FORM 2
THE PATENT ACT 1970
(39 OF 1970)
&
The Patent Rules, 2003

COMPLETE SPECIFICATION
(See Section 10 and Rule 13)
1 TITLE OF THE INVENTION :
COLD ROLLED ULTRA-HIGH STRENGTH STEEL SHEET WITH IMPROVED HOLE EXPANSION AND METHOD OF ITS MANUFACTURING.
2 APPLICANT (S)
Name : JSW STEEL LIMITED.
Nationality : An Indian Company incorporated under the Companies Act, 1956.
Address : JSW CENTRE,
BANDRA KURLA COMPLEX,
BANDRA(EAST),
MUMBAI-400051,
MAHARASHTRA,INDIA.
3 PREAMBLE TO THE DESCRIPTION
COMPLETE
The following specification particularly describes the invention and the manner in which it is to
be performed.

FIELD OF THE INVENTION
The Present invention relates to cold rolled high strength steel sheet having excellent hole expansion and strain hardening property and method of manufacturing the same. The steel sheets have Tensile strength of 1000 MPa or more involving selective chemical composition and processing to achieve the desired microstructure and the stretch formability property. The advancement favors generation of cold rolled high strength steel sheet having Yield strength of 600MPa or more, Tensile strength of 1000 MPa or more, total elongation of 14% or more, strain hardening coefficient of 0.12 or more and hole expansion ratio of 30 %or more and crash resistance which makes such steel sheets suitable for automobile applications. The present advancement also concerns achieving better hole expansion and without thickness variations during cold rolling which resulted because of selective steel microstructure and cold rolling parameters which follow the differential equation, δY*W*((R*Δh)^1/2+R*Δh*Ra/2hav)) <= 100.
BACKGROUND OF THE INVENTION
There is an increased attention to light weighing, reliability in product performance and passenger safety in automotive segment. To boot, the stringent emission norms has triggered the automakers to speed up the programs to reduce vehicle weight for higher fuel efficiency and better environmental performance. This can be achieved by incorporating thinner high strength steel sheet having strength more than 1000 MPa in place of conventional one. Conversely, increasing strength of steel through higher amount of alloying results in poor drawability and surface appearance. As a result, high strength steel sheet are not recommended to be used for automotive body parts requiring high amount of drawability and superior surface appearance. In recent years, many high strength steels have been tried conventionally with the aim of reducing the vehicle weight and increasing the strength of the auto body to ensure safety.

Formability is a major limitation which restricts the application of high strength steel in automotive body parts having complex profile. Through improving the strain hardening coefficient better formability can be achieved. To facilitate, ferrite-Bainite Materials has been utilized where bainite, retained austenite and Tempered martensite in ferrite matrix results in excellent hole expansion. However, the optimum deployment of said steel can only be achieved by right combination of retained austenite, bainite and martensite phase fractions and their distribution. In order to achieve the said high Hole Expansion Ratio, Si and Al are added to get the desired amount of retained austenite and Bainite at room temperature. To avoid crack generation during press forming, the high strength steel sheet having strength >1000 MPa must also exhibit a good strain hardening coefficient (n-value) of atleast 0.12 along with total elongation of no less than 14 %and Hole Expansion ratio from 30 to 50%.
As a part of prior art , the Chinese patent application number CN102471849A discloses method of manufacturing a cold rolled steel sheet with minimum UTS of 980 MPa and its process for automotive structural component. A high strength automotive steel sheet is disclosed, obtained by balancing bainite and martensite volume fraction percentage .However, the method disclosed in prior art fall short in getting good total elongation and n value due to higher amount of 50% or more martensite phase fraction as strengthening phase.
Japanese patent application numberJP20063274417A discloses a
High strength cold rolled sheet steel having excellent balance of
strength and workability, and metal plated steel strip method
comprising Bainitic ferrite 70% or more;

