CN113897552A - 30 GPa% - Google Patents
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- CN113897552A CN113897552A CN202111184538.9A CN202111184538A CN113897552A CN 113897552 A CN113897552 A CN 113897552A CN 202111184538 A CN202111184538 A CN 202111184538A CN 113897552 A CN113897552 A CN 113897552A
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Abstract
The invention relates to the technical field of steel plates, and provides a 30 GPa%: 0.29-0.30% of C, 1.80-2.00% of Mn, 1.00-1.10% of Si, 0.50-0.70% of Al and the balance of Fe; the critical annealing temperature of the steel plate is 780-790 ℃. The problem of how to select proper target components and continuous annealing temperature to realize the performance of the alloy under the condition of not adding microalloy elements in the prior art and reach the performance product index of 30GPa percent when the tensile strength exceeds 980MPa is solved.
Description
Technical Field
The invention relates to the technical field of steel plates, in particular to a 30 GPa%.
Background
In order to meet the requirements of safety, light weight, environmental protection and economic oil consumption in the automobile industry, the research and development strength of the advanced high-strength steel for automobiles is increased by steel enterprises, the tensile strength is over 980MPa, and the product of strength and elongation of 30 GPa% -is acknowledged as a performance index of the third-generation advanced high-strength automobile steel, and no report of mass production of the steel is provided at present.
Transformation Induced Plasticity (TRIP) steels are ideal candidate Steel grades for third-generation automotive Steel sheets because of their low alloy content, high strength-Plasticity alloy, and easy smooth production. According to the alloying principle, on one hand, the research and development of the steel grade at present improves the strength of the steel through adding microalloy elements vanadium and titanium and through the effects of precipitation strengthening and fine grain strengthening, and in addition, vanadium-titanium carbide is subjected to redissolution in the critical annealing process to carburize austenite, improve the stability of the steel and further improve the plasticity; on the other hand, the aluminum element is added to enlarge the two-phase region of ferrite and austenite so as to increase the carbon content in austenite, and then the residual austenite is promoted to play the TRIP effect, thereby improving the product of strength and elongation. However, it is worth pointing out that the square hard brittle phase of vanadium titanium nitride type is easy to be separated out and coarsened in the preparation process, which causes the micro-alloyed TRIP steel to have unstable performance and is not beneficial to the smooth production. On the premise of not adding microalloy elements, how to select proper target components and continuous annealing temperature to enable the performance of the steel to achieve a product of strength and elongation index of 30 GPa% -when the tensile strength exceeds 980MPa is not reported, and particularly how to adopt a scientific design research and development idea to realize the successful preparation of third-generation TRIP primary steel in a short period almost has no examples for reference.
Disclosure of Invention
The invention provides a 30 GPa%.
The technical scheme of the invention is as follows: the 30 GPa% -transformation induced plasticity automobile steel plate is characterized by comprising the following chemical components in percentage by mass: 0.29-0.30% of C, 1.80-2.00% of Mn, 1.00-1.10% of Si, 0.50-0.70% of Al and the balance of Fe; the critical annealing temperature of the steel plate is 780-790 ℃.
The steel plate comprises the following chemical components in percentage by mass: 0.30% of C, 1.90% of Mn, 1.00% of Si, 0.60% of Al and 96.20% of Fe; the critical annealing temperature of the steel sheet was 780 ℃.
The steel plate comprises the following chemical components in percentage by mass: 0.29 percent of C, 2.00 percent of Mn, 1.10 percent of Si, 0.50 percent of Al and 96.11 percent of Fe; the critical annealing temperature of the steel sheet was 780 ℃.
The steel plate comprises the following chemical components in percentage by mass: 0.29 percent of C, 1.80 percent of Mn, 1.00 percent of Si, 0.70 percent of Al and 96.21 percent of Fe; the critical annealing temperature of the steel sheet was 780 ℃.
The steel plate comprises the following chemical components in percentage by mass: 0.30% of C, 1.80% of Mn, 1.00% of Si, 0.60% of Al and 96.30% of Fe; the critical annealing temperature of the steel sheet was 780 ℃.
