AU2008249238B2

AU2008249238B2 - Casting steel strip

Info

Publication number: AU2008249238B2
Application number: AU2008249238A
Authority: AU
Inventors: Walter Blejde; Rama Ballav Mahapatra; Lazar Strezov
Original assignee: Nucor Corp
Current assignee: Nucor Corp
Priority date: 2001-09-14
Filing date: 2008-11-27
Publication date: 2011-03-24
Anticipated expiration: 2022-09-13
Also published as: MXPA04002374A; JP4495455B2; EP1439926A1; JP2005501741A; UA77001C2; BRPI0212499B1; IS7168A; CO5560594A2; EP1439926A4; ATE509716T1; NO342646B1; CN1553836A; US20030111206A1; BR0212499A; WO2003024644A1; HRP20040234A2; RU2004111292A; RU2297900C2; CN1277634C; EP1439926B1

Abstract

A method of producing strip comprising the steps of assembling a pair of casting rolls with a nip between them, introducing between the casting rolls to form a casting pool of molten carbon steel having a total oxygen content of at least 100 ppm and usually less than 250 ppm, counter rotating the casting rolls, solidifying the molten steel on the rolls to form metal shells with levels of oxide inclusions reflected by the total oxygen content of the molten steel, and forming thin steel strip through the nip between the casting rolls from the solidified shells. A unique steel strip may be obtained using the method having ductile properties.

