1. The cold-rolled continuous annealing steel plate with the ultrahigh formability of the automobile at 980MPa is characterized by comprising the following components in percentage by weight: 0.18% -0.24%, Si: 1.5% -2.0%, Mn: 1.8% -2.5%, Ti: 0.01 to 0.03 percent of the total weight of the alloy, less than or equal to 0.01 percent of P, less than or equal to 0.005 percent of S, and the balance of Fe and inevitable impurities.

2. The plastic die steel having excellent high-temperature strength as claimed in claim 1, wherein Cr: less than or equal to 0.5 percent, Mo: less than or equal to 0.3 percent, Cu: less than or equal to 0.2 percent, Nb: less than or equal to 0.02 percent, less than or equal to 0.05 percent of V, less than or equal to 0.005 percent of Ca and less than or equal to 0.003 percent of B.

3. The cold-rolled continuous-annealing steel plate with ultra-high formability for automobiles as claimed in claim 1, wherein the steel plate has a yield strength of 700MPa or more, a tensile strength of 980MPa or more, a yield ratio of 0.65 or more, a post-fracture elongation of 25% or more, and a hole expansion value of 40% or more.

4. The cold-rolled continuous-annealed steel plate with ultra-high formability for automobiles of 980MPa grade according to claim 1, wherein the microstructure of the steel plate is ferrite + tempered martensite + bainite + residual austenite; the microstructure of the steel plate is as follows according to volume percentage: ferrite 22-34%, tempered martensite 42-48%, bainite: 13% -15% of ferrite and 10% -15% of retained austenite, wherein the ferrite is critical zone ferrite and oriented periphytic ferrite.

5. A method for preparing the automobile ultra-high formability 980MPa cold rolled continuous annealing steel plate as claimed in any one of claims 1 to 4, comprising smelting, hot rolling, acid washing, cold rolling, and continuous annealing; the method is characterized in that:

(1) hot rolling: the heating temperature is 1230-1280 ℃, the initial rolling temperature is 1100-1150 ℃, the final rolling temperature is 950-1000 ℃, and the coiling temperature is 450-500 ℃;

(2) cold rolling: rolling reduction rate is 54% -63%;

(3) and (3) continuous annealing: firstly, heating a cold-rolled steel plate to 800-870 ℃ at a speed of 2-10 ℃/s, and keeping the temperature constant for 50-240 s; then, slowly cooling the steel plate to 660-710 ℃ at a cooling speed of 0.5-4 ℃/s; and then quenching the steel plate to 220-280 ℃ at a cooling speed of 30-35 ℃/s in a rapid cooling stage, then heating to the overaging temperature of 360-450 ℃ at a heating speed of more than or equal to 10 ℃/s, carrying out isothermal treatment for 180-450 s, and finally cooling to room temperature.

6. The method for preparing the cold-rolled continuous annealing steel plate with the ultra-high formability for the automobile of 980MPa according to claim 5, wherein in the step (1), 50-100 meters of the head and the tail of the coiling process are coiled by a 600 +/-30 ℃ U-shaped coil, and then the steel plate enters a cover furnace to be subjected to stress relief annealing at 450-500 ℃ for 25-35 hours.

7. The method for preparing the cold-rolled continuous annealing steel plate with the ultra-high formability of 980MPa for automobiles according to claim 5, wherein in the step (1), the structure of the steel plate after coiling is 40% -45% of ferrite, 35% -40% of bainite, and the balance of pearlite and unidentified phases.

8. The method for preparing the cold-rolled continuous annealing steel plate with the ultrahigh formability of 980MPa for automobiles according to claim 5, wherein in the step (3), the microstructure of the steel plate after quenching is more than or equal to 30% of martensite and more than or equal to 30% of supercooled austenite in percentage by volume.