Residual austenite is 5% to 20%. A good combination of strength and workability has been claimed as a part of invention. However, due to presence of high proportion of bainite, strength deteriorates. However, CO2 emissions regulations in recent years have become increasingly stringent, weight reduction of the vehicle body is further demanded , in automotive component like cross member and pillars, workability with low strength of 780MPa will not result in weight reduction and hence inorder to doso, strength needs to be increased to actively reduce the weight.
The present invention thus attempts to overcome the above mentioned problems and limitations of the prior art by way of providing a high-strength cold-rolled steel sheet with minimum tensile strength of 1000MPa, and total elongation more than 14% having improved strain hardening properties along with uniform thickness along the length as well as width and a process for its manufacture.
OBJECTS OF THE INVENTION
The basic object of the present invention is directed to provide cold rolled ultra high strength steel sheet having excellent strain hardening property, surface quality and method of manufacturing the same.
A still further object of the present invention is directed to provide cold rolled ultra high strength steel sheet involving selective composition to achieve the desired microstructure and the stretch formability property.
A still further object of the present invention is directed to provide cold rolled ultra high strength steel sheet having tensile strength 1000 MPa or more, a good strain hardening coefficient (n-value) of atleast 0.12

along with high total elongation of no less than 14 %,and Hole Expansion ration more than 30%.
A still further object of the present invention is directed to provide cold rolled ultra high strength steel sheet with uniform thickness along width and length of the coil by involving selective Work roll diameter and work roll roughness.
SUMMARY OF THE INVENTION
The basic aspect of the present invention is directed to provide Cold
rolled ultra-high strength steel sheets having tensile strength atleast
1000 MPa with composition in terms of weight % comprising:
C: 0.16-0.2 %;
Mn: 2.0-2.5 %;
Si: 0.96–1.0%;
Al: 0.12-0.5%
S: 0.005 % or less;
N: 0.005 % or less
Ti: 0.005-0.05%;
Mo: 0.02-0.08%;
and the balance being Fe and other unavoidable impurities; wherein
[Si] / [Al] ratio is in a range of 2 to 8 and having selective steel
microstructure constituents including atleast 20% Bainite phase,
Tempered Martensite from 1 to 5% and Retained Austenite from 5 to
10% in ferrite matrix for excellent hole Expansion ratio.
A still further aspect of the present invention is directed to said cold rolled ultra high strength steel sheets wherein said steel microstructure constituents comprise 20 % or more of bainite, 5 % or less of martensite phase, 5 % or more of retained austenite phase and balance being ferrite phase along with carbide, nitride and sulphide.

A still further aspect of the present invention is directed to said Cold rolled ultrahigh strength steel sheet comprising atleast one type of element selected from the group of elements consisting of Ca, Zr, Va, W and Cr in amount less than 0.04 wt%.
A still further aspect of the present invention is directed to said cold rolled ultrahigh strength steel sheet additionally comprising in terms of weight % atleast one element selected from the group consisting of 0.002 % to 0.2 % Cu and 0.002 % to 0.2 % Ni.
Another aspect of the present invention is directed to said cold rolled ultrahigh strength steel sheets having Yield strength of 600 MPa or more, Tensile strength of 1000 MPa or more, total elongation of 14% or more, strain hardening coefficient of 0.12 or more and Hole Expansion Ratio of 30 %or more.
A further aspect of the present invention is directed to a process for manufacturing the cold rolled ultra high strength steel sheets as described above having tensile strength of atleast 1000 MPa comprising the steps of:
a) providing steel having composition comprising
C: 0.16-0.2 %;
Mn: 2.0-2.5 %;
Si: 0.96–1.0%;
Al: 0.12-0.5%
S: 0.005 % or less;
N: 0.005 % or less
Ti: 0.005-0.05%;
Mo: 0.02-0.08%;
and the balance being Fe and other unavoidable impurities;
involving processing through Heat from basic oxygen furnace
(BOF) and RH degasser and subsequently continuously casting

