steel strip to increase the tensile strength at a temperature of at least 550 0 C.
  • the age hardening may occur at a temperature between 550 0 C and 800 0 C, or between 625 0 C and 750 0 C, or between 675 0 C and 750 0 C.
  • Conventional furnaces of continuous galvanizing or annealing lines are thus capable of providing the age hardening temperatures needed to harden the microalloyed cast strip product.
  • a steel composition was prepared by making a steel composition of a 0.026% niobium, 0.04% by weight carbon, 0.85% by weight manganese, 0.25% by weight silicon that has been cast by a thin cast strip process.
  • the strip was cast at 1.7 mm thick and inline hot rolled to a range of strip thickness from 1.5 mm to 1.1 mm using a twin roll caster as illustrated in FIGS. 1 and 2.
  • the strip was coiled at coiling temperatures of 590- 620 0 C (1094-1148 0 F).
  • the yield and tensile strength levels achieved in the present cast strip are compared to the yield and tensile strength levels achievable in the base, non- microalloyed, cast strip steel composition over a range of coiling temperatures. It can be seen that the niobium steel strip achieved yield strengths in the range of 420-440 MPa (about 61-64 ksi) and tensile strengths of about 510 MPa (about 74 ksi).
  • the present cast strip product is compared to C-Mn-Si base steel compositions processed with the same coiling temperature as the microalloyed steel, with the niobium steel producing substantially higher strength levels.
  • the compared base steel strip had to be coiled at very low temperatures to approach comparable strength levels to the cast niobium steel product.
  • the cast niobium steel product did not need to be coiled at low coiling temperatures to achieve its strengthening potential with the hot rolling.
  • the yield and tensile strength levels for the cast niobium steel was not significantly affected by the degree of inline hot rolling with a reduction of at least 19% to 37% as shown in FIG. 7.
  • FIG. 9 The hardenability of the present steels is shown in FIG. 9. As shown in FIG. 9, a niobium level of as little as 0.007% was effective in increasing the strength of the final strip, and yield strength levels of over 380 MPa were achieved with niobium levels greater than about 0.01%. Note that niobium levels less than about 0.005% may be considered residual. Thus even very small additions of microalloying elements can be effective in substantial strengthening. [0081] The high strengths were achieved by utilizing the niobium microalloying addition to increase the hardenability of the steel through the suppression of the formation of proeutectic ferrite. FIG.
  • FIG. 4b shows that proeutectic ferrite formed along the prior austenite grain boundaries (allotriomorphic ferrite) in the base steel, but it was not present in the niobium steel shown in FIG. 4a.
  • the hardenability effects of the niobium addition suppressed the ferrite transformation, hence enabling the stronger bainitic and acicular ferrite microstructure to be produced while using conventional cooling rates during cooling and higher coiling temperatures.
  • the final microstructure of the present niobium steels comprises mostly a combination of bainite and acicular ferrite.
  • the base steel shown in FIG. 4b was cooled to a relatively low coiling temperature, less than 500 0 C, a cooling condition known to suppress ferrite formation at the austenite grain boundaries.
  • the austenite grain size was measured at each thickness in the 0.026 Nb steel.
  • the base steel tended to be fully recrystallized above about 25% hot reduction
  • the 0.026 Nb steel showed only limited recrystallization even at 40% reduction.
  • the niobium in solid solution reduced the effect of hot reduction on the strength properties by suppressing static recrystallization of the deformed austenite after hot rolling.
  • FIG. 10 shows that the austenite grains have been elongated by the hot rolling reduction without recrystallising into finer grains. Finer grains increase the austenite grain boundary area, thereby reducing the steel hardenability.
  • the thin cast strip niobium steel product had consistent yield and tensile strength levels over the range of hot rolling applied, and capable of providing a yield strength of at least 410 MPa with a reduction of between 20% and 40%.
  • the prior austenite grain size was determined for each strip thickness. The austenite grain size measurements indicated that only very limited recrystallization had occurred at high hot rolling reductions, whereas in the comparable base steel strip, the microstructure almost fully recrystallized at hot rolling reductions over about 25%.
  • the addition of niobium to the cast steel strip suppressed the recrystallization of the coarse as-cast austenite grain size during the hot rolling process, and resulted in the hardenability of the steel being retained after hot rolling and retention of niobium in solution.
  • the higher strength of the present steel strip after hot rolling was mostly due to the microstructure formed.