Description

AUSTRALIA Patents Act 1990 COMPLETE SPECIFICATION Standard Patent Applicant (s): NUCOR CORPORATION Invention Title: CASTING STEEL STRIP The following statement is a full description of this invention, including the best method for performing it known to me/us: P63938.AU.2 PaSe1 _Filng Appcatlon 2008-11-27.doc (M) - 2 CASTING STEEL STRIP TECHNICAL FIELD This invention relates to the casting of steel 5 strip. It has particular application to continuous casting of thin steel strip in a twin roll caster. In twin roll casting, molten metal is introduced between a pair of contra-rotated horizontal casting rolls which are cooled 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 rolls. The term "nip" is used herein 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. 5 When casting thin steel strip in a twin roll caster the molten steel in the casting pool will generally be at a temperature of the order of 1500*C and above, and it is therefore necessary to achieve very high cooling rates over the casting surfaces of the rolls. It is particularly 0 important to achieve a high heat flux and extensive nucleation on initial solidification of the steel on the casting surfaces to form the metal shells. United States Patent 5,720,336 describes how the heat flux on initial solidification can be increased by adjusting the steel melt chemistry such that a 5 substantial proportion of the metal oxides formed as deoxidation products are liquid at the initial solidification temperature so as to form a substantially liquid layer at the interface between the molten metal and each casting surface. N:\Melbourne\Casee\Patent\63000-63999\P63938.AU.2\Specia\US 60-322261 nat phase au.doc 27/11/08 - 3 As disclosed in United States Patents 5,934,359 and 6,059,014 and International Application AU 99/00641, nucleation of the steel on initial solidification can be influenced by the texture of the casting surface. In particular International Application AU 99/00641 discloses that a random texture of peaks and troughs can enhance initial solidification by providing potential nucleation sites distributed throughout the casting surfaces. We have now determined that nucleation is also dependent on the presence of oxide inclusions in the ) steel melt and that surprisingly it is not advantageous in twin roll strip casting to cast with "clean" steel in which the number of inclusions formed during deoxidation has been minimised in the molten steel prior to casting . Steel for continuous casting is subjected to deoxidation treatment in the ladle prior to pouring. In twin roll casting the steel is generally subjected to silicon manganese ladle deoxidation although it is possible to use aluminum deoxidation with calcium addition to control the formation of solid A1 2 0 3 inclusions that can clog the fine ) metal flow passages in the metal delivery system through which molten metal is delivered to the casting pool. It has hitherto been thought desirable to aim for optimum steel cleanliness by ladle treatment to minimise the total oxygen level in the molten steel. However we have now determined 5 that lowering the steel oxygen level reduces the volume of inclusions and if the total oxygen content of the steel is reduced below a certain level the nature of the initial contact between the steel and roll surfaces can be adversely effected to the extent that there is insufficient nucleation 0 to generate rapid initial solidification and high heat flux. Molten steel is trimmed by deoxidation in the ladle such that the total oxygen content falls within a range which ensures satisfactory solidification on the casting rolls and production of a satisfactory strip product. The molten steel 5 contains a distribution of oxide inclusions (typically MnO, CaO, Si0 2 and/or A1 2 0 3 ) sufficient to provide an adequate density of nucleation sites on the roll surfaces for initial solidification and the resulting strip product exhibits a N:\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Specis\US 60-322261 nat phase au.doc 27/11/08 -4 characteristic distribution of solidified inclusions. DISCLOSURE OF THE INVENTION There is provided a method of making a steel strip by continuous casting comprising the steps of: a. assembling a pair of cooled casting rolls having a nip between them and with confining closures adjacent the ends of the nip; b. introducing molten low carbon steel having a total oxygen content of at least 100 ppm and a free oxygen content between 30 and 50ppm between the pair of casting rolls to form a casting pool between the casting rolls; C. counter rotating the casting rolls and solidifying the molten steel to form metal shells on the surface of the casting rolls with levels of oxide inclusions reflected by the total oxygen content of the molten steel to promote the formation of thin steel strip; and d. forming solidified thin steel strip through the nip of the casting rolls from said solidified shells. There is also provided a method of making a steel 5 strip by continuous casting comprising the steps of: a. assembling a pair of cooled casting rolls having a nip between them and with confining closures adjacent the ends of the nip; 0 b. introducing molten steel between the pair of casting rolls to form a casting pool between the casting rolls, the molten steel being a low carbon steel having a carbon content in the range of 0.001% to 0.01% by weight, a manganese 5 content in the range of 0.01 to 2.0% by weight, and a silicon content in the range of 0.01% to 10% by weight and having a total oxygen content of at least 100 ppm; N?