Claims:
1. A process for production of low carbon Al-killed, batch annealed, deep drawable steel strip, the process comprising the steps of:
subjecting a low-carbon hot-rolled steel strip to cold rolling; and
subjecting the cold rolled steel strip to batch annealing, wherein the batch annealing comprises the steps of:
(i) heating the cold rolled strips to a temperature of about 570°C, wherein rate of heating is about 60°C/hour;
(ii) soaking the heated cold rolled strips for about 30 minutes;
(iii) heating the cold rolled strips obtained from step (ii) to a temperature of about 690°C, wherein rate of heating is about 15°C/hour;
(iv) soaking the heated cold rolled strips obtained from step (iii) for about 30 minutes; and
(v) cooling the cold rolled strips obtained from step (iv) to room temperature to obtain the low carbon Al-killed, batch annealed, deep drawable steel strip,
wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits plastic anisotropy (rm) of at least 2.2.
2. The process as claimed in claim 1, wherein the low-carbon hot-rolled steel strip is prepared by subjecting a low-carbon continuously cast steel slab to hot rolling at a finish rolling temperature (FRT) of 900 + 10°C and coiling temperature (CT) of 540 + 10°C.
3. The process as claimed in claim 1, wherein said low-carbon hot-rolled steel strip comprises, by percentage weight of composition of said strip:
Carbon- 0 to 0.06%;
Manganese- 0.10 to 0.15%;
Sulphur- 0 to 0.010%;
Phosphorous- 0 to 0.025%;
Silicon- 0 to 0.05%;
Aluminum- 0.03 to 0.05%; and
Nitrogen- 30 ppm to 50 ppm, with remainder being iron and impurities.
4. The process as claimed in claim 1, wherein the step of subjecting low-carbon hot-rolled steel strip to cold rolling effects at least 70% cold reduction.
5. The process as claimed in claim 1, wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits total elongation of at least 35%, and wherein said low carbon Al-killed, batch annealed, deep drawable steel strip exhibits uniform elongation of at least 24%.
6. The process as claimed in claim 1, wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits yield strength of at least 190 MPa, and wherein said the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits an ultimate tensile strength of at least 290 MPa.
7. The process as claimed in claim 1, wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits average misorientation angle of about 10°.
8. A process for production of low carbon Al-killed, batch annealed, deep drawable steel strip, the process comprising the steps of:
producing a melt to form a steel comprising, by weight percentages:
Carbon- from about 0 to about 0.06%;
Manganese- from about 0.10 to about 0.15%;
Sulphur- from about 0 to about 0.010%;
Phosphorous- from about 0 to about 0.025%;
Silicon- from about 0 to about 0.05%;
Aluminum- from about 0.03 to about 0.05%; and
Nitrogen- from about 30 ppm to about 50 ppm;
with the remainder being iron and impurities;
forming said melt into a continuously cast steel slab;
heating said slab;
rolling said heated slab at a pre-determined final rolling temperature (FRT);
coiling said rolled slab at a pre-determined coiling temperature (CT) to produce a low-carbon hot-rolled steel strip;
subjecting the low-carbon hot-rolled steel strip to cold rolling; and
subjecting the cold rolled steel strip to batch annealing to prepare low carbon Al-killed, batch annealed, deep drawable steel strip,
wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits plastic anisotropy (rm) of at least 2.2.
9. The process as claimed in claim 8, wherein the pre-determined final rolling temperature (FRT) is 900 + 10°C, and wherein the pre-determined coiling temperature (CT) is about 540 + 10°C.
10. The process as claimed in claim 8, wherein the batch annealing comprises the steps of:
(i) heating the cold rolled strips to a temperature of about 570°C, wherein rate of heating is about 60°C/hour;
(ii) soaking the heated cold rolled strips for about 30 minutes;
(iii) heating the cold rolled strips obtained from step (ii) to a temperature of about 690°C, wherein rate of heating is about 15°C/hour;
(iv) soaking the heated cold rolled strips obtained from step (iii) for about 30 minutes; and
(v) cooling the cold rolled strips obtained from step (iv).