The steel plate comprises the following chemical components in percentage by mass: 0.30% of C, 1.90% of Mn, 1.10% of Si, 0.50% of Al and 96.20% of Fe; the critical annealing temperature of the steel sheet was 780 ℃.
The steel plate comprises the following chemical components in percentage by mass: 0.30 percent of C, 2.00 percent of Mn, 1.00 percent of Si, 0.70 percent of Al and 96.00 percent of Fe; the critical annealing temperature of the steel sheet was 790 ℃.
An experimental method of 30 GPa% -transformation induced plasticity (TPI) of an automobile steel plate is characterized by comprising the following steps:
a. the chemical components and the critical annealing temperature range of the experimental steel plate are drawn up:
the steel plate comprises the following chemical components in percentage by mass: 0.20 to 0.30 percent of C, 1.50 to 2.00 percent of Mn, 1.00 to 1.50 percent of Si, 0.50 to 1.00 percent of Al and the balance of Fe; the critical annealing temperature of the steel plate is 760-820 ℃;
b. determining characteristic parameters and writing a program file for developing integrated batch calculation:
utilizing a Thermo-Calc calculation software package, writing a program file capable of carrying out characteristic parameter calculation under different components and temperature conditions by adopting a TC-Python interface and using Python language, wherein the characteristic parameter 1 is AF and represents austenite content under different critical annealing temperatures, the characteristic parameter 2 is AC and represents carbon content in austenite under different critical annealing temperatures, and the characteristic parameter 3 is tCRepresents the time required for the diffusion of carbon elements in austenite to equilibrate; the key instructions in the program file comprise that thermodynamic and kinetic data are read simultaneously, and thermodynamic calculation of characteristic parameters 1 and 2 and kinetic calculation of characteristic parameter 3 of different alloy systems are completed; automatic assignment of alloy components and temperature is realized by adopting a cycle statement, and batch calculation is completed; limiting the calculation error range to obtain effective data, and finishing the output of the calculation result;
c. determining calculation conditions, operating a calculation program to screen components:
setting the calculation step length of each alloy element based on the component range determined in the step a, and acquiring AF and t by adopting a program file I for integrally calculating the characteristic parameters 1 and 3 in the step bCBased on the principle of maximizing the product of the two, selecting components corresponding to 20 percent of the first calculated result to carry out annealing temperature screening;
d. determining calculation conditions, operating a calculation program to screen annealing temperature:
setting the calculation step length of the annealing temperature based on the temperature range determined in the step a, adopting a program file II for integrally calculating a characteristic parameter 1 and a characteristic parameter 2 in the step b to obtain the calculation results of AF and AC, and selecting corresponding components and the annealing temperature as target components and the target annealing temperature based on the principle of maximizing the product of the AF and the AC;
e. preparing the transformation induced plasticity steel according to the screened target components and the target annealing temperature:
and d, according to the target components and the target annealing temperature screened in the step d, carrying out smelting, hot rolling, acid pickling and cold rolling and continuous annealing treatment to obtain the transformation induced plasticity steel with the tensile strength of over 980MPa and the strength-elongation product of 30 GPa%.
And the smelting in the step e is to prepare an ingot by using a vacuum induction smelting furnace and then cut a steel block with the thickness of 30 mm.
The hot rolling in the step e means that the steel blocks obtained by smelting are hot-rolled into hot-rolled steel plates with the thickness of 3mm, the initial rolling temperature is 1150 ℃, and the final rolling temperature is above 900 ℃.
The pickling cold rolling in step e is to cold-roll the hot-rolled steel sheet obtained by the hot rolling treatment into a cold-rolled steel sheet having a thickness of 1.2 mm.
The continuous annealing treatment in the step e is to heat the cold-rolled steel plate obtained by the cold rolling treatment to 780-790 ℃ two-phase region, preserve heat for 3-5min, cool the cold-rolled steel plate to 370-430 ℃ in air, preserve heat for 5min, and cool the cold-rolled steel plate to room temperature in air.