\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Specis\US 60-322261 nat phase au.doc 27/11/08 -5 c. counter rotating the casting rolls and solidifying the molten steel to form metal shells on the surface of the casting rolls with levels of oxide inclusions reflected by the total oxygen content of the molten steel to promote the formation of thin steel strip; and d. forming solidified thin steel strip through the nip of the casting rolls from said solidified shells. The total oxygen content of the molten steel in the casting pool may be between 100 ppm and 250 ppm. More specifically, it may be about 200 ppm. The low carbon steel may have a carbon content in the range 0.001% to 0.1% by 5 weight, a manganese content in the range 0.1% to 2.0% by weight and a silicon content in the range 0.01% to 10% by weight. The steel may have an aluminum content of the order of 0.01% or less by weight. The aluminum may for example be as little as 0.008% or less by weight. The molten steel may be a J silicon/manganese killed steel. The oxide inclusions are solidification inclusions and deoxidation inclusions. The solidification inclusions are formed during cooling and solidification of the steel in casting, and deoxidation inclusion are formed during 5 deoxidation of the molten steel before casting. The solidified steel may contain oxide inclusions usually comprised of any one or more of MnO, SiO 2 and A1 2 0 3 distributed through the steel at an inclusion density in the range 2 gm/cm 3 and 4gm/cm 3 . 0 The molten steel may be refined in a ladle prior to introduction between the casting rolls to form the casting pool by heating a steel charge and slag forming material in the ladle whereby to form molten steel covered by a slag containing silicon, manganese and calcium oxides. The molten 5 steel may be stirred by injecting an inert gas into it to cause desulphurisation, and with steels such as a silicon/manganese killed steel, then injecting oxygen, to produce steel having the desired total oxygen content of at N,\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\SpeciB\US 60-322261 nat phase au.doc 27/11/08 -6 least 100 ppm and usually less than 250 ppm. The desulphurisation may reduce the sulphur content of the molten steel to less than 0.01% by weight. The thin steel strip produced by continuous twin roll casting as described above has a thickness of less than 5 mm and is formed of a solidified steel containing solidified oxide inclusions. The distribution of the inclusions may be such that at the two the surface regions of the strip to a depth of 2 microns from the outer faces contain solidified ) inclusions to a per unit area density of at least 120 inclusions/mm 2 . The solidified steel may be a silicon/manganese killed steel and the oxide inclusions may comprise any one or more of MnO, Si0 2 and A1 2 0 3 inclusions. The inclusions typically may range in size between 2 and 12 microns, so that at least a majority of the inclusions are in that size range. The method described above produces a unique steel high in oxygen content distributed in oxide inclusions. Specifically, the combination of the high oxygen content in ) the molten steel and the short residence time of the molten steel in the casting pool results in a thin steel strip with an improved ductility properties. BRIEF DESCRIPTION OF THE DRAWINGS In order that the invention may be described in more detail, some specific examples will be given with reference to the accompanying drawings in which: Figure 1 shows the effect of inclusion melting points on heat fluxes obtained in twin roll casting trials 0 using silicon/manganese killed steels; Figure 2 is an energy dispersive spectroscopy (EDS) map of Mn showing a band of fine solidification inclusions in a solidified steel strip; Figure 3 is a plot showing the effect of varying 5 manganese to silicon contents on the liquidus temperature of inclusions; Figure 4 shows the relationship between alumina content (measured from the strip inclusions) and deoxidation N?\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Specie\US 60-322261 nat phase au.doc 27/11/08 -7 effectiveness; Figure 5 is a ternary phase diagram for MnO.SiO 2 .Al2 O3 ; Figure 6 shows the relationship between alumina ) content inclusions and liquidus temperature; Figure 7 shows the effect of oxygen in a molten steel on surface tension; and Figure 8 is a plot of the results of calculations concerning the inclusions available for nucleation at ) differing steel cleanliness levels. DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT We have conducted extensive casting trials on a twin roll caster of the kind fully described in United States Patents 5,184,668 and 5,277,243 to produce steel strip of the order of 1 mm thick and less. Such casting trials using silicon manganese killed steel have demonstrated that the melting point of oxide inclusions in the molten steel have