into slabs and reheating said slabs having said composition to reheating temperature in the range from 1190°C -1250 °C;
b) said reheated slabs being subjected to roughing rolling in roughing mill with roughing mill delivery temperature of 1080°C or less;
c) Said rough rolled steel being subjected to finish rolling with finish mill exit temperature ranging from Ac3°C to Ac3+100 °C.
A still further aspect of the present invention is directed to said process further comprising the steps of:
a) Coiling the finish rolled steel with average run out table cooling rate of 9 °C/second or more;
b) Acid pickling the Cold rolling the said hot rolled steel sheet with cold reduction of atleast 35%; and it shall follow the following differential equation
δY*W*((R*Δh)^1/2+R*Δh*Ra/2hav)) <= 100, where δY- Change in HR Yield Strength, W-width of strip, R- Radius of work roll, Δh=Change in strip Thickness, Ra- Work Roll Roughness and hav=(hi+hf)/2, where hi=initial thickness and hf=final thickness.
c) Subjecting said cold rolled sheet to continuous annealing with
selective parameters followed by skin passing.
A still further aspect of the present invention is directed to said process wherein cold rolled steel is subjected to said continuous annealing following the steps comprising:
a) annealing the cold rolled steel sheet by heating at the rate of 0.5-5 0C/sec up to soaking section critical temperature range from 800 °C to 850 °C with residence time ranging from 70 to 150 seconds;
b) slow cooling the steel at cooling rate in the rage from 0.2 to 3°C/sec up to a temperature in the range from 680°C to 720 °C after soaking ;

c) rapid cooling the steel from SCS temperature up to a temperature range of 420 °C to 500 °C at a critical cooling rate of 40°C/sec or less.
d) overaging the said steel in the temperature range starting from 380 °C to 420 °C or more with residence time of 250 to 560 seconds wherein,
e) Subjecting the over-aged steel to skin pass elongation of 0.20 to 1%.
The above objects and advantages of the present invention are described hereunder in details with reference to non-limiting accompanying Figure and examples:
BRIEF DESCRIPTION OF THE ACCOMPANYING FIGURE
Figure 1: illustrates the microstructure of the high strength cold rolled
steel according to present invention.
DETAILED DESCRIPTION OF THE INVENTION WITH REFERENCE TO ACCOMPANYING FIGURE
The Present invention relates to cold rolled ultra high strength steel sheet having Tensile strength 1000 MPa or more and composition in terms of weight percent comprising: C: 0.16-0.2 %; Mn: 2.0-2.5 %; Si: 0.96–1.0%; Al: 0.12-0.5%; S: 0.005 % or less; N: 0.005 % or less; Ti: 0.005-0.05%; Mo: 0.02-0.08%; and the balance being Fe and other unavoidable impurities; wherein [Si] / [Al] ratio is in a range of 2 to 8 and having selective steel microstructure constituents including atleast 20% Bainite phase, Tempered Martensite from 1 to 5% and Retained Austenite from 5 to 10% in ferrite matrix for excellent hole Expansion ratio.
Cold rolled ultra high strength steel sheet obtained according to present invention having Yield strength of 600 MPa or more, Tensile

strength of 1000 MPa or more, total elongation of 14% or more, strain
hardening coefficient of 0.12 or more and Hole Expansion Ratio of 30
%or more.
Following abbreviations, terminologies and expressions are used to
describe the manner of implementation of the present invention:
CAL – Continuous annealing Line
RCS -Rapid cooling section
OAS- Over-aging Section
CS - Center Speed
SRT -Slab Reheating Temperature
FET- Finishing Mill Entry Temperature
FT-Finishing Temperature
CT- Coiling Temperature
HER–Hole Expansion Ratio
Ac1 & Ac3 – Critical temperatures in iron-carbide diagram
El – Elongation (%)
UTS - Ultimate Tensile Strength (MPa)
YS - Yield Strength (MPa)
SPM - Skin Pass Elongation (%)
A Cold rolled ultra High strength steel sheet having excellent strain hardening property according to present invention, its chemical compositions and method of manufacturing are described hereunder with explanation on metallurgical factors deciding the range of constituents in a composition according to a preferred embodiment wherein all the elements are in weight % as follows:
Carbon (C: 0.16-0.2 wt %) – Carbon effectively increases the hardenability and strength of steel. It also lowers the transformation temperature; hence more austenite forms during soaking of steel. In addition, Carbon also lowers the martensite finish temperature, which stabilize austenite phase at room temperature. However, to utilize the