Background

The advanced high-strength steel of the automobile always occupies the main material of the body-in-white of the automobile by virtue of the mature production process and lower manufacturing cost. The advanced high-strength steel widely applied to the automobile body at present is concentrated on the first generation and the second generation, represents that interstitial free steel (IF), low-alloy high-strength steel (HSLA), dual-phase steel (DP) and the like exist in steel types, and is used for automobile body covering parts and structural parts, and the strength coverage is 260-780 MPa. With the gradual increase of the lightweight process of automobiles, advanced high-strength steel is updated in real time, wherein the widely researched third-generation automobile advanced high-strength steel is also mature to be applied to automobile parts, and represents that the steel quenching distribution steel (QP) has replaced the existing first and second-generation advanced high-strength steel in a large range and is used for B columns, front longitudinal beams and engine side beams, so that the lightweight effect and the safety performance of an automobile body are improved. It is worth noting that the research and development of the third generation high-strength steel solves the problem that the strength and the plasticity can not be well compatible to a certain extent, for example, the elongation of QP980 steel is improved by about 2 times on the basis of DP980, and the plasticity of the steel plate is greatly improved by introducing the retained austenite, so that the stamping forming performance of the steel plate is improved. However, the new problem of the high-strength steel with over 980MPa is that the punching performance and the flanging performance are incompatible, namely the flanging performance of the steel plate with better punching performance is insufficient, such as QP steel and TWIP steel; or the steel plate with better flanging performance has insufficient stamping performance, such as DP steel and M steel. Such a problem greatly limits the application of high-strength steel of 980MPa or more to vehicle bodies. The stamping performance of the steel plate is mainly related to the elongation, and good stamping performance is determined by good drawing performance; the flanging performance of the steel plate is mainly related to the hole expansion performance, and the good hole expansion rate determines the good flanging performance of the steel plate. Therefore, the development of a steel sheet having both high plasticity and high hole expansion ratio is important for the development of automobile steel of 980MPa or more, which is also an expression of high formability.

The steel plate of the distribution steel disclosed in the patent document 980 MPa-level quenching distribution steel and the preparation method thereof (publication number: CN111118397A) comprises the following components in percentage by weight: c: 0.20 to 0.25, Si: 1.4-1.8, Mn: 1.8-2.2, V: 0 to 0.10, Nb: 0 to 0.050, Ti: 0 to 0.050, less than or equal to 0.0060N, less than or equal to 0.010P, less than or equal to 0.012S and less than or equal to 0.060 Al, the preparation method comprises the working procedures of smelting, hot rolling, acid rolling and continuous annealing, the continuous annealing working procedure carries out annealing in a two-phase region of 780 to 820 ℃, and then the annealing is carried out after cooling to 365 to 390 ℃ for overaging isothermal treatment. The elongation of the product after fracture can reach about 25 percent, and the high-drawing performance is realized. However, the steel is added with a large amount of micro-alloy elements such as Nb, V, Ti and the like, so that the alloy cost of the material is increased; in addition, the yield ratio of the steel is only about 0.5, which indicates that the hole expansion performance of the steel is not good, and the technical requirement of high flanging is difficult to meet.

The steel alloy disclosed in the patent document 980MPa grade cold-rolled high-strength Q & P steel for automobiles and the production method thereof (publication number: CN108193138A) comprises the following components: 0.18 to 0.24%, Si: 0.60 to 1.30%, Mn: 1.60-2.40%, P: 0.02-0.04%, S is less than or equal to 0.005%, Nb: 0.040-0.070%, N is less than or equal to 0.0060%, Als: 0.50 to 1.0% and the balance Fe and inevitable impurities. Obviously, a large amount of Nb element is added into the steel plate to play a role in fine grain strengthening, so that the comprehensive strong plasticity of the steel plate is improved. However, even when a high proportion of microalloy is added, the yield strength of the steel is still about 550MPa, and the yield ratio is only 0.5 to 0.6, which indicates that the hole-expanding performance of the steel is insufficient.