  • the microstructure of the cast niobium steel was comprised of a majority if not mostly bainite for all strip thicknesses.
  • the comparable non-microalloyed steel achieved similar strength by coiling at a low coiling temperature and had a microstructure comprising mostly acicular ferrite with some grain boundary ferrite.
  • the addition of niobium to the steel strip provided an increase in the hardenability of the steel and suppressed the formation of the grain boundary ferrite and promoted the bainitic microstructure, even at considerably higher coiling temperatures.
  • the yield and tensile strength results from the trial steels, shown in Table 2 below, in the as-hot rolled condition are summarized in FIG. 11.
  • the strength level increases with increasing niobium content, with yield strength of at least 340 MPa, with levels up to about 500 MPa in the as-hot rolled condition.
  • the tensile strength may be at least 410 MPa.
  • the initial rapid increase in strength is attributed to the suppression of proeutectic ferrite formation and the promotion of bainite and acicular ferrite, while the subsequent strengthening can be attributed to continued microstructural refinement and possibly solid solution hardening from niobium retained in solid solution.
  • the transmission electron microscopy (TEM) examination may be used to determine the size, identity and volume fraction of niobium carbonitride particles present in the steel.
  • TEM transmission electron microscopy
  • the absence of any niobium carbonitride particles upon TEM examination supported the view that the observed strength was largely attributable to the microstructure being largely bainite rather than ferrite.
  • the subsequent observed strengthening increment arising from an age hardening heat treatment therefore leads to the conclusion that niobium had been substantially in solution in the hot rolled strip.
  • the amount of microalloy element in solid solution can be concluded.
  • Thin foils or carbon replicates may be evaluated by TEM in determining the amount of the present carbonitride particles.
  • TEM transmission electron microscope
  • a foil is prepared. The foil is cut and ground to a thickness of 0.1 mm. The sample is then thinned to electron transparency by electro-polishing using a 5% perchloric acid, 95% acetic acid electrolyte in a Tenupole-2 electro-polishing unit. The sample can then be directly transferred to the TEM.
  • a desired sample may be prepared by etching a polished sample in Nital (a solution of alcohol and nitric acid) after etching, coating the samples with carbon, and then scoring the carbon coating into appropriate dimensions (for example 2 mm square) for TEM analysis. After scoring, carbon replicas may be liberated from the sample by dissolving the ferrite matrix in 3% Nital. The carbon replica samples are collected on 3mm diameter support grids, then repeatedly washed in ethanol/water solutions. The carbon extraction replica with the supporting grid can then be transferred to the TEM.
  • Nital a solution of alcohol and nitric acid
  • An additional factor believed to account for the absence of niobium carbonitride particles in the hot rolled cast strip relates to the nature of the dispersion of niobium with the rapid solidification of the strip during its formation by the method of continuously making cast strip described.
  • relatively long time intervals were involved in the solidification with slab cooling, slab reheating and thermo-mechanical processing that permitted opportunities for pre-clustering and/or solid state precipitation of carbonitride particles such as (Nb,V,Ti,Mo)(CN), that enabled the kinetics for subsequent precipitation through the stages of the manufacturing process.
  • the extremely rapid initial solidification in forming the cast strip (in about 160 microseconds) is believed to inhibit pre-clustering and/or solid state precipitation of carbonitride particles, and in turn, slow and reduce the kinetics for precipitation of the microalloys in subsequent processing including rolling and coiling operations.
  • the microalloys of Nb, V, Ti, and Mo are relatively more evenly distributed in the austenite and ferrite phases, than in thin steel strip previously made by conventional slab casting and processing.
  • Atom probe analysis of niobium cast strip made by forming from a casting pool between casting rolls as above described has verified the more even distribution of microalloys (indicating reduced pre-clustering and/or solid state precipitation) in both the as cast and the hot rolled strip when coiled at about 650 0 C or lower. This more even distribution of elements is believed to be inhibiting the formation of carbonitrides in the coiling operation under conditions where fine coherent precipitation of such elements occurred in previous conventionally made and processed microalloyed slab cast steel.
  • the microstructure of the present age hardened steel product may have niobium carbonitride particles with an average particle size of 10 nanometers and less.
  • the microstructure of the age hardened steel product may have substantially no niobium carbonitride particles greater than 50 nanometers.