TRIP phenomenon at least 0.12 weight % of C is required. More preferably, the amount of carbon must be more than 0.16 to make austenite stable and to effectively lower the Martensite start temperature. On the other hand, increasing the carbon content above 0.2 % deteriorates the weldability and fatigue resistance. Also, with higher carbon, the austenite becomes too stable to be transformed to martensite during forming which results in poor strain hardenability. With these limitations, upper limit of carbon is 0.2 %.
Manganese (Mn: 2.0-2.5wt %) - Similar to C, Mn is an austenite stabilizer .Mn increases the hardenability of steel by lowering Ms Temperature. It also assists in partitioning of C more to austenite and hence makes Austenite more stabilized. In order to attain the desired amount of solid solution strengthening to achieve UTS>1000 MPa, minimum amount of Mn must be atleast 2%. However, an increase in manganese concentration restricts the fraction of bainite that can form. Higher Mn weight percent may also lead to higher martensite fraction resulting in lower strain hardening effect. Hence, the upper limit of Mn is 2.5 %.
Silicon (Si: 0.96–1.0wt %) –Si suppresses precipitation of cementite, therefore, it helps in enrichment of carbon in austenite and make it more stable. Si as a solid solution strengthening element strengthens the ferrite, matrix. To attain that effect and to get minimum UTS>1000 MPa, minimum amount of Si must be atleast0.96wt%. However, increasing Si level more than 1.0 % does not cause any significant effect to inhibit cementite formation. In addition, adding excess Si deteriorates the surface. Hence, the upper Sicontent must not be more than 1.0 %.
Aluminium (Al: 0.12-0.5wt%)-Like Si, Al also suppresses the cementite precipitation and in this way it can be used as a replacement

for Si. However, Al does not strengthen the ferrite matrix, hence more Mn need to be added to achieve the desired strength level. Al also acts as a deoxidizer during steel making process to kill dissolved oxygen. To achieve adequate deoxidation, the soluble aluminum (Al Sol.) preferably be at least 0.02 %. Al also adds on to fix harmful dissolve N to form AlN. Increasing Al level above 0.5 wt% to replace Si causes clogging at sub-entry nozzle problems during continuous casting. Accordingly, upper limit is set to 0.5%.
Titanium (Ti: 0.005-0.05%)- Ti acts as a nitrides forming element to fix solute N in steel thus helps in getting aging resistance. Formability of steel sheet improves by reducing solute N in solution with Ti instead of Al. And so, Amount of Ti preferably added should be 0.01 wt% or more. However, when Ti contents exceeds 0.05 wt%, the effects are saturated, therefore the amount of Ti is made to be 0.05% or less. when Ti is added in excess of the amount required for reducing solid solution N, excessive TiC may form, which inhibits the stable formation of second phase, which is not preferable .
Molybdenum (Mo: 0.02-0.08 wt %) – Mo as carbide former strengthens the ferrite matrix by formation of nano sized MoC precipitates. For achieving the said benefits, minimum amount of Mo must be above 0.02 %. Mo also refines the grain size and improves the strength. However, excess addition of Mo results in coarse carbide formation which reduces the elongation. Also, excessive Mo addition result in lower carbon fraction in austenite and reduces its stability. Accordingly, upper limit of Mo is set 0.08 %.
Nitrogen (N: 0.005 wt% or less) – N is present in steel as an impurity and should be present at minimum amount to avoid aging. In addition, to achieve good aging resistance, upper limit of N must be 0.005 wt % or less.