The steel plate disclosed in the patent document CN103233161A (a low yield ratio high-strength hot-rolled Q & P steel) and the manufacturing method thereof and the patent document CN111411299A (a 1000MPa grade cold-rolled high-elongation Q & P steel plate and the manufacturing method thereof) is 1000MPa grade cold-rolled high-elongation QP steel, and can reach the yield strength of 550-600 MPa, the tensile strength of more than 1000MPa and the elongation after fracture of about 20 percent. However, it is obvious that the application of the alloy design and the manufacturing process of the products can not produce cold-rolled products with both high yield ratio and elongation, i.e. the cold-rolled products are only suitable for parts with high drawing requirements in the actual part forming application and can not meet the forming parts with high flanging and high drawing requirements such as engine side beams and comprehensive solutions of the lower ends of A columns.

Disclosure of Invention

The invention aims to overcome the problems and the defects and provide a 980 MPa-grade cold-rolled continuous annealing steel plate with ultrahigh formability for automobiles, which has high drawing and flanging performances, yield strength of more than 700MPa, tensile strength of more than 980MPa, yield ratio of more than 0.65, elongation after fracture of more than 25% and hole expansion value of more than 40%, and a preparation method thereof.

The purpose of the invention is realized as follows:

a980 MPa-grade cold-rolled continuous annealing steel plate with ultrahigh formability for automobiles comprises the following components in percentage by weight: c: 0.18% -0.24%, Si: 1.5% -2.0%, Mn: 1.8% -2.5%, Ti: 0.01 to 0.03 percent of the total weight of the alloy, less than or equal to 0.02 percent of P, less than or equal to 0.005 percent of S, and the balance of Fe and inevitable impurities.

Further, Cr: less than or equal to 0.5 percent, Mo: less than or equal to 0.3 percent, Cu: less than or equal to 0.2 percent, Nb: less than or equal to 0.02 percent, less than or equal to 0.05 percent of V, less than or equal to 0.005 percent of Ca and less than or equal to 0.003 percent of B.

Further, the steel plate has a yield strength of above 700MPa, a tensile strength of above 980MPa, a yield ratio of above 0.65, a post-fracture elongation of above 25%, and a hole expansion value of above 40%.

Further, the microstructure of the steel plate is ferrite, tempered martensite, bainite and residual austenite; the microstructure of the steel plate is as follows according to volume percentage: ferrite 22-34%, tempered martensite 42-48%, bainite: 13-15 percent of ferrite and 10-15 percent of residual austenite, wherein the ferrite is critical zone ferrite and oriented periphytic ferrite, the critical zone ferrite content is 17-20 percent, and the oriented periphytic ferrite content is 2-15 percent.

The invention has the following design reasons:

c: c is one of the important alloying elements in the present invention. C is dissolved in the matrix as interstitial solid solution atoms to cause lattice distortion, and acts to strengthen the steel sheet. Secondly, the fluctuation of the concentration of the C element is also a necessary condition for austenite nucleation, namely, the addition of a proper amount of the C element promotes the nucleation and stabilization process of austenite in the critical region. In addition, for the steel containing the retained austenite in the room temperature structure, the addition of the C element is indispensable, and the related literature reports that the C content in the retained austenite needs to be more than 1.2% to maintain the phase stability of the retained austenite at room temperature. For the 980MPa steel, the structure composition and the mechanical property of the steel plate are influenced by the excessively low or high C addition. If the content of C is less than 0.18 percent, the formation of residual austenite at room temperature with enough content cannot be ensured, and the plasticity of the experimental steel is influenced; if the content of C is more than 0.24%, the Ms point of the steel plate in the critical zone under the isothermal condition is reduced, so that the optimized quenching temperature point in actual production is reduced, and the manufacturing difficulty and the production cost are increased.

Si: si element is one of important elements in the present invention. Si is used as solid solution strengthening atoms, lattice distortion is caused by a mode of replacing Fe atoms, and the ferrite strength is improved; secondly, the addition of Si can promote the formation of ferrite and enlarge the selection of annealing temperature in a critical zone; in addition, the addition of Si in a sufficient amount can suppress the formation of carbides at the overaging stage, and prevent the steel sheet from deteriorating in properties due to carbide precipitation. However, too high Si addition causes embrittlement of the steel sheet after rolling, thereby reducing cold workability of the steel sheet. Therefore, the content of the Si element is controlled to be 1.5 to 2.0 percent in the invention.