an effect on the heat fluxes obtained during steel solidification ) as illustrated in Figure 1. Low melting point oxides improve the heat transfer contact between the molten metal and the casting roll surfaces in the upper regions of the pool, generating higher heat transfer rates. Liquid inclusions are not produced when the melting point is greater than the steel 5 temperature in the casting pool. Therefore, there is a dramatic reduction in heat transfer rate when the inclusion melting point is greater than approximately 1600"C. Casting trials with aluminum killed steels have shown that in order to avoid the formation of high melting 0 point alumina inclusions (melting point 2050*C) it is necessary to have calcium treatment to provide liquid CaO.A1 2 0 3 inclusions. The oxide inclusions formed in the solidified metal shells and in turn the thin steel strip comprise inclusions 5 formed during cooling and solidification of the steel, and deoxidation inclusions formed during refining in the ladle. The free oxygen level in the steel is reduced dramatically during cooling at the meniscus, resulting in the Nt\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Speci\US 60-322261 nat phase au.doc 27/11/08 - 8 generation of solidification inclusions near the surface of the strip. These solidification inclusions are formed predominantly of MnO.SiO 2 by the following reaction: Mn+Si+30 = MnO.SiO 2 The appearance of the solidification inclusions on the strip surface, obtained from an Energy Dispersive Spectroscopy (EDS) map, is shown in Figure 2. It can be seen ) that solidification inclusions are extremely fine (typically less than 2 to 3pm) and are located in a band located within 10 to 20pm from the surface. A typical size distribution of the inclusions through the strip is shown in Figure 3 of our paper entitled Recent Developments in Project M the Joint Development of Low Carbon Steel Strip Casting by BHP and IHI, presented at the METEC Congress 99, Dusseldorf Germany (June 13-15, 1999) The comparative levels of the solidification inclusions is primarily determined by the Mn and Si levels in ) the steel. Figure 3 shows that the ratio of Mn to Si has a significant effect on the liquidus temperature of the inclusions. A manganese silicon killed steel having a carbon content in the range of 0.001% to 0.1% by weight, a manganese content in the range 0.1% to 2.0% by weight and a silicon 5 content in the range 0.1% to 10% by weight and an aluminum content of the order of 0.01% or less by weight can produce such oxide inclusions during cooling of the steel in the upper regions of the casting pool. In particular the steel may have the following composition, termed M06: 0 Carbon 0.06% by weight Manganese 0.6% by weight Silicon 0.28% by weight Aluminium 0.002% by weight. 5 Deoxidation inclusions are generated during deoxidation of the molten steel in the ladle with Al, Si and Mn. Thus, the composition of the oxide inclusions formed N.\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Specis\US 60-322261 nat phase au.doc 27/11/08 - 9 during deoxidation is mainly MnO.SiO 2 .A1 2 0 3 based. These deoxidation inclusions are randomly located in the strip and are coarser than the solidification inclusions near the strip surface. The alumina content of the inclusions has a strong effect on the free oxygen level in the steel. Figure 4 shows that with increasing alumina content, free oxygen in the steel is reduced. With the introduction of alumina, MnO.SiO 2 inclusions are diluted with a subsequent reduction in their ) activity, which in turn reduces the free oxygen level, as seen from the reaction below: Mn + Si + 30 + A1 2 0 3 C> (A1 2 0 3 ) .MnO.SiO 2 . For MnO-SiO 2 -Al 2 0 3 based inclusions, the effect of inclusion composition on liquidus temperature can be obtained from the ternary phase diagram shown in Figure 5. Analysis of the oxide inclusions in the thin steel strip has shown that the MnO/SiO 2 ratio is typically within 0.6 to 0.8 ) and for this regime, it was found that alumina content of the oxide inclusions had the strongest effect on the inclusion melting point (liquidus temperature), as shown in Figure 6. We have determined that it is important for casting in accordance with the present invention to have the S solidification and deoxidation inclusions such that they are liquid at the initial solidification temperature of the steel and that the molten steel in the casting pool have an oxygen content of at least 100 ppm to produce metal shells with levels of oxide inclusions reflected by the total oxygen 0 content of the molten steel to promote nucleation and high heat flux during the initial solidification of the steel on the casting roll surfaces. Both solidification and deoxidation inclusions are oxide inclusions and provide nucleation sites and contribute significantly to nucleation during the metal 5 solidification process, but the deoxidation inclusions are ultimately rate controlling in that their concentration can be varied. The deoxidation inclusions are much bigger, typically greater than 4 microns, whereas the solidification inclusions N:\Melbourne\Casea\Patent\63000-63999\P63938.AU.2\Specis\US 60-322261 nat phase au.doc 27/11/08 - 10 are generally less than 2 microns