  • short time age hardening is carried out to simulate the ageing potential from processing the niobium microalloyed cast steel product through an annealing furnace attached to continuous galvanizing line or conventional continuous annealing line.
  • the age hardened high strength strip product maybe subsequently galvanized, painted or utilized uncoated.
  • the yield strengths achieved for steel C and steel F are shown in FIG. 12, and the yield strength results for the 0.014% Nb heat, steel A, produced with a lower Mn content, are presented in FIG. 13.
  • the niobium additions increased the yield strength at all coiling temperatures relative to the base steel composition.
  • the yield strength increased by about 70 to 100 MPa (10 to 15 ksi) for the 0.014% Nb and 0.026 Nb additions, and by about 140 to 175 MPa (20-25 ksi) for the 0.065 Nb addition.
  • From FIG. 12 it can be seen that the 0.026% Nb steel achieved higher yield strengths than the 0.8 Mn base steel for similar coiling temperatures, and comparable yield strengths to when the 0.8 Mn base steel was coiled a low temperatures.
  • the strengths achieved in the 0.8 Mn base steel at low coiling temperatures (about 500 0 C) can be achieved at higher coiling temperatures (about 600 0 C) with this Nb addition.
  • the microstructure of the hot rolled and subsequently coiled and cooled steel comprises bainite and acicular ferrite with more than 70% niobium and/or vanadium remaining in solid solution.
  • the microstructure of the hot rolled and subsequently coiled and cooled steel may comprise bainite and acicular ferrite with more than 80% niobium and/or vanadium remaining in solid solution, and alternately may have more than 90 % remaining in solid solution.
  • the niobium cast strip results in light gauge, high strength, steel product.
  • the niobium addition firstly is capable of suppressing the austenite recrystallization during hot rolling, which enhances the hardenability of the steel by retaining the relatively coarse as cast austenite size.
  • the niobium being retained in solid solution in austenite after hot rolling directly increases the steel's hardenability, which assists in transforming the austenite to a final microstructure comprised mostly of bainite, even at relatively high coiling temperatures.
  • the formation of a bainitic microstructure promoted the retention of the niobium addition in solid solution in the hot rolled strip.
  • microalloying elements such as niobium and vanadium in solid solution by the prior processing conditions provided considerable hardenability for subsequent age hardening cycle.
  • Such an age hardening cycle can be produced using a suitable continuous galvanizing line or continuous annealing facility.
  • a microalloyed steel strip made using a thin strip casting process, combined with an age hardening heat treatment provided by a suitable galvanizing line or annealing line, is a unique manufacturing path providing a unique strengthening approach for this type of steel product.
  • microalloying elements such as niobium and vanadium
  • the microalloying elements in solid solution are available for age hardening during a subsequent heat treatment to increase strength.
  • Laboratory age hardening studies established that substantial strengthening could be achieved even with relatively short heat treatment cycles, such as available with continuous annealing lines and galvanizing lines.
  • the results from laboratory simulated continuous annealing cycles applied to trial Steel C (0.026% Nb), Steel F (0.065% Nb), and Steel G (0.084% Nb) are shown in FIGS. 15, through 18.
  • a 10 second hold cycle may be used between about 675 0 C to 725 0 C to prevent overaging.
  • the temperature range is a function of the holding time. Increasing the hold time to 20 seconds lowered the temperature range slightly, while for the zero hold time, the temperature range was increased slightly, as shown in FIG. 17.
  • the age hardening temperature range may be between about 625 0 C and 800 0 C depending upon on the overall heat treatment cycle time, i.e. heating rates, the holding time, and cooling rates.
  • 500 0 C to 650 0 C may be used. From FIG. 6 it can be seen that a heat treatment of 20 minutes at 600 0 C produces similar strength levels as 10 seconds in a continuous annealing cycle at 700 0 C.
  • FIG. 22 shows results of laboratory heat treatments carried out for 20 and 120 minutes. The results show that substantial hardening was achieved for a heat treatment of 120 minutes at 550 0 C, but the 120 minute aging at temperatures over about 650 0 C reduced the hardness of the steel.
  • Fine particles in the size range of 4 to 15 nanometers were found. These fine particles were found to include niobium carbonitrides, indicating that the strengthening may be attributed to age hardening by fine niobium carbonitride particles.
  • the microstructure of the age hardened microalloyed steel product may have niobium carbonitride particles, with an average particle size of 10 nanometers and less.