Ca, Zr, V, W and Cr (collectively <0.04 wt%): Ca, Zr, V, W and Cr forms carbide and impart precipitation strengthening to the steel. However as Mo is already added, any additional content more than 0.04 of each element will add up to cost of production. Moreover, higher addition of this element will form coarser carbides, reducing elongation. Formation of excess carbide also leads to lower carbon fraction in austenite and reduces its stability. Accordingly, upper limit of at least one of the element selecting from Ca, Zr, V, W and Cr must be less than 0.04 wt%.
Method of evaluating hole expansion ratio: The hole expansion ratio (HER %) is significant to assess the stretch flangeability of steel sheets. It is acquired by the hole expansion test utilizing conical or cylindrical punch in forming test machine. Whole expansion tests were performed as per ISO 16630-2009 utilizing forming test machine. Samples having a pouched hole of 10mm diameter were used for the test. Conical punch having an angle of 600 and cylinder diameter 50 mm was used. The punching speed of the conical punch during hole expansion was 0.3 mm/s. The conical punch was moved up against the sample with 10mm hole until the small crack appeared at the edge of hole and detected by optical instrument. The final average diameter of the hole after the small crack appeared was determined by measuring in two directions. Test were repeated for four to five times for each steel numbers and average HER% was taken with the following standard equation -
HER% = [(Df- Do)/ D0]X100
Where Do = Initial hole diameter, Df = final hole diameter before crack.
Description of the process of manufacturing:

To achieve Slab chemistry as described in scope of the invention, Heat from basic oxygen furnace (BOF) is processed through RH degasser and subsequently continuously casted. Special measures are taken to hot roll resulted slabs by keeping slab reheating temperature in the range of 1190°C to 1250°C intended to control roughing mill delivery temperature under 1080°C and finishing mill entry temperature under 1080°C to check surface defects like rolled in scale. During hot rolling, finishing mill temperature is varied in the range from Ac3 °C to Ac3+100 °C. After finish rolling, Run out table cooling rate from finishing mill to coiler of more than 9 0C/sec was maintained to achieve coiling temperature range of 530 to 630 °C, to avoid ID collapse after coil winding, it is held for 120sec at mandrel. Hot rolled coils were subsequently processed through pickling coupled with tandem cold rolling mill to remove the oxide surface present in the surface and to provide selective cold reduction of 35% or more, work roll diameter less than 430 mm, work roll Ra less than 0.5 so that it shall follow the following differential equation
δY*W*((R*Δh)^1/2+R*Δh*Ra/2hav)) <= 100, where δY- Change in HR Yield Strength, W-width of strip, R- Radius of work roll, Δh=Change in strip Thickness, Ra- Work Roll Roughness and hav=(hi+hf)/2, where hi=initial thickness and hf=final thickness.
Subsequent to pickling and cold rolling to desired thickness, cold rolled steel strip are processed through continuous annealing line where electrolytic cleaning removes rolling emulsion present on the surface. Cleaned surface passes through the preheating and heating section where the strip is heated at the rate of 0.5-5 0C/sec up to soaking section temperature. Soaking section temperature was maintained in the range from 800 °C to 850 °C to achieve retained austenite in final microstructure. Annealing time is kept in the range from 70 to 150 seconds to allow sufficient time for annealed and homogenization of austenite microstructure. After soaking section steel strip passes

through slow cooling section at cooling rate in the rage from 0.2 to 3 °C/sec. Slow cooling section temperature is kept in the range from 680 to 720 °C to avoid any pearlite formation during cooling. Following slow cooling section, annealed strip sheet passes through rapid cooling section at cooling rate of 40˚Cor less and cooled up to rapid cooling section temperature of 420 °C or more. This is to keep martensite area fraction in microstructure less than 2 %. Subsequent to RCS, annealed strip passes through over aging section(OAS) where rapid cooled steel strip is over aged keeping the over aging section temperature in between of 380 to 420˚C. Over aged steel sheet is then provided with skin-pass elongation in the range from 0.20 to 1 % to avoid yield point elongation.
Complete description of steel according to the present advancement and comparative steel grades are illustrated in following table 1 to table 4 and the weight percent range of constituents and the selective process parameters according to the invention are validated through following examples 1a, 1b & 6:
Table 1: Elemental Compositions in weight % of the inventive steel sheets along with comparative example.
Table 2: Hot rolling and cold rollingof inventive with comparative steel sheets having chemical compositions as per Table 1.
Table 3: CAL Parameters of inventive with comparative steel sheets having chemical compositions as per Table 1.
Table 4:Mechanical properties, HER % and micro structural phase fractions of inventive and comparative steels having chemical composition as per table 1 and being processed as per Table 2 and Table 3.

