EP1337362A1 - A method of producing steel strip - Google Patents

A method of producing steel strip

Info

Publication number
EP1337362A1
EP1337362A1 EP01971503A EP01971503A EP1337362A1 EP 1337362 A1 EP1337362 A1 EP 1337362A1 EP 01971503 A EP01971503 A EP 01971503A EP 01971503 A EP01971503 A EP 01971503A EP 1337362 A1 EP1337362 A1 EP 1337362A1
Authority
EP
European Patent Office
Prior art keywords
strip
steel
cast
microstructure
residuals
Prior art date
Legal status (The legal status 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 status listed.)
Ceased
Application number
EP01971503A
Other languages
German (de)
French (fr)
Other versions
EP1337362A4 (en
Inventor
Lazar Strezov
Kannappar Mukunthan
Walter Blejde
Rama Mahapatra
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nucor Corp
Original Assignee
Nucor Corp
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
Application filed by Nucor Corp filed Critical Nucor Corp
Publication of EP1337362A1 publication Critical patent/EP1337362A1/en
Publication of EP1337362A4 publication Critical patent/EP1337362A4/en
Ceased legal-status Critical Current

Links

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
    • 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
    • B22D11/16—Controlling or regulating processes or operations
    • B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
    • B22D11/225—Controlling or regulating processes or operations for cooling cast stock or mould for secondary cooling
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/573—Continuous furnaces for strip or wire with cooling