Mn: the Mn element is one of important elements in the present invention. Mn is used as a replacement solid solution atom to play a role in solid solution strengthening; secondly, in the research, Mn guarantees the austenite stabilization in the critical region and the stability of the supercooled austenite in the cooling process, and inhibits the formation of pearlite; most importantly, the addition of sufficient Mn element improves the hardenability of the steel plate and ensures the transformation quantity of martensite in a quenching state. However, excessive Mn addition causes serious Mn segregation in the continuous casting process, and meanwhile, the slab continuous casting is easy to generate a hot cracking phenomenon; furthermore, the addition of high Mn will also cause an increase in carbon equivalent in the subsequent welding stage, thereby deteriorating the welding performance. Therefore, the Mn content in the steel of the invention is controlled to be 1.8-2.5%.

Ti: ti element is one of the important elements in the present invention. Ti combines with impurity element N of steel grade to form TiN, free N atoms in the steel are present in the steel grade to deteriorate the toughness of the steel plate, so the formation of TiN plays a role in fixing N; in addition, Ti still forms Ti (C, N) with C, N, and plays a role in refining prior austenite grains. However, the Ti content is too high, which results in too large size of TiN and deterioration of the steel sheet properties. Therefore, the Ti content in the invention should be controlled between 0.01% and 0.03%.

P: p element is impurity element in steel, is easy to be partially gathered in crystal boundary, and is easy to form Fe when P content in steel is high₂P particles, which reduce the plasticity and toughness of the steel, are preferably contained in a lower amount. In the invention, the content of the P element is controlled to be less than or equal to 0.01 percent.

S: the S element is an impurity element in steel, and is easily combined with Mn to form MnS inclusions, thereby deteriorating the plasticity of the steel plate, so that the lower the content is, the better the content is. In the invention, the content of the S element is controlled to be less than or equal to 0.005 percent.

Cr: cr is added into the steel as a Mn element supplement element, and when the content of Mn is lower, a proper Cr element can be added, so that the hardenability effect of the steel plate is improved; meanwhile, the addition of Cr can improve the oxidation resistance of the steel plate to a certain extent and improve the internal oxidation state of the steel plate. In the invention, the Cr content is controlled within 0.5 percent.

Mo: mo itself is a solid solution strengthening element, and plays a role in strengthening the steel plate. Meanwhile, the Mo content in the invention is controlled within 0.3%.

The Cu element itself is dissolved in austenite to improve the strength of the steel sheet. In the continuous annealing stage, the simple substance Cu is precipitated in austenite to play a certain precipitation strength role. In the invention, the Cu content is controlled within 0.2 percent.

Nb: in the invention, the appropriate addition of Nb can promote the strain-induced precipitation behavior in the hot rolling recrystallization rolling stage, promote the recrystallization of prior austenite grains and play a role in refining the grains. In the present invention, the Nb content is controlled to be 0.02% or less, and the element is added as a substitute element when the Ti content is low.

V: in the invention, the V element is properly added to strengthen the precipitation strengthening effect in the coiling stage, inhibit the dislocation self-recovery phenomenon in the cold rolling process, improve the retention of deformation energy storage and promote the recrystallization behavior in the continuous annealing stage; meanwhile, VC is precipitated in ferrite in the continuous annealing isothermal stage, and plays a role in precipitation strengthening. In the invention, the content of V is controlled within 0.05 percent.

Ca: the inclusion morphology can be controlled by adding a proper amount of Ca, thereby improving the quality of the casting blank steel plate. In the invention, the content of Ca is controlled within 0.005 percent.

B: the addition of B in the invention can supplement the hardenability of the steel plate and ensure the formation of martensite in the rapid cooling stage in the continuous annealing galvanization process. Too much B is added to increase the brittleness of the steel sheet and deteriorate the workability of the steel sheet. In the invention, the content of B is controlled to be 0.03 percent.