, Description:
FIELD OF THE INVENTION
[0001] The present disclosure generally relates to a process for preparation of low carbon Al-killed batch annealed deep drawable steel. Specifically, the present disclosure relates to a process for preparation of low carbon Al-killed, batch annealed, deep drawable steel strips that exhibits high plastic anisotropy.

BACKGROUND OF THE INVENTION
[0002] Background description includes information that may be useful in understanding the present invention. It is not an admission that any of the information provided herein is prior art or relevant to the presently claimed invention, or that any publication specifically or implicitly referenced is prior art.
[0003] Currently, two basic types of low-carbon steels are used commercially for press forming. These are low-carbon rimmed steels and aluminum-killed steels. The low-carbon rimmed steels are more economical for both the producer and the worker and have better surface characteristics than the aluminum-killed steels; however, they do not have the good deep-drawing properties of aluminum-killed steels and are also prone to strain-aging.
[0004] The press formability of steel sheets is dependent on two properties: the drawability (the ability to draw-in steel from the flange area of a pressed part into the recessed die-cavity of the die) and the stretchability (the ability of the steel to stretch, under biaxial tension, to the contours of a punch and/or die cavity). Drawability is related to the plastic anisotropy of steel sheets.
[0005] A measure of the plastic anisotropy is the plastic-strain ratio, r, which can be determined from sheet tension tests, and which is defined as the ratio of the true width strain to the true thickness strain. For most commercial low-carbon steel sheets, the plastic-strain ratio varies with test direction in the plane of the sheet. The variation of r in the plane of the sheet is termed the planar anisotropy.
[0006] Lately, the deep-drawability of steel sheets has been related to the type and intensity of crystallographic textures, as determined by X-ray techniques. Good deep drawability requires development of pronounced anisotropy. High normal anisotropy (r) values are produced by textures containing a high proportion of grains with (111) planes and low proportion of grains with (100) planes parallel to the sheet surface. Hence, the intensity of these texture components has been used to assess plastic anisotropy and hence predict deep drawability.
[0007] In extra deep drawing steel, aluminium nitride (AlN) plays important role to control the texture of the steel sheet and thereby high r value ( >1.6 with yield strength ~ 180 MPa). Almost every change in chemical and manufacturing conditions leaves a detectable print on the texture and thereby on the plastic anisotropy of the final product. Desirable texture develops only if AlN precipitation occurs before or concurrently with recrystallization during annealing as prior precipitation during hot rolling/after recrystallization destroys texture control. While developing the desirable texture, AlN also helps in formation of a pancake grain structure thereby resulting in better r value, and neutralization of the harmful effect of nitrogen in solid solution as well as enhancement of non-aging properties.
[0008] Although a lot of research has been done so far in the instant technology domain so as to improve and/or tune the drawability of the steel strips/sheets to suit the requirements of the desired application thereof, to the best of our knowledge, there has been no reported process for preparing low carbon Al-killed, batch annealed, deep drawable steel strips that exhibit high plastic anisotropy.
[0009] There is, therefore, a need for a process for preparation of low carbon Al-killed, batch annealed, deep drawable steel strips that exhibit high plastic anisotropy. The present disclosure satisfies the existing needs and provides an improved process for preparing low carbon Al-killed, batch annealed, deep drawable steel strips that exhibit high plastic anisotropy.

OBJECTS OF THE INVENTION
[00010] Primary object of the present disclosure is to provide a process for preparation of low carbon Al-killed, batch annealed, deep drawable steel strips that exhibit high plastic anisotropy.
[00011] Another object of the present disclosure is to provide a process for preparing low carbon Al-killed, batch annealed, deep drawable steel strips that exhibit high plastic anisotropy crystallographic texture with predominance of (111) planes, parallel to the plane of sheet/strip.
[00012] Other objects of the present disclosure will be apparent from the description of the invention herein below.

SUMMARY OF THE INVENTION
[00013] The present disclosure generally relates to a process for preparation of low carbon Al-killed batch annealed deep drawable steel. Specifically, the present disclosure relates to a process for preparation of low carbon Al-killed, batch annealed, deep drawable steel strips that exhibits high plastic anisotropy.