Definitions

  • the present invention relates to a method of producing steel strip and the cast strip produced according to the method.
  • the present invention relates to producing steel strip in a continuous strip caster.
  • strip as used in the specification is to be understood to mean a product of 5mm thickness or less.
  • casting steel strip continuously in a twin roll caster involves introducing molten steel between a pair of contra-rotated horizontal casting rolls which are internally water cooled so that metal shells solidify on the moving rolls surfaces and are brought together at the nip between them to produce a solidified strip delivered downwardly from the nip between the rolls, the term "nip" being used to refer to the general region at which the rolls are closest together.
  • the molten metal may be poured from a ladle into a smaller vessel from which it flows through a metal delivery nozzle located above the nip so as to direct it into the nip between the rolls, so forming a casting pool of molten metal supported on the casting surfaces of the rolls immediately above the nip and extending along the length of the nip.
  • This casting pool is usually confined between side plates or dams held in sliding engagement with end surfaces of the rolls so as to dam the two ends of the casting pool against outflow, although alternative means such as electromagnetic barriers have also been proposed.
  • the casting of steel strip in twin roll casters of this kind is for example described in United States Patents 5,184,668, 5,277,243 and 5,934,359.
  • the concentration of residuals in the steel composition can have a significant effect on the finished microstructure, and in turn affect yield strength properties of cast strip.
  • higher concentrations of residuals make it possible to use lower cooling rates to transform the strip from austenite to ferrite in a temperature range between 850°C and 400°C to produce microstructures in cast strip that provide high yield strengths - It is understood that the transformation temperature range is within the range between 850°C and
  • the continuous caster may be a twin roll caster.
  • residuals covers levels of elements, such as copper, tin, zinc, nickel, chromium, and molybdenum, that are included in relatively small amounts, and are usually as a consequence of standard steel making.
  • the elements may be present as a result of using scrap steel to produce steel.
  • the total amount of the residuals is 1.2 wt°6 or less. These residuals may be up to 2.0 wt% where harder steel strip is desired with yield strengths up to and in excess of 700 MPa. This weight percent is the total weight percent in the steel strip including the residuals from scrap steel and steel processing.
  • the cast strip produced in step (a) may have a thickness of no more than 2mm.
  • the cast strip produced in step (a) may include austenite grains that are columnar.
  • the steel may be low carbon steel.
  • low carbon steel is understood to be mean steel of the following composition, in wt%:
  • Mn 1 .0 or less ; residuals: 1.2 or less; and Fe: balance.
  • the low carbon steel may be silicon/manganese killed and may have the following composition by weight:
  • the low carbon steel may be aluminum killed and may have the following composition by weight:
  • the aluminum killed steel may be calcium treated.
  • the method may further include the step of inline hot rolling the cast strip after step (a) and prior to step (b) .
  • Step (b) may include cooling the strip to transform the strip from the austenite to ferrite at a selected cooling rate of at least 0.01°C/sec, and usually at least 0.1 °C/sec, to produce a microstru ⁇ ture that provides required yield strength properties of the cast strip, the microstru ⁇ ture being selected from a group that includes microstructures that are:
  • microstructures of types (ii) and (iii) will have microstructures of types (ii) and (iii) .
  • low temperature transformation products includes idmanstatten ferrite, acicular ferrite, bainite, and martensite.
  • Figure 1 illustrates a strip casting installation incorporating an in-line hot rolling mill and coiler