  • the microstructure of the age hardened steel product may have substantially no niobium carbonitride particles greater than 50 nanometers. Samples of the present niobium steel were inspected using TEM evaluation, and portions of the microstructure had no measurable amount of niobium carbonitride particles.
  • the element additions may provide for increased elongation with increased strength after age hardening by producing smaller precipitate free zone width and smaller change in hardness than in conventionally produced niobium steels. Because of the more even dispersion of elements in rapidly solidified steels, the kinetics of age hardening can be retarded so as to effectively expand the time-temperature window over which the formation of nano-clusters can be stably controlled.
  • the element nano-clusters may provide strengthening in the early stages of age hardening. Cluster strengthening may be due to the extra energy required for dislocations to cut the diffuse boundary of the cluster of solute species. The clusters may provide substantial strengthening without reducing ductility because their elastically soft boundaries do not severely inhibit dislocation movement or cause pile-ups in the way that normal second phase particles do.
  • the microstructure of the hot rolled and subsequently coiled and cooled steel comprises bainite and acicular ferrite with more than 70% niobium and/or vanadium addition remaining in solid solution and substantially no niobium carbonitride particles greater than 50 nanometers.
  • the microstructure of the hot rolled and subsequently coiled and cooled steel may comprise bainite and acicular ferrite with more than 80% niobium and/or vanadium addition remaining in solid solution, and alternately may have more than 90% remaining in solid solution.
  • Formation of carbonitride particles can be activated during heat treatment.
  • pre-precipitation clusters and finer particles are stable over an extended range of time and temperature because of the significant amount of niobium and/or vanadium in solid solution prior to age hardening.
  • the precipitate free zones that form near grain boundaries as a normal precipitation phenomenon are narrower and contain more evenly dispersed nano-clusters and finer precipitates than for conventionally produced steels.
  • the hardness changes in the precipitate free zones relative to the grain interior are relatively small for the present steels. We believe that narrower precipitate free zones and small hardness changes across precipitate free zones reduce stress concentrations in the precipitate free zones reducing microcracking from preferential deformation in the precipitate free zones.
  • the cluster strengthening may be characterized by a strength increase without a deterioration in ductility since dislocation pile -up does not occur at clusters.
  • the combination of narrow precipitate free zones and cluster strengthening mechanisms is believed to lead to precipitate free zones of the present steels. This results in improved elongation because cracks are more difficult to initiate and less constrained to the grain boundary precipitate free zone region.
  • the nano-clusters may co-exist with distinct particles within the grain interior regions over a certain annealing temperature/time combinations.
  • An annealing furnace may be used to perform the age hardening, which is not a current strengthening approach for processing such products.
  • the annealing condition may be a continuous annealing cycle with a peak temperature of at least 650 0 C and less than 800 0 C and better 675 0 C to 750 0 C.
  • strengthening may be achieved in a production environment using a very short age hardening cycle available with conventional annealing furnaces incorporated in continuous galvanizing lines.
  • the final strength levels recorded in the full scale plant trials were similar to that produced with the laboratory heat treatments of the respective steels.
  • Similar results are contemplated with niobium between about 0.01% and about
  • titanium between about 0.01% and about 0.20%, molybdenum between about 0.05% and about 0.50%, and vanadium between about 0.01% and about 0.20%.
  • the yield strength of steel H is shown in FIG. 23.
  • the vanadium steel was produced with two different coiling temperatures, and was subsequently aged for 20 minutes at 650 0 C and 700 0 C to induce hardening by vanadium in solid solution. The results show that significant strengthening was achieved from these heat treatment conditions.
  • the strengthening increment was slightly higher for the material produced with the higher coiling temperature, which may be due to the effects of opposing processes of precipitation hardening and microstructural softening.
  • the strengthening increment realized with the material produced at the lower coiling temperature was of the same order of that achieved with the 0.026% Nb steel.
  • FIG. 24 The yield strength of steel H in the as-hot rolled and galvanized conditions are presented in FIG. 24.
  • FIGS. 23 and 24 indicate that the vanadium steel achieved higher strength levels than the plain carbon base steel, even though it was produced using higher coiling temperatures.
  • the coiling temperature of steel H was 570 0 C, and the base steel coiling temperature was less than 500 0 C.
  • FIG. 24 Also shown in FIG. 24, a strength increase was realized in the vanadium steel from an age hardening using the annealing furnaces on a continuous galvanising line, but the strength increase was less than was realized from an equivalent niobium content.