The working principle and the beneficial effects of the invention are as follows: the Fe-Mn-Si-Al-C TRIP series third-generation transformation induced plasticity automobile steel plate with the tensile strength of more than 980MPa and the product of strength and elongation of 30GPa percent can be obtained, trace elements are not added, the total proportion of the alloy elements C, Mn, Si and Al is controlled within 5 percent, and the production cost of the steel plate can be reduced.
The austenite content in TRIP steel and its stability are the key to determine its properties. The critical annealing in a ferrite and austenite two-phase region is a key process, and in the process, the austenite content and the stability thereof depend on the components and the temperature; c, Mn in the composition is an austenite forming element which increases the austenite content but possibly reduces the carbon content in austenite, while Si and Al are ferrite forming elements which decrease the austenite content but increase the carbon content in austenite, contributing to the austenite stability. It is clear that the effect of these alloying elements on austenite is contrary, and that a high austenite content and its stability can be achieved simultaneously only with the correct proportions. It is known that the addition of microalloying elements increases the strength of steel by precipitation strengthening and fine grain strengthening, while the phenomenon of the re-dissolution of vanadium titanium carbides, as compared to niobium, causes carburization of the austenite in the two-phase region, thereby increasing the plasticity. However, vanadium is a strong carbide forming element, and the content of vanadium is not controlled properly or the subsequent heat treatment process is not controlled properly, which may cause the decrease of carbon content in austenite and the coarsening of carbide particles, and is not favorable for performance improvement. The patent indicates that the maximization of austenite content and carbon content thereof can be better realized by adjusting the proportion of C, Mn, Al and Si, so that the residual austenite fully exerts the effect of phase transformation induced plasticity in the deformation process, the strength is increased due to the formation of martensite while the plasticity is improved, and the strong plasticizing effect of microalloy elements can be completely comparable to or even better than that of the microalloy elements.
Based on the above, the research considers the service performance, the process performance and the like of the 780 MPa-grade TRIP steel on the basis of the component range, properly improves the content of alloy elements (the total content of the alloy elements is not more than 5 wt%), and determines the component range; in addition, the continuous annealing temperature range is determined by combining production line process parameters, the austenite content, the carbon content in austenite and the time required by the diffusion of carbon in austenite are used as characteristic parameters for evaluating the stability of the continuous annealing temperature range, thermodynamic and kinetic calculations are carried out, and target components and annealing temperatures are determined.
The traditional research and development mode of steel Materials inherits the thought of a trial and error method, namely, a large number of trial and error experiments are made on the basis of the component range and the heat treatment process of the existing steel grade, and the target components and the process parameters are finally determined to obtain the expected performance. The invention integrates the phase diagram thermodynamics and the diffusion dynamics calculation into an integral system to realize the scientific design of the target components and the process of the third-generation TRIP original steel and complete the short-period preparation, which is the original work of the invention.
Drawings
FIG. 1 shows the data point calculations during the screening of the components of the present invention.
FIG. 2 is a data point calculation result during the process screening of the present invention.
Detailed Description
The invention is described in detail below with reference to the figures and the specific embodiments.