  • Figure 2 illustrates details of the twin roll strip caster
  • Figure 3 illustrates the effect of residuals on yield strength of cast strip.
  • twin roll casters The following description is in the context of continuous casting steel strip using a twin roll caster.
  • the present invention is not limited to the use of twin roll casters and extends to other types of continuous strip casters.
  • Figure 1 illustrates successive parts of a production line whereby steel strip can be produced in accordance with the present invention.
  • Figures 1 and 2 illustrate a twin roll caster denoted generally as 11 which produces a cast steel strip 12 that passes in a transit path 10 across a guide table 13 to a pinch roll stand 14 comprising pinch rolls 14A.
  • the strip passes into a hot rolling mill 16 comprising a pair of reduction rolls 16A and backing rolls 16B by in which it is hot rolled to reduce its thickness .
  • the rolled strip passes onto a runout table 17 on which it may be force cooled by water jets 18 and through a pinch roll stand 20 comprising a pair of pinch rolls 20A, and thence to a coiler 19.
  • twin roll caster 11 comprises a main machine frame 21 which supports a pair of parallel casting rolls 22 having a 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 25 and thence through a metal delivery nozzle 26 into the nip 27 between the casting rolls 22.
  • Molten metal thus delivered to the nip 27 forms a pool 30 above the nip and this pool is confined at the ends of the rolls by a pair of side closure dams or plates 28 which are applied to the ends of the rolls by a pair of thrusters (not shown) comprising hydraulic cylinder units connected to the side plate holders.
  • the upper surface of pool 30 (generally referred to as the "meniscus" level) may rise above the lower end of the delivery nozzle so that the lower end of the delivery nozzle is immersed within this pool .
  • Casting rolls 22 are water cooled so that shells solidify on the moving roll surfaces and are brought together at the nip 27 between them to produce the solidified strip 12 which is delivered downwardly from the nip between the rolls.
  • twin roll caster may be of the kind which is illustrated and described in some detail in United States Patents 5,184,668 and 5,277,243 or United States Patent 5,488,988 and reference may be made to those patents for appropriate constructional details which form no part of the present invention.
  • the cooling rate in transforming the strip from austenite to ferrite in a temperature range between 850°C and 400°C is selected to be at least 0.01°C/sec, preferably at least 0.1°C/sec, and may be in excess of 100°C/sec. With such cooling rates for low carbon steel it is possible to produce cast strip having microstructures including:
  • the concentration of residuals in the steel is selected having regard to the finished microstructure of the cast strip that is required to provide required mechanical properties for the strip.
  • the present disclosure is based on experimental work that has found the presence of a high amount of residuals (0.2%Cr, 0.2%Ni, 0.2%Mo, 0.4%Cu, 0.2%Sn) has produced a strip with improved microstructure.
  • the experimental findings include that the austenite microstructure of strip cast at 75 m/min was similar to the microstructure of strip without residuals. However, when the cast strip with residuals was subjected to a standard cooling rate of 10-15°C/sec, the resultant finished microstructure was very different from that of the cast strip without residuals cooled at the same rate.
  • the observed microstructure of cooled cast strip with residuals was predominantly bainitic with only a thin band of grain boundary ferrite appearing along the prior austenite grain boundaries, indicating a severely suppressed ferrite transformation caused by the presence of residuals.
  • the mechanical properties of the resultant product are very desirable, with typical values of 540 MPa yield strength, 650 MPa tensile strength and 15% total elongation. Such values could be achieved in the past by icroalloying which added considerable cost to the production of the cast strip.