Table 1

Chemical Composit on in %
Sample No C MN S P SI AL N TI [Si]/[Al] Mo Other Elements Remarks
1a 0.16 2 0.003 0.021 0.96 0.12 0.004 0.025 8 0.02 Ca-0.002,
Zr-0.003,
V-0.02, Cr-
0.01 I
1b 0.16 2 0.003 0.021 0.96 0.12 0.004 0.025 8 0.02 Zr-0.003, I
2 0.2 2.5 0.003 0.021 1 0.5 0.004 0.05 2 0.08 V-0.02, Cr-0.01 C
3 0.08 2.6 0.003 0.015 03 0.03 0.003 0.02 10 0.03 C
4 0.08 2.9 0.003 0.01 03 0.03 0.003 0.02 10 0.015 C
5 0.06 12 0.005 0.02 02 0.05 0.006 - 8.3 0.03 C
6 0.2 2.5 0.005 0.02 1 0.5 0.004 0.05 2 0.07 I
*I - Present inventive example, C- Comparative Examples *Underline boxes indicates “outside the appropriate range” Example 1
It can be appreciated from Table 1 to Table 4 that steel sheets remarked as “I” are satisfying all the scopes of present invention and exhibits excellent strain hardening property, HER% and free from gauge Variation along the length. These steels exhibits improved n value>0.1, HER %> 30, yield ratio of >0.6, UTS ≥1000MPa and Yield strength more than 600MPa. Whereas, Steel remarked as 2 from Table 1 to Table 4 doesn’t comply with atleast one of the scope of the present invention and does not conform with minimum one or more of the end product attributes as mentioned in the scope of the present invention. For example steel no. 3 to 5 in table 1 has the less carbon % than the scope and does not comply with required ratio of Si/Al ratio and has poor Hole Expansion Ratio and less n value.
Table 2

Hot Rolling Parameters Cold Rolling Parameters
Sampl e No SRT˚ C Roughi ng Mill temp˚C FT˚ C CTC Cold Reducti on % δY( MP a) WR Ra R (mm) Eq1=
δY*W*((R*Δh)^ 1/2+R*Δh*Ra/2 hav)) (Ton) Gauge Variations

1a 1205 1075 903 558 40 100 0.4 210 61 No Gauge Variations
1b 1205 1075 903 558 59 100 1.2 250 153 GV observed
2 1220 1070 908 570 45 100 0.4 220 63 No Gauge Variations
3 1210 1080 910 560 50
4 1190 1065 915 570 50
5 1200 1085 900 560 47
6 1205 1075 903 558 40 100 0.4 210 61 No Gauge Variations
*I - Present inventive example, C- Comparative Examples, GV- Gauge Variation, ER- Work Roll
EQ1= δY*W*((R*Δh)^1/2+R*Δh*Ra/2hav)) (Ton)<=100where δY- Change in HR Yield Strength, W-width of strip, R- Radius of work roll,Δh=Change in strip Thickness, Ra- Work Roll Roughness and hav=(hi+hf)/2, where hi=initial thickness and hf=final thickness.
Note: Steel marked as 1a and 1b have the same chemical composition as steel number 1, and however they are processed at different conditions to validate the claimed process. In steel no 1b is processed with high work roll Ra-1.2, higher Work roll diameter and not satisfying EQ1were Gauge Variations are observed as shown in Table2 whereas in 1a and 2 sample Work roll Ra and Work roll diameter maintained as per claim and satisfying EQ1 where no gauge variations are observed.
In sample no 1a and 1b the Rapid cooling temperature is varied in 1a temperature is 443˚C where retained austenite formed is 5% and n value is greater than 0.12 whereas in sample 1b where rapid cooling temperature is 380˚C where retained austenite formed is 0% and n value is 0.120 less than required value.
In sample 3 4 and 5 where carbon percentage is less than 0.1%,where RCS temperature is less than 420 and OAS temperature is less than 380 where percentage of martensite formed is more than desired level and results in less n value and Hole Expansion Ratio.
* SRT- Slab reheating temperature,FT- hot finish rolling temperature ,ROT- Run out table at hot strip mill , CR%- Cold rolling reduction % ,