[00014] An aspect of the present disclosure relates to a process for production of low carbon Al-killed, batch annealed, deep drawable steel strip, the process comprising the steps of: subjecting a low-carbon hot-rolled steel strip to cold rolling; and subjecting the cold rolled steel strip to batch annealing, wherein the batch annealing comprises the steps of: (i) heating the cold rolled strips to a temperature of about 570°C, wherein rate of heating is about 60°C/hour; (ii) soaking the heated cold rolled strips for about 30 minutes; (iii) heating the cold rolled strips obtained from step (ii) to a temperature of about 690°C, wherein rate of heating is about 15°C/hour; (iv) soaking the heated cold rolled strips obtained from step (iii) for about 30 minutes; and (v) cooling the cold rolled strips obtained from step (iv) to room temperature to obtain the low carbon Al-killed, batch annealed, deep drawable steel strip, wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits plastic anisotropy (rm) of at least about 2.2.
[00015] In an embodiment, the low-carbon hot-rolled steel strip is prepared by subjecting low-carbon continuously cast steel slab to hot rolling at a finish rolling temperature (FRT) of 900 + 10°C and coiling temperature (CT) of 540 + 10°C. In an embodiment, said low-carbon hot-rolled steel strip comprises, by percentage weight of composition of said strip: Carbon- from about 0 to about 0.06%; Manganese- from about 0.10 to about 0.15%; Sulphur- from about 0 to about 0.010%; Phosphorous- from about 0 to about 0.025%; Silicon- from about 0 to about 0.05%; Aluminum- from about 0.03 to about 0.05%; and Nitrogen- from about 30 ppm to about 50 ppm; with the remainder being iron and impurities. In an embodiment, the step of subjecting low-carbon hot-rolled steel strip to cold rolling effects at least 70% cold reduction. In an embodiment, the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits total elongation of at least 35%, and wherein said low carbon Al-killed, batch annealed, deep drawable steel strip exhibits uniform elongation of at least 24%. In an embodiment, the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits yield strength of at least 190 MPa, and wherein said the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits an ultimate tensile strength of at least 290 MPa. In an embodiment, the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits average misorientation angle of about 10°.
[00016] Another aspect of the present disclosure relates to a process for production of low carbon Al-killed, batch annealed, deep drawable steel strip, the process comprising the steps of: producing a melt to form a steel comprising, by weight percentages: Carbon- from about 0 to about 0.06%; Manganese- from about 0.10 to about 0.15%; Sulphur- from about 0 to about 0.010%; Phosphorous- from about 0 to about 0.025%; Silicon- from about 0 to about 0.05%; Aluminum- from about 0.03 to about 0.05%; and Nitrogen- from about 30 ppm to about 50 ppm; with the remainder being iron and impurities; forming said melt into a continuously cast steel slab; heating said slab; rolling said heated slab at a pre-determined final rolling temperature (FRT); coiling said rolled slab at a pre-determined coiling temperature (CT) to produce a low-carbon hot-rolled steel strip; subjecting the low-carbon hot-rolled steel strip to cold rolling; and subjecting the cold rolled steel strip to batch annealing to prepare low carbon Al-killed, batch annealed, deep drawable steel strip, wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits plastic anisotropy (rm) of at least about 2.2. In an embodiment, the pre-determined final rolling temperature (FRT) is 900 + 10°C, and wherein the pre-determined coiling temperature (CT) is about 540 + 10°C. In an embodiment, the batch annealing comprises the steps of: (i) heating the cold rolled strips to a temperature of about 570°C, wherein rate of heating is about 60°C/hour; (ii) soaking the heated cold rolled strips for about 30 minutes; (iii) heating the cold rolled strips obtained from step (ii) to a temperature of about 690°C, wherein rate of heating is about 15°C/hour; (iv) soaking the heated cold rolled strips obtained from step (iii) for about 30 minutes; and (v) cooling the cold rolled strips obtained from step (iv) to room temperature.
[00017] Various objects, features, aspects and advantages of the inventive subject matter will become more apparent from the following detailed description of preferred embodiments, along with the accompanying drawing figures in which like numerals represent like components.

BRIEF DESCRIPTION OF THE DRAWINGS
[00018] The following drawings form part of the present specification and are included to further demonstrate certain aspects of the present disclosure, the inventions of which can be better understood by reference to one or more of these drawings in combination with the detailed description of specific embodiments presented herein.