Abstract

Steel strips and methods for producing steel strips are provided. In an illustrated embodiment, a method for producing steel strips includes continuously casting molten steel into a strip, said molten steel comprising a concentration of residuals of 2.0 wt% or less is selected with regard to the microstructure of the finished strip to provide a desired yield strength; and cooling the strip to transform the strip from austenite to ferrite in the temperature range of 850°C to 400°C. Cast steel with improved yield strength properties is produced by such method.

Description

A METHOD OF PRODUCING STEEL STRIP
This application claims priority to Australian Provisional Patent Application No. PR0460, filed October 2, 2000.
Background and Summary of the Invention
The present invention relates to a method of producing steel strip and the cast strip produced according to the method.
In particular, the present invention relates to producing steel strip in a continuous strip caster.
The term "strip" as used in the specification is to be understood to mean a product of 5mm thickness or less.
The applicants have carried out extensive research and development work in the field of casting steel strip in a continuous strip caster in the form of a twin roll caster.
In general terms, casting steel strip continuously in a twin roll caster involves introducing molten steel between a pair of contra-rotated horizontal casting rolls which are internally water cooled so that metal shells solidify on the moving rolls surfaces and are brought together at the nip between them to produce a solidified strip delivered downwardly from the nip between the rolls, the term "nip" being used to refer to the general region at which the rolls are closest together. The molten metal may be poured from a ladle into a smaller vessel from which it flows through a metal delivery nozzle located above the nip so as to direct it into the nip between the rolls, so forming a casting pool of molten metal supported on the casting surfaces of the rolls immediately above the nip and extending along the length of the nip. This casting pool is usually confined between side plates or dams held in sliding engagement with end surfaces of the rolls so as to dam the two ends of the casting pool against outflow, although alternative means such as electromagnetic barriers have also been proposed. The casting of steel strip in twin roll casters of this kind is for example described in United States Patents 5,184,668, 5,277,243 and 5,934,359.
The concentration of residuals in the steel composition can have a significant effect on the finished microstructure, and in turn affect yield strength properties of cast strip. In particular, higher concentrations of residuals make it possible to use lower cooling rates to transform the strip from austenite to ferrite in a temperature range between 850°C and 400°C to produce microstructures in cast strip that provide high yield strengths - It is understood that the transformation temperature range is within the range between 850°C and
400°C and not that entire temperature range. The precise transformation temperature range will vary with the chemistry of the steel composition and processing characteristics .
There is provided a method of producing steel strip which includes the steps of:
(a) continuously casting molten steel into a strip, said molten steel comprising a concentration of residuals in the steel composition selected with regard to the microstructure of the strip that is required to provide required mechanical properties; and
(b) cooling the strip to transform the strip from austenite to ferrite in a temperature range between 850°C and 400°C.
The continuous caster may be a twin roll caster.
The term "residuals" covers levels of elements, such as copper, tin, zinc, nickel, chromium, and molybdenum, that are included in relatively small amounts, and are usually as a consequence of standard steel making. By way of example, the elements may be present as a result of using scrap steel to produce steel.
In one embodiment, the total amount of the residuals is 1.2 wt°6 or less. These residuals may be up to 2.0 wt% where harder steel strip is desired with yield strengths up to and in excess of 700 MPa. This weight percent is the total weight percent in the steel strip including the residuals from scrap steel and steel processing.
In one embodiment, the cast strip produced in step (a) may have a thickness of no more than 2mm.
In one embodiment, the cast strip produced in step (a) may include austenite grains that are columnar.
The steel may be low carbon steel. The term "low carbon steel" is understood to be mean steel of the following composition, in wt%:
C : 0 .02-0 . 08
Si : 0 .5 or less ;
Mn: 1 .0 or less ; residuals: 1.2 or less; and Fe: balance.
The low carbon steel may be silicon/manganese killed and may have the following composition by weight:
Carbon 0.02 - 0.08%
Manganese 0.30 - 0.80% Silicon 0.10 - 0.40%
Sulphur 0.002 - 0.05%
Aluminum less than 0.01%
The low carbon steel may be aluminum killed and may have the following composition by weight:
Carbon 0.02 - 0.08%
Manganese 0.40% max
Silicon 0.05% max Sulphur 0.002 - 0.05%
Aluminum 0.05% max
The aluminum killed steel may be calcium treated.
The method may further include the step of inline hot rolling the cast strip after step (a) and prior to step (b) .
Step (b) may include cooling the strip to transform the strip from the austenite to ferrite at a selected cooling rate of at least 0.01°C/sec, and usually at least 0.1 °C/sec, to produce a microstruσture that provides required yield strength properties of the cast strip, the microstruσture being selected from a group that includes microstructures that are:
(i) predominantly polygonal ferrite;
(ii) a mixture of polygonal ferrite and low temperature transformation products; and (iii) predominantly low temperature transformation products .
It is understood that most embodiments of the present invention will have microstructures of types (ii) and (iii) .