  • the yield strength of the sample in FIG. 24 on the galvanizing line was about 450 MPa in the galvanised condition, which is in the order achieved with the longer term laboratory heat treatments shown in FIG. 23.
  • the strength of the vanadium steel may be more sensitive to coiling temperature than the niobium steels.
  • This thin cast strip enables production of new steel product types including:
  • a high strength, light gauge, galvanized strip by utilizing a microstructure that has bainite as the major constituent and age hardening during the galvanizing process.
  • the annealing section of the galvanizing line can be used to induce age hardening of the niobium and/or vanadium of the thin cast strip that has been hot rolled.
  • a high strength, light gauge, uncoated strip by utilizing a microstructure that is majority bainite and age hardened during processing on a continuous annealing line.
  • the high temperature furnace of the conventional continuous annealing can be used to induce activation of the niobium and vanadium elements retained in solid solution by the bainite microstructure after hot rolling of the thin cast strip.
  • a high strength, light gauge, hot rolled cast strip product where the strength levels are insensitive to the degree of hot rolling reduction applied.
  • the bainitic microstructure produces a relatively high strength product (YS > 380 MPa ( ⁇ 55ksi)).
  • the suppression of austenite recrystallization during or after hot rolling can provide final strength levels insensitive to the degree of hot rolling reduction.
  • the final strength levels will be consistent across a range of thicknesses that can be produced by a thin cast strip process.

Abstract

Produit en acier ou bande moulée en acier mince comprenant en poids moins de 0,25 % de carbone, entre 0,20 et 2,0% de manganèse, entre 0,05 et 0,50% de silicium, moins de 0,01% d'aluminium, et entre 0,01% de niobium et 0,20% et/ou entre 0,01% et 0,20% de vanadium, ce produit ou cette bande possédant une microstructure qui contient majoritairement de la bainite et de la ferrite aciculaire et plus de 70% de niobium et/ou de vanadium dans une solution solide. Le produit en acier peut présenter une augmentation de son élongation et de sa limite d'élasticité après avoir durci par vieillissement. Le produit en acier durci par vieillissment peut comprendre des particules de carbonitrure de niobium à taille granulométrique moyenne d'au moins 10 nanomètres et pratiquement pas de particules de carbonitrure de niobium supérieures à 50 nanomètres. Le produit en acier peut avoir une limite d'élasticité d'au moins 380 MPa ou une résistance à la traction d'au moins 410 MPa ou les deux à la fois. Le produit en acier ou la bande moulée, en acier, mince a une élongation totale d'au moins 6% ou 10%.
PCT/US2008/062776 2007-05-06 2008-05-06 Produit en bande, moulé, mince contenant des ajouts de microalliage, et son procédé de fabrication WO2008137898A1 (fr)

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PL08747712T PL2152451T3 (pl) 2007-05-06 2008-05-06 Wyrób w postaci cienkiej odlewanej taśmy z dodatkami mikrostopów i sposób jego wytwarzania
JP2010507600A JP5385899B2 (ja) 2007-05-06 2008-05-06 マイクロ合金添加した薄鋳造ストリップ品及びその製造方法
AU2008247365A AU2008247365B2 (en) 2007-05-06 2008-05-06 A thin cast strip product with microalloy additions, and method for making the same
EP08747712.1A EP2152451B1 (fr) 2007-05-06 2008-05-06 Produit en bande, moulé, mince contenant des ajouts de microalliage, et son procédé de fabrication
CN200880023167A CN101765470A (zh) 2007-05-06 2008-05-06 具有微合金添加剂的薄铸造带材产品及其制造方法
NZ581424A NZ581424A (en) 2007-05-06 2008-05-06 A thin cast strip product with microalloy additions, and method for making the same
BRPI0811554A BRPI0811554B1 (pt) 2007-05-06 2008-05-06 produto de aço, produto de aço laminado a quente e método para preparar tira fina de aço lingotado bobinada
CA2686495A CA2686495C (fr) 2007-05-06 2008-05-06 Produit en bande, moule, mince contenant des ajouts de microalliage, et son procede de fabrication

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US11/744,881 US20070212249A1 (en) 2005-10-20 2007-05-06 Thin cast strip product with microalloy additions, and method for making the same
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US60/943,781 2007-06-13

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