The second technical scheme of the invention is to provide a preparation method of 980MPa grade cold-rolled continuous annealing steel plate with ultrahigh formability for automobiles, which comprises smelting, casting, hot rolling, acid washing, cold rolling and continuous annealing;

(1) smelting: smelting and casting the components into a wedge-shaped casting blank.

(2) Hot rolling: the heating temperature is 1230-1280 ℃, the initial rolling temperature is 1100-1150 ℃, the final rolling temperature is 950-1000 ℃, and the coiling temperature is 450-500 ℃; in the coiling process, U-shaped coiling at 600 +/-30 ℃ is adopted for 50-100 meters of the head and the tail, then the steel plate enters a bell-type furnace for stress relief annealing at 450-500 ℃ for 25-35 hours, and the thickness of a hot-rolled coil is 3.2-3.5 mm.

The heating temperature is 1230-1280 ℃: for high-strength steel containing Ti, the heating temperature is important to control, and in order to achieve a more ideal N fixation effect, the heating temperature is generally controlled to be above 1230 ℃. Thereby ensuring that fine TiN or Ti (C, N) is separated out in the heating and recrystallization zone rolling stages, and playing the effects of pinning grain boundaries and refining original austenite grains.

The finishing temperature is 950-1000 ℃: the setting of the finish rolling temperature is mainly to ensure that the rough rolling and finish rolling stages are completed as soon as possible so as to prevent TiN precipitates from coarsening and further to prevent poor pinning effect of crystal boundary. Therefore, the finishing temperature of the invention should be controlled to 950-1000 ℃.

Coiling temperature is 450-500 ℃: in order to solve the surface problem caused by high Si addition in the product of the invention, low-temperature coiling is adopted to avoid SiO₂/MnO₂Isogenic oxide formation; meanwhile, the U-shaped coiling at the temperature of 600 +/-30 ℃ from head to tail is adopted in consideration of overhigh strength of the hot coil. And then, in order to prevent the rolling force in the cold rolling stage from being too large, the hot coil is placed in a bell-type furnace to be subjected to stress relief annealing at 450-500 ℃.

The steel plate structure after coiling is 40-45% of ferrite, 35-40% of bainite, and the balance of pearlite and unidentified phase.

(3) Acid washing: FeO and Fe exist on the surface of the hot rolled and coiled steel₂O₃、Fe₃O₄And removing iron oxide in different existing forms after acid pickling.

(4) Cold rolling: the specification of a cold-rolled product is kept to be 1.2-1.8 mm thick, the thickness of a target automobile part corresponding to the product is controlled to be 54% -63% corresponding to the thickness (1.2mm, 1.4mm, 1.6mm and 1.8mm) of the product, and the low rolling reduction rate cannot ensure enough cold-rolling deformation energy storage, so that the ferrite recrystallization effect is insufficient in the continuous annealing stage; the load of the cold rolling mill is greatly increased under the condition of overhigh rolling reduction, and the realization of the target thickness cannot be ensured.

(5) And (3) continuous annealing: firstly, heating a cold-rolled steel plate to 800-870 ℃ at a speed of 2-10 ℃/s, and keeping the temperature constant for 50-240 s; then, slowly cooling the steel plate to 660-710 ℃ at a cooling speed of 0.5-4 ℃/s; and then quenching the steel plate to 220-280 ℃ at a cooling speed of 30-35 ℃/s in a rapid cooling stage, then heating to the overaging temperature of 360-450 ℃ at a heating speed of more than or equal to 10 ℃/s, carrying out isothermal treatment for 180-450 s, and finally cooling to room temperature.

The final organization is: ferrite + tempered martensite + bainite + residual austenite.

The isothermal heating temperature is 800-870 ℃, and the purpose is to ensure that the austenitizing degree of a sufficient critical region is more than 60%, further ensure the contents of martensite and super-cooled austenite in a structure after subsequent quenching, the martensite forms tempered martensite in a subsequent overaging stage, the strength of the steel plate is ensured, and the super-cooled austenite forms bainite and retained residual austenite in the overaging stage, so that coordinated deformation is realized, and the plasticity is improved.