[00019] FIG. 1 illustrates schematic representation of batch annealing cycle, in accordance with embodiments of the present disclosure.
[00020] FIG. 2A and 2B illustrate ODF sections at f2 = 0o and f2 = 45o of the annealed sample on the RD-TD plane, respectively, in accordance with an embodiment of the present disclosure.

DETAILED DESCRIPTION OF THE INVENTION
[00021] The embodiments herein and the various features and advantageous details thereof are explained more comprehensively with reference to the non-limiting embodiments that are detailed in the following description. Descriptions of well-known components and processing techniques are omitted so as to not unnecessarily obscure the embodiments herein. The examples used herein are intended merely to facilitate an understanding of the ways in which the embodiments herein may be practiced and to further enable those of skill in the art to practice the embodiments herein. Accordingly, the examples should not be construed as limiting the scope of the embodiments herein.
[00022] Unless otherwise specified, all terms used in disclosing the invention, including technical and scientific terms, have the meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. By means of further guidance, term definitions may be included to better appreciate the teaching of the present invention.
[00023] As used in the description herein, the meaning of “a,” “an,” and “the” includes plural reference unless the context clearly dictates otherwise. Also, as used in the description herein, the meaning of “in” includes “in” and “on” unless the context clearly dictates otherwise.
[00024] As used herein, the terms “comprise”, “comprises”, “comprising”, “include”, “includes”, and “including” are meant to be non- limiting, i.e., other steps and other ingredients which do not affect the end of result can be added. The above terms encompass the terms “consisting of” and “consisting essentially of”.
[00025] As used herein, the terms “composition” “blend,” or “mixture” are all intended to be used interchangeably.
[00026] The terms “weight percent,” “wt-%,” “percent by weight,” “% by weight,” and variations thereof, as used herein, refer to the concentration of a substance as the weight of that substance divided by the total weight of the composition and multiplied by 100. It is understood that, as used here, “percent,” “%,” and the like are intended to be synonymous with “weight percent,” “wt-%,” etc.
[00027] The term “strip” used herein, through the present disclosure, includes within its scope, strips, sheets and the like products with desired dimensions to suit their applications, as known to or appreciated by a person skilled in the pertinent art.
[00028] The present disclosure generally relates to a process for preparation of low carbon Al-killed batch annealed deep drawable steel. Specifically, the present disclosure relates to a process for preparation of low carbon Al-killed, batch annealed, deep drawable steel strips that exhibits high plastic anisotropy.
[00029] An aspect of the present disclosure relates to a process for production of low carbon Al-killed, batch annealed, deep drawable steel strip, the process comprising the steps of: subjecting a low-carbon hot-rolled steel strip to cold rolling; and subjecting the cold rolled steel strip to batch annealing, wherein the batch annealing comprises the steps of: (i) heating the cold rolled strips to a temperature of about 570°C, wherein rate of heating is about 60°C/hour; (ii) soaking the heated cold rolled strips for about 30 minutes; (iii) heating the cold rolled strips obtained from step (ii) to a temperature of about 690°C, wherein rate of heating is about 15°C/hour; (iv) soaking the heated cold rolled strips obtained from step (iii) for about 30 minutes; and (v) cooling the cold rolled strips obtained from step (iv) to room temperature to obtain the low carbon Al-killed, batch annealed, deep drawable steel strip, wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits plastic anisotropy (rm) of at least 2.2.
[00030] In an embodiment, the low-carbon hot-rolled steel strip is prepared by subjecting low-carbon continuously cast steel slab to hot rolling at a finish rolling temperature (FRT) of 900 + 10°C and coiling temperature (CT) of 540 + 10°C. In an embodiment, said low-carbon hot-rolled steel strip comprises, by percentage weight of composition of said strip: Carbon- from about 0 to about 0.06%; Manganese- from about 0.10 to about 0.15%; Sulphur- from about 0 to about 0.010%; Phosphorous- from about 0 to about 0.025%; Silicon- from about 0 to about 0.05%; Aluminum- from about 0.03 to about 0.05%; and Nitrogen- from about 30 ppm to about 50 ppm; with the remainder being iron and impurities. In an embodiment, the step of subjecting low-carbon hot-rolled steel strip to cold rolling effects at least 70% cold reduction. In an embodiment, the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits total elongation of at least 35%, and wherein said low carbon Al-killed, batch annealed, deep drawable steel strip exhibits uniform elongation of at least 24%. In an embodiment, the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits yield strength of at least 190 MPa, and wherein said the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits an ultimate tensile strength of at least 290 MPa. In an embodiment, the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits average misorientation angle of about 10°.