and are MnO-SiO 2 based and have no A1 2 0 3 whereas the deoxidation inclusions also have Al 2 0 3 . It has been found in casting trials using the above 5 M06 grade of silicon/manganese killed steel that if the total oxygen content of the steel is reduced in the ladle refining process to low levels of less than 100 ppm, heat fluxes are reduced and casting is impaired whereas good casting results can be achieved if the total oxygen content is at least above ) 100 ppm and typically on the order of 200 ppm. These oxygen levels in the ladle result in total oxygen levels of at least 70ppm and free oxygen levels between 20 and 60 ppm in the tundish, and in turn the same or slightly lower oxygen levels in the casting pool. The total oxygen content may be measured ) by a "Leco" instrument and is controlled by the degree of "rinsing" during ladle treatment, i.e. the amount of argon bubbled through the ladle via a porous plug or top lance, and the duration of the treatment. The total oxygen content was measured by conventional procedures using the LECO TC-436 ) Nitrogen/Oxygen Determinator described in the TC 436 Nitrogen/Oxygen Determinator Instructional Manual available from LECO (Form No. 200-403, Rev. Apr. 96, Section 7 at pp. 7 1 to 7-4. In order to determine whether the enhanced heat 5 fluxes obtained with higher total oxygen contents was due to the availability of oxide inclusions as nucleation sites, casting trials were carried out with steels in which deoxidation in the ladle was carried out with calcium silicide (Ca-Si) and the results compared with casting with the low 0 carbon Si-killed steel known as M06 grades of steel. The results are set out in the following table: Table 1 Heat flux differences between M06 and Cal-Sil grades. 5 Casting Pool Total heat Cast No. Grade speed, Height, Removed (m/min) (mm) (MW) N:\Melbourne\Casea\Patent\63000-63999\P63938.AU.2\Specis\US 60-322261 nat phase au.doc 27/11/08 - 11 M 33 M06 64 171 3.55 M 34 M06 62 169 3.58 o 50 Cal-Sil 60 176 2.54 o 51 Cal-Sil 66 175 2.56 Although Mn and Si levels were similar to normal Si killed grades, the free oxygen level in Ca-Si heats was lower and the oxide inclusions contained more CaO. Heat fluxes in 5 Ca-Si heats were lower despite a lower inclusion melting point (See Table 2). Table 2 Slag compositions with Ca-Si deoxidation Free Inclusion Grade Oxygen Slag Composition (wt %) melting (ppm) Si0 2 MnO Al 2 0 3 CaO temperature (*C) Ca-Si 23 32.5 9.8 32.1 22.1 1399 The free oxygen levels in Ca-Si grades were lower, typically 20 to 30 ppm compared to 40 to 50 ppm with M06 grades. Oxygen is a surface active element and thus reduction in oxygen level is expected to reduce the wetting between molten steel and the casting rolls and cause a reduction in the heat transfer rate. However, from Figure 7 it appears that oxygen reduction from 40 to 20 ppm may not be sufficient to increase the surface tension to levels that explain the 0 observed reduction in the heat flux. It can be concluded that lowering the free and total oxygen levels in the steel reduces the volume of inclusions and thus reduces the number of oxide inclusions for initial nucleation. This has the potential to adversely impact the 5 nature of the initial contact between steel and the roll surface. Dip testing work has shown that a nucleation per unit area density of about 120/mm 2 is required to generate sufficient heat flux on initial solidification in the upper or N?\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Specie\US 60-322261 nat phase au.doc 27/11/08 - 12 meniscus region of the casting pool. Dip testing involves advancing a chilled block into a bath of molten steel at such a speed as to closely simulate the conditions at the casting surfaces of a twin roll caster. Steel solidifies onto the chilled block as it moves through the molten bath to produce a layer of solidified steel on the surface of the block. The thickness of this layer can be measured at points throughout its area to map variations in the solidification rate and therefore the effective rate of heat transfer at the various ) locations. It is thus possible to produce an overall solidification rate as well as total heat flux measurements. It is also possible to examine the microstructure of the strip surface to correlate changes in the solidification microstructure with the changes in observed solidification rates and heat transfer values and to examine the structures associated with nucleation on initial solidification at the chilled surface. A dip testing apparatus is more fully described in United States Patent 5,720,336. The relationship of the oxygen content of the liquid ) steel on initial nucleation and heat transfer has been examined using a model described in Appendix 1. This model assumes that all the oxide inclusions are spherical and are uniformly distributed throughout the steel. A surface layer was assumed to be 2 pm and that only inclusions present in 5 that surface layer could participate in the nucleation process on initial solidification of the steel. The input to the model was total oxygen content in the steel, inclusion diameter, strip thickness, casting speed, and surface layer thickness. The output was the percentage of inclusions of the 0 