The term "low temperature transformation products" includes idmanstatten ferrite, acicular ferrite, bainite, and martensite.
In order that the invention may be more fully explained, an example will be described with reference to the accompanying drawings, in which:
Brief Description of the Drawings
Figure 1 illustrates a strip casting installation incorporating an in-line hot rolling mill and coiler;
Figure 2 illustrates details of the twin roll strip caster; and
Figure 3 illustrates the effect of residuals on yield strength of cast strip.
Detailed Description of the Invention
The following description is in the context of continuous casting steel strip using a twin roll caster. The present invention is not limited to the use of twin roll casters and extends to other types of continuous strip casters.
Figure 1 illustrates successive parts of a production line whereby steel strip can be produced in accordance with the present invention. Figures 1 and 2 illustrate a twin roll caster denoted generally as 11 which produces a cast steel strip 12 that passes in a transit path 10 across a guide table 13 to a pinch roll stand 14 comprising pinch rolls 14A. Immediately after exiting the pinch roll stand 14, the strip passes into a hot rolling mill 16 comprising a pair of reduction rolls 16A and backing rolls 16B by in which it is hot rolled to reduce its thickness . The rolled strip passes onto a runout table 17 on which it may be force cooled by water jets 18 and through a pinch roll stand 20 comprising a pair of pinch rolls 20A, and thence to a coiler 19.
As shown in Figure 2, twin roll caster 11 comprises a main machine frame 21 which supports a pair of parallel casting rolls 22 having a 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 25 and thence through a metal delivery nozzle 26 into the nip 27 between the casting rolls 22. Molten metal thus delivered to the nip 27 forms a pool 30 above the nip and this pool is confined at the ends of the rolls by a pair of side closure dams or plates 28 which are applied to the ends of the rolls by a pair of thrusters (not shown) comprising hydraulic cylinder units connected to the side plate holders. The upper surface of pool 30 (generally referred to as the "meniscus" level) may rise above the lower end of the delivery nozzle so that the lower end of the delivery nozzle is immersed within this pool .
Casting rolls 22 are water cooled so that shells solidify on the moving roll surfaces and are brought together at the nip 27 between them to produce the solidified strip 12 which is delivered downwardly from the nip between the rolls.
The twin roll caster may be of the kind which is illustrated and described in some detail in United States Patents 5,184,668 and 5,277,243 or United States Patent 5,488,988 and reference may be made to those patents for appropriate constructional details which form no part of the present invention.
Typically, the strip passing from the twin roll caster will be of the order of 1400°C and the temperature of the strip presented to the hot rolling mill may be about 900-1100°C. The strip may have a width in the range of 0.9 m to 2.0 m and a thickness in the range of 0.7 mm to 2.0 mm. The strip speed may be in the order of 1.0 m/sec.
The cooling rate in transforming the strip from austenite to ferrite in a temperature range between 850°C and 400°C is selected to be at least 0.01°C/sec, preferably at least 0.1°C/sec, and may be in excess of 100°C/sec. With such cooling rates for low carbon steel it is possible to produce cast strip having microstructures including:
(i) predominantly polygonal ferrite;
(ii) a mixture of polygonal ferrite and low temperature transformation products, such as a acicular ferrite, Widmanstatten ferrite, and bainite; and
(iii) predominantly low temperature transformation products.
It is understood that most embodiments of the present invention will have microstructures of types (ii) and (iii).
In the case of low carbon steels, such a range of microstructures can produce yield strengths in excess of 450MPa .
The concentration of residuals in the steel is selected having regard to the finished microstructure of the cast strip that is required to provide required mechanical properties for the strip.
The present disclosure is based on experimental work that has found the presence of a high amount of residuals (0.2%Cr, 0.2%Ni, 0.2%Mo, 0.4%Cu, 0.2%Sn) has produced a strip with improved microstructure.
The experimental findings include that the austenite microstructure of strip cast at 75 m/min was similar to the microstructure of strip without residuals. However, when the cast strip with residuals was subjected to a standard cooling rate of 10-15°C/sec, the resultant finished microstructure was very different from that of the cast strip without residuals cooled at the same rate.
The observed microstructure of cooled cast strip with residuals was predominantly bainitic with only a thin band of grain boundary ferrite appearing along the prior austenite grain boundaries, indicating a severely suppressed ferrite transformation caused by the presence of residuals. The mechanical properties of the resultant product are very desirable, with typical values of 540 MPa yield strength, 650 MPa tensile strength and 15% total elongation. Such values could be achieved in the past by icroalloying which added considerable cost to the production of the cast strip.
The effect of residuals was to enhance the proportion of low temperature transformation products (particularly the bainites) by lowering austenite to ferrite transformation temperatures and slowing the kinetics of polygonal ferrite formation. One, but not the only one, of the important consequences of this finding is that an increase in the concentration of residuals effects a reduction in the cooling rate that is required to transform austenite to ferrite to form a required microstructure to provide high yield strengths .
Many modifications may be made to the present invention as described above without departing from the spirit and scope of the invention.