Firstly, an experimental method of a steel plate:
the invention provides the research and development of 30 GPa% -percent phase change induced plasticity automobile steel plates based on ICME technology for the first time, the austenite content under the critical annealing condition is innovatively selected as a characteristic parameter 1, the carbon element content in the austenite is a characteristic parameter 2, the time required for the carbon element in the austenite to diffuse to balance is a characteristic parameter 3, commercial calculation software Thermo-Calc and an interface program are adopted, and the optimization of alloy components and critical annealing process parameters is carried out by integrating the calculation of phase diagram thermodynamics and diffusion kinetics, and the method specifically comprises the following steps:
a. the chemical components and the critical annealing temperature range of the experimental steel plate are drawn up:
the steel plate comprises the following chemical components in percentage by mass: 0.20 to 0.30 percent of C, 1.50 to 2.00 percent of Mn, 1.00 to 1.50 percent of Si, 0.50 to 1.00 percent of Al and the balance of Fe; the critical annealing temperature of the steel plate is 760-820 ℃;
b. determining characteristic parameters and writing a program file for developing integrated batch calculation:
utilizing a Thermo-Calc (TC) calculation software package, and compiling a program file capable of carrying out characteristic parameter calculation under different components and temperature conditions by adopting a TC-Python interface and using Python language, wherein the characteristic parameter 1 is AF and represents austenite content under different critical annealing temperatures, the characteristic parameter 2 is AC and represents carbon content in austenite under different critical annealing temperatures, and the characteristic parameter 3 is tCRepresents the time required for the diffusion of carbon elements in austenite to equilibrate; the written program file I can simultaneously read thermodynamic data (TCFE10 database) and kinetic data (MOBFE5 database) in TC software, complete thermodynamic calculation of characteristic parameters 1 and kinetic calculation of characteristic parameters 3 of different alloy systems, and obtain AF and tCThe change rule along with the components; the written program file II can read thermodynamic data (TCFE10 database) in TC software, thermodynamic calculation of characteristic parameters 1 and 2 of different alloy systems is completed, and the change rule of AF and AC along with temperature is obtained; realizing automatic assignment of alloy components and temperature by adopting a loop statement in a python program, namely assigning the alloy element content and the temperature successively according to the calculation step length in the following table 1 to finish batch calculation, limiting the calculation error range to obtain effective data and finishing the output of a calculation result;
c. determining calculation conditions, operating a calculation program to screen components:
because the distribution of the austenite content and the carbon content thereof during critical annealing is closer to the equilibrium state, the higher the residual austenite content and the higher the stability, and the more significant the transformation induced plasticity effect exerted under the action of an external load, that is, the better the product of the forcing and the elongation, based on the component range determined in step a, the calculation step length of C is set to 0.01%, the calculation step lengths of the remaining alloy elements are set to 0.1%, as shown in table 1, the total of the calculated component points is 11 × 6 × 6 × 6 ═ 2376, a program file i for integrating and calculating the characteristic parameter 1 and the characteristic parameter 3 in step b is adopted, the component range and the step length are input, the average value of the continuous annealing temperature of the production line is set to 800 ℃, and 2376 groups of AF and t are finally obtainedCBased on the maximum product principle of the two, selecting 475 components corresponding to the first 20% of the calculation result to perform annealing temperature screening, wherein the calculation result of the screened data points is shown in fig. 1;
TABLE 1 calculated step lengths for the individual alloying elements
d. Determining calculation conditions, operating a calculation program to screen annealing temperature:
because the austenite content and the carbon content in the TRIP steel structure are correspondingly increased or reduced along with the increase or decrease of the critical annealing temperature, in order to obtain the ideal annealing temperature, the influence of the austenite content and the carbon content thereof should be comprehensively considered, therefore, the calculation step length is determined to be 10 ℃ based on the temperature range (760 + 820 ℃) determined in the step a, as shown in Table 1, the total number of calculation points is 7 × 475 ═ 3325, the calculation results of 3325 groups of AF and AC are obtained by adopting the program file II for integrating and calculating the characteristic parameter 1 and the characteristic parameter 2 in the step b, as shown in FIG. 2, and the components and the annealing temperature corresponding to the area A are selected as the target components and the temperature range, namely C0.29-0.30%, Mn 1.8-2.0%, Si 1.0-1.1% and Al 0.5-0.7%, and the balance of Fe based on the maximum product principle of the two; the critical annealing temperature of the steel plate is 780-790 ℃;