[00031] Another aspect of the present disclosure relates to a process for production of low carbon Al-killed, batch annealed, deep drawable steel strip, the process comprising the steps of: producing a melt to form a steel comprising, by weight percentages: Carbon- from about 0 to about 0.06%; Manganese- from about 0.10 to about 0.15%; Sulphur- from about 0 to about 0.010%; Phosphorous- from about 0 to about 0.025%; Silicon- from about 0 to about 0.05%; Aluminum- from about 0.03 to about 0.05%; and Nitrogen- from about 30 ppm to about 50 ppm; with the remainder being iron and impurities; forming said melt into a continuously cast steel slab; heating said slab; rolling said heated slab at a pre-determined final rolling temperature (FRT); coiling said rolled slab at a pre-determined coiling temperature (CT) to produce a low-carbon hot-rolled steel strip; subjecting the low-carbon hot-rolled steel strip to cold rolling; and subjecting the cold rolled steel strip to batch annealing to prepare low carbon Al-killed, batch annealed, deep drawable steel strip, wherein the low carbon Al-killed, batch annealed, deep drawable steel strip exhibits plastic anisotropy (rm) of at least about 2.2. In an embodiment, the pre-determined final rolling temperature (FRT) is 900 + 10°C, and wherein the pre-determined coiling temperature (CT) is about 540 + 10°C. In an embodiment, the batch annealing comprises the steps of: (i) heating the cold rolled strips to a temperature of about 570°C, wherein rate of heating is about 60°C/hour; (ii) soaking the heated cold rolled strips for about 30 minutes; (iii) heating the cold rolled strips obtained from step (ii) to a temperature of about 690°C, wherein rate of heating is about 15°C/hour; (iv) soaking the heated cold rolled strips obtained from step (iii) for about 30 minutes; and (v) cooling the cold rolled strips obtained from step (iv) to room temperature.
[00032] According to certain embodiments of the present disclosure, while carbon increases steel strength, it reduces the cold workability, r-value and deep drawability of cold-rolled steel sheet remarkably and thus the higher limit of the cold rolled sheet is set at 0.1 wt%. For improving the r-value i.e. drawability, it is desirable to reduce the carbon level less than 0.06 wt%. Lowering the carbon content below 0.025 wt% results in poor ageing property since below 0.025 wt% steel is in complete a-ferrite region in Iron-Cementite phase diagram resulting no cementite formation. Consequently, more free carbon will be available in steel matrix which deteriorates the ageing property. Keeping low carbon <0.025 % also requires vacuum degassing the molten steel which adds to cost of production. To avoid that, the carbon level is preferably maintained between 0.025-0.06 wt%.
[00033] Major advantage in low carbon grade is that it scavenges off the N by forming AlN precipitate which improves drawability by reducing interstitial N and by promoting the formation of (111) type of texture during batch annealing hence, facilitating the drawability and high r-values. Availability of Al/N ratio more than 8 ensures sufficient AlN precipitation during batch annealing to improve ageing properties and Al/N ratio less than 12 ensure very less remaining Al in the solid solution which deteriorate the drawability. In addition, higher Al content of more than 0.05 % may deteriorate the cleanliness of the steel during casting due to formation of unavoidable oxide Al2O3 inclusions which deteriorates the surface properties. Thus, the upper value is limited to 0.05%. When better drawability is required, it is desirable to restrict the acid soluble aluminum content to less than 0.05%, and preferably between 0.03-0.05%.
[00034] According to certain embodiments of the present disclosure, coiling temperature is kept between 540 + 100C to avoid AlN precipitation before batch annealing as sufficient time is provided to precipitate out AlN during annealing and hence, no prior precipitation is needed. AlN helps in formation of pancake grain structure and development of desired texture for formability.