total in the steel required to meet a targeted nucleation per unit area density of 120/mm 2 . Figure 8 is a plot of the percentage of oxide inclusions in the surface layer required to participate in the nucleation process to achieve the target nucleation per unit 5 area density at different steel cleanliness levels as expressed by total oxygen content, assuming a strip thickness of 1.6 mm and a casting speed of 80/min. This shows that for a 2 pm inclusion size and 200 ppm total oxygen content, 20% of N:\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Specis\US 60-322261 nat phaae au.doc 27/11/08 - 13 the total available oxide inclusions in the surface layer are required to achieve the target nucleation per unit area density of 120/mm 2 . However, at 80 ppm total oxygen content, around 50% of the inclusions are required to achieve the critical nucleation rate and at 40 ppm total oxygen level there will be an insufficient level of oxide inclusions to meet the target nucleation per unit area density. Accordingly when trimming the steel by deoxidation in the ladle, the oxygen content of the steel can be controlled to produce a ) total oxygen content in the range 100 to 250 ppm and typically about 200 ppm. This will have the result that the two micron deep layers adjacent the casting rolls on initial solidification will contain oxide inclusions having a per unit area density of at least 120/mm 2 . These inclusions will be present in the outer surface layers of the final solidified strip product and can be detected by appropriate examination, for example by energy dispersive spectroscopy (EDS). Nc\Melbourne\Casea\Patent\63000-63999\P63938.AU.2\Specis\US 60-322261 nat phase au-doc 27/11/08 - 14 EXAMPLE INPUTS Critical nucleation per unit area 120 This value has been density no/mm2 (needed to achieve obtained from sufficient heat transfer rates) experimental dip testing work ) Roll width m 1 Strip thickness mm 1.6 Ladle tonnes t 120 Steel density, kg/m3 7800 Total oxygen, ppm 75 Inclusion density, kg/m3 3000 OUTPUTS Mass of inclusions, kg 21.42857 S Inclusion diameter, m 2.OOE-06 Inclusion volume, m3 0.0 Total no of inclusions 1706096451319381.5 0 Thickness of surface 2 layer, um (one side) Total no of 4265241128298.4536 These inclusions 5 inclusions surface can participate only in the initial nucleation process N:\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Specia\US 60-322261 nat phase au.doc 27/11/08 - 15 Casting speed, m/min 80 Strip length, m 9615.38462 Strip surface area, m2 19230.76923 Total no of nucleating 2307692.30760 sites required ) % of available inclusions 54.10462 that need to participate in the nucleation process )| N:\Melbourne\Cae\Patent\63000-63999\P63938.AU.2\Specie\US 60-322261 nat phase audoc 27/11/08 - 16 APPENDIX 1 List of symbols w = roll width, m t = strip thickness, mm m= steel weight in the ladle, tonne pa = density of steel, kg/m 3 ) pi = density of inclusions, kg/m3 Ot = total oxygen in steel, ppm d = inclusion diameter, m vi= volume of one inclusions, m3 mi= mass of inclusions, kg 5 Nt = total number of inclusions t= thickness of the surface layer, um Na= total number of inclusions present in the surface (that can participate in the nucleation process) u = casting speed, m/min ) La = strip length, m A. = strip surface area, m2 Nreq= Total number of inclusions required to meet the target nucleation density NCt = target nucleation per unit area density, number/mm2 5 (obtained from dip testing) N.,= % of total inclusions available in the molten steel at the surface of the casting rolls for initial nucleation process. 0 Equations mi= (Ot x m, x 0.001)/0.42 Note: for Mn-Si killed steel, 0.42kg of oxygen is 5 needed to produce 1 kg of neclusions with a composition of 30% MnO, 40% Si0 2 and 30% A1 2 0 3 . For Al-killed steel (with Ca injection), 0.38 kg of N:\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Specia\US 60-322261 nat phase au.doc 27/11/08 - 17 oxygen is required to produce 1 kg of inclusions with a composition of 50% A1 2 0 3 and 50% CaO. vi=4.19 x (d/2) 3 (3) Nt--Mi/ (pi x Vi) (4) N,=(2.0 t, x 0.001 x Nt/t) (5) L.=(m. x 1000)/(p. x w x t/1000) (6) A = 2.0 x L. x w Nreq =A, X 106 x NCt (8) Nav % = (Nreq/Na) x 100.0 Eq. 1 calculates the mass of inclusions in steel. Eq. 2 calculates the volume of one inclusion assuming they are spherical. Eq. 3 calculates the total number of inclusions available in steel. 5 Eq. 4 calculates the total number of inclusions available in the surface layer (assumed to be 2 um on each side). Note that these inclusions can only participate in the initial nucleation. 0 Eq. 5 and Eq. 6 used to calculate the total surface area of the strip. Eq. 7 calculates the number of inclusions needed at the 5 surface to meet the target nucleation rate. Eq. 8 is used to calculate the percentage of total inclusions available at the surface which must participate in the Ns\Melbourne\Case\Patent\63000-63999\P63938.AU.2\Specia\US 60-322261 nat phase au.doc 27/11/08 - 18 nucleation process. Note if this number is great than 100%, then the number of inclusions at the surface is not sufficient to meet target nucleation rate. N:\Melbourne\Cases\Patent\63000-63999\P63938.AU.2\Speci8\US 60-322261 nat phase au.doc 27/11/08