The isothermal time in the heating stage is 50-240 seconds, when the isothermal time in the heating stage is too low, ferrite recrystallization and austenite phase deformation nuclei are not sufficiently performed, and when the isothermal time is too high, ferrite softening, austenite grain coarsening and other phenomena are serious, so that the final structure performance is influenced. Therefore, the isothermal time is controlled within 50-240 s.

The slow cooling temperature is 660-710 ℃, the slow cooling stage generally plays a role in uniform structure in common steel, and the slow cooling temperature is strictly controlled to be 660-710 ℃ in the invention so as to prevent excessive oriented epiferrite from forming and reducing the yield strength of the experimental steel and even the final tensile strength.

In the rapid cooling stage, the cooling speed is above 30-35 ℃/s to prevent the formation of oriented ferrite in the rapid cooling stage from influencing the performance of the steel plate; secondly, the quenching temperature is 220-280 ℃, the quenching temperature is one of the very important parameters in the invention, the final structure state of the invention is ferrite, tempered martensite, bainite and residual austenite, the selection of the quenching temperature directly influences the proportion of the tempered martensite, the bainite and the residual austenite under the final configuration, the quenching temperature of 220-280 ℃ in the invention ensures that the proportion of the martensite is more than or equal to 30% and the proportion of the super-cooled austenite is more than or equal to 30% under the quenching state, and further ensures that the tempered martensite content is 42-48%, the bainite content is 13-15% and the residual austenite content is 10-15% in the final structure. If the quenching temperature is too low, the content of super-cooled austenite in a quenching state is reduced, so that the proportion of subsequent bainite and residual austenite is too low, and the plasticity of the steel plate is influenced; if the quenching temperature is too high, the martensite content in the quenched state is reduced, so that the tempered martensite content in the final structure is reduced, and the strength of the steel plate is influenced.

Good plasticity in the invention is caused by bainite formation and residual austenite content increase in the overaging stage, and the formation of bainite and the retention of residual austenite are inhibited by overlow overaging temperature; at the same time, the higher strength in the present invention results from a suitably tempered martensite configuration. An excessively high overaging temperature causes cementite precipitation at the overaging stage, deteriorating the mechanical properties of the steel sheet. Therefore, the overaging temperature should be controlled to be 360-450 ℃.

Bainite transformation usually requires a longer incubation period, and too short overaging isothermal time is not beneficial to formation of bainite; meanwhile, the over-aging time also affects the tempering resistance of the tempered martensite, and the excessively long over-aging time causes cementite in the tempered martensite to be precipitated, thus deteriorating the mechanical property of the steel plate. Therefore, the overaging time is controlled to be 180-450 s.

The invention has the beneficial effects that:

(1) compared with products of the same grade, the 980 MPa-grade cold-rolled continuous annealing steel plate with high formability is free from or less in precious metal addition in alloy components, and the alloy cost is well controlled.

(2) According to the invention, through reasonable component and process design, the structure evolution characteristics of martensite phase transformation, bainite phase transformation and retained austenite are fully combined, the phase proportion of tempered martensite, bainite and retained austenite in the final structure is effectively regulated and controlled, and the compatibility of high yield and extension of the product is further ensured.

(3) The invention has obvious advantages of plasticity and strength in 980MPa same-grade products, can be used for more complex vehicle body stage parts, meets high drawing and flanging resistance, and is particularly suitable for stamping and roll forming.

The invention relates to a 980MPa grade cold-rolled continuous annealing steel plate with high formability, which has the advantages of more than 700MPa, tensile strength of more than 980MPa, yield ratio of more than 0.65, elongation after fracture of more than 25 percent and hole expansion value of more than 40 percent. Compared with 980MPa grade cold rolling continuous annealing steel plates, the product of the invention has the characteristics of high yield and high extension, and the product of the invention has the forming advantages of high flanging and high drawing in the stamping process.

Drawings

FIG. 1 is an SEM micrograph of a structure according to example 1 of the present invention.

Detailed Description

The present invention is further illustrated by the following examples.