SS- soaking section ,SCS- Slow cooling section , RCS- Rapid cooling section , OAS- Over-aging section , SPM- Skin pass elongation.
Table 3

CAL Parameters
Sample No SS
TEMP SS
Residence
Time SCS
TEMP SCS
Cooling
Rate˚C/Sec RCS
TEMP RCS
Cooling
Rate-C/Sec OAS TEMPERATURE OAS
Residence
Time SPM ELONG
1a 816 95 685 2 443 30 394 327 0.3
1b 816 95 685 2 380 42 360 327 0.3
2 830 113 690 1.67 460 25 410 393 0.4
3 810 113 700 1.32 380 33.5 350 390 0.4
4 820 110 710 1.35 310 30 280 390 0.4
5 800 103 700 1.2 410 27 380 430 0.5
6 816 95 685 2 443 30 394 327 0.3
Table 4

Mechanical Prop Product Properties
Sampl e No YS Y P
E TS ELONGATI ON Yield Ratio n Value H
E R % Ferri te % Bainite
% Retained Austenit
e % Martensit e % Remark
s
1a 750 0 1040 17 0.7 0.16 40 69.2 23.8 5 2 I
1b 700 0 1150 13 06 0.1 26 80 0 0 20 C
2 800 0 1030 15 0.8 0.12 32 59 29 7 5 I
3 650 0 1005 12 0.6 0.09 23 65 0 35 C
4 630 0 1020 11 0.6 0.09 25 70 0 30 C
5 530 0 837 13 0.6 0.095 26 78 0 22 C
6 850 0 1130 14 0.75 0.13 32 63 30 5 2 I
*I - Present inventive example, C- Comparative Examples
In sample 3, 4 and 5 where in sample 3 Tensile strength is 1005 MPa
and n value is 0.09.
In case of sample 4 and 5 n values is less than 0.12 which is out of
scope of current invention,incase of sample 1b where retained

austenite is 0 and martensite percentage is 20 percent and n value is 0.1 less than 0.12 and has poor HER % less than 30% which is out of scope of current invention.
It is thus possible by way of the present invention to provide 1000 MPa Tensile strength level high strength cold rolled steel sheet involving select chemical elements in terms of weight percent: C: 0.16-0.2 %; Mn: 2.0-2.5 %; Si: 0.96–1.0%; Al: 0.12-0.5% S: 0.005 % or less; N: 0.005 % or less Ti: 0.005-0.05%; Mo: 0.02-0.08%; and the balance being Fe and other unavoidable impurities; wherein [Si] / [Al] ratio is in a range of 2 to 8 and having selective steel microstructure constituents including atleast 20% Bainite phase, Tempered Martensite from 1 to 5% and Retained Austenite from 5 to 10% in ferrite matrix as shown in Fig. 1(Bainite-26%, Retained Austenite: 8%, Ferrite-64%) for excellent hole Expansion ratio.
The advancement favors generation of cold rolled high strength steel
sheet having Yield strength of 600MPa or more, Tensile strength of
1000 MPa or more, total elongation of 14% or more, strain hardening
coefficient of 0.12 or more and Hole Expansion ratio 30 %or more and
follow selective Work roll diameter and work roll roughness so that it
follow the following differential equation
δY*W*((R*Δh)^1/2+R*Δh*Ra/2hav)) <= 100, to avoid gauge variation along the length of the coil.