[00035] The following examples are included to demonstrate preferred embodiments of the invention. It should be appreciated by those of skill in the art that the techniques disclosed in the examples which follow represent techniques discovered by the inventor to function well in the practice of the invention, and thus can be considered to constitute preferred modes for its practice. However, those of skill in the art should, in light of the present disclosure, appreciate that many changes can be made in the specific embodiments which are disclosed and still obtain a like or similar result without departing from the spirit and scope of the invention.
Examples
Example 1
[00036] Low-carbon, industrially made hot-rolled steel of following composition (Table 1) was cold rolled to 1mm thickness in laboratory experimental cold rolling mill with 72% cold reduction. Finish rolling temperature and coiling temperature of industrially hot rolled steel were 900 + 10 °C and 540 + 10 °C.
Table 1: Chemical composition (wt %) of low carbon Al-killed batch annealed steel
C Mn S P Si Al N(ppm)
~0.03 ~0.12 ~0.007 ~0.019 ~0.03 ~0.038 ~39
[00037] Tensile samples prepared from cold rolled sheets were subjected to batch annealing simulations in prototype simulator. Samples were heated to 5700C with heating rate of 600C/hour and soaked for half an hour for diffusion of aluminium and aluminium nitride precipitation as shown schematically in Figure 1. Subsequently, samples were heated to 6900C with heating rate of 150C/hour and soaked for half an hour for recrystallisation. Formability of fully recrystallized steels was good and suitable for component stamping. Un-recrystallized steels had very limited formability and were suited for simple bending or roll forming operations only.
[00038] Samples after conducting batch annealing experiment were subjected to detailed characterization with respect to mechanical properties evaluation and texture examination, using electron back scattered diffraction (EBSD). Excellent combination of properties was achieved as depicted in Table 2.
Table 2: Mechanical properties of low carbon Al-killed batch annealed steel
YS,
MPa UTS,
MPa %
Total El %
Uniform El YS/UTS rm
196 300 49 28 0.65 2.45
[00039] Cold rolled samples after being subjected to batch annealing cycle, in accordance with an embodiment of the present disclosure, exhibited good strength values with respect to yield strength (YS) and tensile strength (UTS) with a very high uniform and total elongation values (El). Plastic anisotropy (rm) was found to be as high as 2.45 and excellent combination of strength & ductility were achieved. The unique batch annealing cycle of the present disclosure resulted into strong gamma fibre and thereby very high plastic anisotropy (rm) to the level of 2.45; reported for the first time in EDD steel and in fact are comparable to that of IF/IF-HS.
[00040] With the grain structure, it was visible that the grains were recrystallized and underwent grain growth preferentially along the longitudinal direction. Figure 2 represents the orientation distribution function (ODF) section at f2= 00 and f2=450 on the RD-TD plane of the annealed samples which clearly shows evidence of strong gamma fibre. The average misorientation angle in steel was found to be low (10o) which implied that the grain structure was pancaked, which is also evident from the inverse pole figure (IPF) maps.
[00041] The foregoing description of the specific embodiments will so fully reveal the general nature of the embodiments herein that others can, by applying current knowledge, readily modify and/or adapt for various applications such specific embodiments without departing from the generic concept, and, therefore, such adaptations and modifications should and are intended to be comprehended within the meaning and range of equivalents of the disclosed embodiments. It is to be understood that the phraseology or terminology employed herein is for the purpose of description and not of limitation. Therefore, while the embodiments herein have been described in terms of preferred embodiments, those skilled in the art will recognize that the embodiments herein can be practiced with modification within the spirit and scope of the embodiments as described herein.

ADVANTAGES OF THE INVENTION
[00042] The present disclosure provides a process for preparation of low carbon Al-killed, batch annealed, deep drawable steel strips that exhibit high plastic anisotropy.
[00043] The present disclosure provides a process for preparing low carbon Al-killed, batch annealed, deep drawable steel strips that exhibit high plastic anisotropy crystallographic texture with predominance of (111) planes, parallel to the plane of sheet/strip.