According to the embodiment of the invention, smelting, hot rolling, acid washing, cold rolling and continuous annealing are carried out according to the component proportion of the technical scheme.

(1) Hot rolling: the heating temperature is 1230-1280 ℃, the initial rolling temperature is 1060-1150 ℃, the final rolling temperature is 950-1000 ℃, and the coiling temperature is 450-500 ℃;

(2) cold rolling: rolling reduction rate is 54% -63%;

(3) and (3) continuous annealing: firstly, heating a cold-rolled steel plate to 800-870 ℃ at a speed of 2-10 ℃/s, and keeping the temperature constant for 50-240 s; then, slowly cooling the steel plate to 660-710 ℃ at a cooling speed of 0.5-4 ℃/s; and then quenching the steel plate to 220-280 ℃ at a cooling speed of 30-35 ℃/s in a rapid cooling stage, then heating to the overaging temperature of 360-450 ℃ at a heating speed of more than or equal to 10 ℃/s, carrying out isothermal treatment for 180-450 s, and finally cooling to room temperature.

Further, in the step (1), 50-100 meters of the head and the tail of the coiling process are coiled by adopting a U-shaped coil at 600 +/-30 ℃, and then the steel plate enters a bell-type furnace to be subjected to stress relief annealing at 450-500 ℃ for 25-35 hours.

Further, in the step (1), the steel sheet structure after coiling is 40-45% of ferrite, 35-40% of bainite, and the balance of pearlite and unidentified phases.

Furthermore, the microstructure of the quenched steel plate comprises more than or equal to 30 percent of martensite and more than or equal to 30 percent of supercooled austenite in percentage by volume.

The compositions of the steels of the examples of the invention are shown in table 1. The main process parameters of the steel rolling of the embodiment of the invention are shown in Table 2. The main process parameters of the continuous annealing of steel in the embodiment of the invention are shown in Table 3. The microstructure of the steels of the examples of the invention is shown in Table 4. The properties of the steels of the examples of the invention are shown in Table 5.

TABLE 2 Main Process parameters for Steel Rolling in the examples of the present invention

TABLE 3 Main Process parameters for continuous annealing of steel in the examples of the present invention

Table 4 microstructure (vol.%) of inventive example steels

TABLE 5 tensile Properties of steels according to examples of the invention

Examples	Rp0.2/MPa	Rm/MPa	Rp0.2/Rm	A50/％	λ/％
						1	743	1015	0.73	26.5	43.6
2	752	1033	0.73	25.5	48.5
						3	737	1024	0.72	25.7	53.6
4	755	1034	0.73	25.9	44.8
						5	706	1026	0.69	25.7	52.5
6	728	1045	0.70	25.8	41.8
						7	747	1037	0.72	26.5	52.9
8	764	1038	0.74	25.6	54.8
						9	757	1031	0.73	26.9	55.7
10	747	1021	0.73	26.8	52.6
						11	756	1052	0.72	25.4	46.3
12	718	1043	0.69	25.6	44.7
						13	778	1025	0.76	26.8	48.4
14	792	1034	0.77	27.8	42.9
						15	787	1031	0.76	26.3	44.7

As can be seen from the above, the 980MPa grade cold-rolled continuous annealing steel plate with high formability has the yield strength of more than 700MPa, the tensile strength of more than 980MPa, the yield ratio of more than 0.65, the elongation after fracture of more than 25 percent and the hole expansion value of more than 40 percent. Compared with 980MPa grade cold rolling continuous annealing steel plates, the product of the invention has the characteristics of high yield and high extension, and the product of the invention has the forming advantages of high flanging and high drawing in the stamping process.

In order to express the present invention, the above embodiments are properly and fully described by way of examples, and the above embodiments are only used for illustrating the present invention and not for limiting the present invention, and those skilled in the relevant art can make various changes and modifications without departing from the spirit and scope of the present invention, and any modifications, equivalent substitutions, improvements, etc. made by the persons skilled in the relevant art should be included in the protection scope of the present invention, and the protection scope of the present invention should be defined by the claims.