We Claim:
1. Cold rolled high strength steel sheets having tensile strength atleast
1000 MPa with composition in terms of weight % comprising:
C: 0.16-0.2 %;
Mn: 2.0-2.5 %;
Si: 0.96–1.0%;
Al: 0.12-0.5%
S: 0.005 % or less;
N: 0.005 % or less
Ti: 0.005-0.05%;
Mo: 0.02-0.08%;
and the balance being Fe and other unavoidable impurities; wherein [Si] / [Al] ratio is in a range of 2 to 8 and having selective steel microstructure constituents including atleast 20% Bainite phase, Tempered Martensite from 1 to 5% and Retained Austenite from 5 to 10% in ferrite matrix for excellent hole Expansion ratio.
2. Cold rolled high strength steel sheets as claimed in claim 1 wherein said microstructure constituents comprise 20 % or more of bainite, 5 % or less of martensite phase, 5 % or more of retained austenite phase and balance being ferrite phase along with carbide, nitride and sulphide.
3. Cold rolled high strength steel sheet as claimed in anyone of claims 1 or 2 comprising atleast one type of element selected from the group of elements consisting of Ca, Zr, V, W and Cr in amount less than 0.04 wt%.
4. Cold rolled high strength steel sheet as claimed in anyone of claims 1 to 3 additionally comprising in terms of weight % atleast one element selected from the group consisting of 0.002 % to 0.2 % Cu and 0.002 % to 0.2 % Ni
5. Cold rolled high strength steel sheets as claimed in anyone of claims 1 to 4 having Yield strength of 600 MPa or more, Tensile strength of 1000 MPa or more, total elongation of 14% or more, strain hardening

coefficient of 0.12 or more and Hole Expansion Ratio of 30 MPa or more.
6. A process for manufacturing the cold rolled high strength steel
sheets as claimed in claims 1 to 5 having tensile strength of atleast
1000 MPa comprising the steps of:
providing steel having composition comprising
C: 0.16-0.2 %;
Mn: 2.0-2.5 %;
Si: 0.96–1.0%;
Al: 0.12-0.5%
S: 0.005 % or less;
N: 0.005 % or less
Ti: 0.005-0.05%;
Mo: 0.02-0.08%;
and the balance being Fe and other unavoidable impurities;
involving processing through Heat from basic oxygen furnace (BOF) and RH degasser and subsequently continuously casting slab and reheating the slab having said composition to reheating temperature in the range from 1190°C -1250 °C; said reheated slab being subjected to roughing rolling in roughing mill with roughing mill delivery temperature of 1080°C or less;
Said rough rolled steel being subjected to finish rolling with finish mill exit temperature ranging from Ac3°C to Ac3+100 °C.
7. A process for manufacturing the cold rolled high strength steel
sheets as claimed in claim 6 further comprising the steps of:
a)Coiling the finish rolled steel at with average run out table cooling rate of 9 °C/second or more;
b) Acid pickling the Cold rolling the said hot rolled steel sheet with cold reduction of atleast 35%; and it shall follow the following differential equation

δY*W*((R*Δh)^1/2+R*Δh*Ra/2hav)) <= 100, where δY- Change in HR Yield Strength, W-width of strip, R- Radius of work roll, Δh=Change in strip Thickness, Ra- Work Roll Roughness and hav=(hi+hf)/2, where hi=initial thickness and hf=final thickness. Subjecting said cold rolled sheet to continuous annealing with selective parameters followed by skin passing.
8. A process for manufacturing cold rolled steel sheet as claimed in anyone of claims 6 or 7, wherein cold rolled steel is subjected to said continuous annealing following the steps comprising:
a) annealing the cold rolled steel sheet by heating at the rate of 0.5-5 °C/sec up to soaking section critical temperature range from 800 °C to 850 °C with residence time ranging from 70 to 150 seconds;
b) slow cooling the steel at cooling rate in the rage from 0.2 to 3°C/sec up to a temperature in the range from 680°C to 720 °C after soaking ;
c) rapid cooling the steel from SCS temperature up to a temperature range of 420 °C to 500 °C at a critical cooling rate of 40°C/sec or less;
d) overaging the said steel in the temperature range starting from 380 °C to 420 °C or more with residence time of 250 to 560 seconds wherein
e) Subjecting the over-aged steel to skin pass elongation of 0.20 to 1%.