Claims

THE CLAIMS DEFINING THE INVENTION ARE AS FOLLOWS:
1. A method of producing steel strip including the steps of :
(a) continuously casting molten steel into a strip including austenite grains, said molten steel comprising a concentration of residuals selected with regard to the microstructure of the finished strip to provide a desired yield strength; and
(b) cooling the cast strip to transform austenite grains in the strip to ferrite in a temperature range between 850°C and 400°C.
2. The method of claim 1 wherein the total amount of the residuals is 2.0 wt% or less.
3. The method of claim 1 wherein the total amount of the residuals is 1.2 wt% or less.
4 - The method of any one of the preceding claims wherein the cast strip produced in step (a) has a thickness of no more than 2mm.
5. The method of any one of the preceding claims wherein the cast strip produced in step (a) includes austenite grains that are columnar.
6. The method of any one of the preceding claims wherein the steel is low carbon steel.
7. The method of claim 6 wherein the low carbon steel is a silicon/manganese killed steel.
8. The method of claim 7 wherein the silicon/manganese killed steel includes, by wt%:
Carbon 0.02 - 0.08%
Manganese 0.30 - 0.80% Silicon 0.10 - 0.40%
Sulphur 0.002 - 0.05%
Aluminium less than 0.01%
9. The method of any one of claims 1 to 6 wherein the low carbon steel is an aluminum killed steel.
10. The method of in claim 9 wherein the aluminum killed low carbon steel has the following composition by weight :
Carbon 0.02 - 0.08%
Manganese 0.40% max
Silicon 0.05% max
Sulphur 0.002 - 0.05'
Aluminum 0.05% max
11. The method of any one of the preceding claims wherein the continuous caster is a twin roll caster.
12. The method of any one of the preceding claims further including the step of in-line hot rolling the casted strip of step (a) prior to step (b) .
13. The method of any one of the preceding claims wherein step (b) includes cooling the casted strip to transform the strip from austenite to ferrite in a temperature range between 850°C and 400°C at a selected cooling rate of at least 0.01°C/sec to produce a microstructure that provides required yield strength of the casted strip, the microstructure being selected from a group including: (i) predominantly polygonal ferrite;
(ii) a mixture of polygonal ferrite and low temperature transformation products; and
(iii) predominantly low temperature transformation products.
14. The method of claim 13 wherein the cooling rate is selected so that the microstructure is either (ii) a mixture of polygonal ferrite and low temperature transformation products; or (iii) predominantly low temperature transformation products.
15. A cast steel strip produced by the steps of:
(a) continuously casting molten steel into a strip including austenite grains, said molten steel comprising a concentration of residuals selected with regard to the microstructure of the finished strip to provide a desired yield strength; and
(b) cooling the cast strip to transform the austenite grains in the strip to ferrite in a temperature range between 850°C and 400°C.
16. The cast steel strip of claim 15 wherein the total amount of the residuals is 2.0 wt% or less.
17. The cast steel strip of claim 15 wherein the total amount of the residuals is 1.2 wt% or less.
18. The cast steel strip of any one of claims 15 to 17 wherein the cast strip produced in step (a) includes austenite grains that are columnar.
19. The cast steel strip of any one of claims 15 to 18 wherein the steel is low carbon steel.
20. The cast steel strip of claim 19 wherein the low carbon steel is a silicon/manganese killed steel.
21. The cast steel strip of claim 20 wherein the silicon/manganese killed steel includes, by wt%:
Carbon 0.02 - 0.08%
Manganese 0.30 - 0.80%
Silicon 0.10 - 0.40%
Sulphur 0.002 - 0.05% Aluminum less than 0.01%
22. The cast steel strip of claim 19 wherein the low carbon steel is an aluminum killed steel.
23. The cast steel strip of claim 22 wherein the aluminum killed low carbon steel has the following composition by weight:
Carbon 0.02 - 0.08% Manganese 0.40% max
Silicon 0.05% max
Sulphur 0.002 - 0.05%
Aluminum 0.05% max
24. The cast steel strip of any one of claims 15 to
23 further includes the step of in-line hot rolling the casted strip of step (a) prior to step (b) .
25. The cast steel strip of any one of claims 15 to 24 wherein step (b) includes cooling the cast strip to transform the strip from austenite to ferrite at a selected cooling rate of at least 0.01°C/sec to produce a microstructure that provides required yield strength of the casted strip, the microstructure being selected from a group including:
(i) predominantly polygonal ferrite;
(ii) a mixture of polygonal ferrite and low temperature transformation products; and
(iv) predominantly low temperature transformation products.
26. The cast strip of claim 25 wherein the cooling rate is selected so that the microstructure is either (ii) a mixture of polygonal ferrite and low temperature transformation products; or (iii) predominantly low temperature transformation products.
EP01971503A 2000-10-02 2001-09-28 A method of producing steel strip Ceased EP1337362A4 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
AUPR046000 2000-10-02
AUPR0460A AUPR046000A0 (en) 2000-10-02 2000-10-02 A method of producing steel strip
PCT/AU2001/001224 WO2002028569A1 (en) 2000-10-02 2001-09-28 A method of producing steel strip

Publications (2)

Publication Number Publication Date
EP1337362A1 true EP1337362A1 (en) 2003-08-27
EP1337362A4 EP1337362A4 (en) 2004-11-03

Family

ID=3824520

Family Applications (1)

Application Number Title Priority Date Filing Date
EP01971503A Ceased EP1337362A4 (en) 2000-10-02 2001-09-28 A method of producing steel strip

Country Status (13)

Country Link
US (1) US20020043304A1 (en)
EP (1) EP1337362A4 (en)
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JP4197269B2 (en) * 2002-09-09 2008-12-17 株式会社キッツ Nickel elution prevention method for copper alloy piping equipment such as valves and fittings and its copper alloy piping equipment
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