Claims

1. A method of making a steel strip by continuous casting comprising the steps of: a. assembling a pair of cooled casting rolls having a nip between them and with confining closures adjacent the ends of the nip; b. introducing molten low carbon steel having a total oxygen content of at least 100 ppm and a free oxygen content between 30 and 50ppm between the pair of casting rolls to form a casting pool between the casting rolls; c. counter rotating the casting rolls and solidifying the molten steel to form metal shells on the surface of the casting rolls with levels of oxide inclusions reflected by the total oxygen content of the molten steel to promote the formation of thin steel strip; and d. forming solidified thin steel strip through the nip of the casting rolls from said solidified shells.

2. A method of making steel strip as claimed in Claim 1, wherein the molten steel in the casting pool has carbon content in the range of 0.001% to 0.01% by weight, a manganese content in the range of 0.01% to 2.0% by weight, and a silicon content in the range of 0.01% to 10% by weight.

3. A method of making a steel strip by continuous casting comprising the steps of: a. assembling a pair of cooled casting rolls having a nip between them and with confining 25909351 (GH Mtter) - 20 closures adjacent the ends of the nip; b. introducing molten steel between the pair of casting rolls to form a casting pool between the casting rolls, the molten steel being a low carbon steel having a carbon content in the range of 0.001% to 0.01% by weight, a manganese content in the range of 0.01 to 2.0% by weight, and a silicon content in the range of 0.01% to 10% by weight and having a total oxygen content of at least 100 ppm; c. counter rotating the casting rolls and solidifying the molten steel to form metal shells on the surface of the casting rolls with levels of oxide inclusions reflected by the total oxygen content of the molten steel to promote the formation of thin steel strip; and d. forming solidified thin steel strip through the nip of the casting rolls from said solidified shells.

4. A method of making steel strip as claimed in Claim 2 or claim 3 wherein the molten steel in the casting pool has an aluminum content on the order of 0.01% or less by weight.

5. A method of making steel strip as claimed any one of the preceding claims, wherein the molten steel in the casting pool has an oxygen content between 100 ppm and 250 ppm.

6. A method of making steel strip as claimed in any one of the preceding claims, wherein the molten steel contains oxide inclusions comprising any one or more of MnO, SiO 2 and A1 2 0 3 distributed through the steel at an inclusion density in the range 2 gm/cm 3 to 4 gm/cm 3 . 25909351 (GHMatters) - 21

7. A method of making steel strip as claimed in any one of the preceding claims, wherein more than a majority of the inclusions range in size between 2 and 12 microns.

8. A method of making steel strip as claimed in any one of the preceding claims, wherein the sulphur content of the molten steel is less than 0.01% by weight.

9. A method of making steel strip as claimed in any one of the preceding claims comprising the additional steps of: e. refining the molten steel in the ladle prior to forming the casting pool by heating a steel charge and slag forming material in the ladle to form molten steel covered by a slag containing silicon, manganese and calcium oxides, stirring the molten steel in the ladle by injecting an inert gas into molten steel to cause desulphurisation, and thereafter injecting oxygen to produce molten steel having the total oxygen content of greater than 100ppm.

10. A method of making steel strip as claimed in Claim 9, wherein the desulphurisation reduces the sulphur content of the molten steel to less than 0.01% by weight.

11. A method of making a thin steel strip as claimed in Claim 9 or claim 10, wherein the solidified steel is a silicon/manganese killed steel and the inclusions comprise any one or more of MnO, SiO 2 and A1 2 0 3 .

12. A method of making a thin steel strip as claimed in any one of Claims 9 to 11, wherein more than a majority of the inclusions range in size between 2 and 12 microns. 2590935_1 (GHtMattrs) - 22

13. A method of making a steel strip as claimed in any one of Claims 9 to 12, wherein the solidified steel has a total oxygen content in the range of 100 ppm to 250 ppm.

14. A thin steel strip produced by twin roll casting to a thickness of less than 5mm and formed of a solidified steel containing solidified oxide inclusions distributed such that at surface regions of the strip to a depth of 2 microns from the surface contain such inclusions to a per unit area density of at least 120 inclusions/mm 2 .

15. A thin steel strip as claimed in Claim 14, wherein the majority of the solidified steel is a silicon/manganese killed steel and the inclusions comprise any one or more of MnO, Si0 2 and A1 2 0 3 .

16. A thin steel strip as claimed in Claim 14 or Claim 15, wherein the majority of the inclusions range in size between 2 and 12 microns.

17. A thin steel strip as claimed in any one of Claims 14 to 16, wherein the solidified steel has an oxygen content reflective of total oxygen content in the range 100 ppm to 250 ppm and a free oxygen content between 30 and 50ppm in the molten steel from which the strip is made.

18. A thin steel strip produced by twin roll casting to a thickness of less than 5 mm and formed of a solidified steel containing oxide inclusions distributed to reflect a total oxygen content in the range 100 ppm to 250 ppm and a free oxygen content between 30 and 50ppm in the molten steel from which the strip is made.

19. A thin steel strip as claimed in Claim 18, wherein the majority of the solidified steel is a silicon/manganese 2590935_1 (GHMattnm) - 23 killed steel and the inclusions comprise any one or more of MnO, SiO 2 and A1 2 0 3 .

20. A thin steel strip as claimed in Claim 18 or Claim 19, wherein the majority of the inclusions range in size between 2 and 12 microns.

21. A method of making a steel strip by continuous casting according to claim 1 or 3 substantially as herein described with reference to the accompanying drawings or Example.

22. A thin steel strip according to claim 14 or 18 substantially as herein described with reference to the accompanying drawings or Example. 2590935_1 (GF*Aattrs)