e. according to the screened target components and the annealing temperature range, preparing a third-generation TRIP automobile steel plate with the tensile strength of more than 980MPa and the product of strength and elongation of 30 GPa% in a laboratory:
according to the components and the annealing temperature corresponding to the point with the largest product in the area A screened in the step d, preparing a cast ingot by adopting a 20kg vacuum induction smelting furnace, and then cutting a steel block with the thickness of 30mm for hot rolling; rolling the steel plate to 3mm by multiple hot rolling, wherein the initial rolling temperature is 1150 ℃, and the final rolling temperature is above 900 ℃; then, cold-rolled to 1.2mm by pickling to obtain an experimental steel sheet, the composition of which is shown in the following Table 2;
table 2 experimental steel plate composition (mass%)
| C(％) | Mn(％) | Si(％) | Al(％) | Fe(％) |
| 0.3 | 1.90 | 1.00 | 0.60 | 96.20 |
Equally dividing the experimental steel plate into four same cold-rolled plates, respectively heating to two phase regions of 780 ℃, preserving heat for 3min for one of the two phase regions, preserving heat for 5min for the other three phase regions, then air-cooling the cold-rolled plates preserved for 3min to 430 ℃, preserving heat, and air-cooling to room temperature after 5 min; the other three cold-rolled plates which are kept warm for 5min are respectively cooled to 370 ℃, 400 ℃ and 430 ℃ in air and kept warm, after 5min, the cold-rolled plates are cooled to room temperature in air, finally, the experimental steel plate can obtain the Fe-Mn-Si-Al-C TRIP series third-generation transformation induced plasticity automobile steel plate with the strength-plasticity product of more than 980MPa and 30 GPa%, and the heat treatment process and the performance of the experimental steel plate are shown in the table 3:
TABLE 3 Experimental Steel plate Heat treatment Process and Properties
As can be seen from the data in Table 3, the tensile strength of the steel sheet obtained by the target composition and annealing temperature obtained by the experimental method of the present invention is 980MPa or more, and the product of strength and elongation is 30 GPa% or more.
With the target composition and annealing temperature obtained above as example 1, five further sets of comparative examples are given below, as shown in table 4:
table 4 composition and annealing temperature of steel sheets of example 1 and comparative examples 1 to 5
Comparative example 1 has the same annealing temperature as example 1 and the same contents of Mn, Si and Al, and different contents of C and Fe and C is not in the range of 0.29-0.30%;
comparative example 2 has the same annealing temperature as example 1 and the same contents of C, Si and Al, and different contents of Mn and Fe and Mn not in the range of 1.80-2.00%;
comparative example 3 has the same annealing temperature as example 1 and the same contents of C, Mn and Al, different contents of Si and Fe and Si not in the range of 1.00-1.10%;
comparative example 4 has the same annealing temperature as example 1 and the same contents of C, Mn and Si, and different contents of Al and Fe and Al is not in the range of 0.50-0.70%;
comparative example 5 has the same chemical composition as example 1 except for the annealing temperature, and the annealing temperature of comparative example 5 is not in the range of 780-790 ℃.
According to the chemical components and the annealing temperature of the comparative example, a 20kg vacuum induction melting furnace is adopted to prepare an ingot, and then a steel block with the thickness of 30mm is cut out for hot rolling; rolling the steel plate to 3mm by multiple hot rolling, wherein the initial rolling temperature is 1150 ℃, and the final rolling temperature is above 900 ℃; then acid washing and cold rolling to 1.2mm to obtain a primary steel plate; heating the primary steel plate to the annealing temperature of the two-phase region and preserving heat for 5min, then air-cooling to 400 ℃ and preserving heat, and air-cooling to room temperature after 5min, wherein the properties of the obtained steel plate are shown in Table 5:
TABLE 5 Properties of the Steel sheets obtained in comparative examples 1 to 5
| Tensile strength (MPa) | Elongation (%) | Product of strength and elongation (MPa%) | |
| Comparative example 1 | 1128.6 | 16.4 | 18509.0 |
| Comparative example 2 | 1030.5 | 25.0 | 25762.5 |
| Comparative example 3 | 1089.2 | 23.3 | 25378.4 |
| Comparative example 4 | 1068.5 | 22.9 | 24468.7 |
| Comparative example 5 | 1041.2 | 25.7 | 26758.8 |
It can be seen from the data in tables 5 and 3 that the properties of the resulting steel sheets are changed when the amount of one of the alloying elements is changed, and the properties of the resulting steel sheets are also different when the other conditions are the same and only the annealing temperature is different.
In addition to the above-mentioned compositions and annealing temperatures, the following five groups of examples were selected within the given a-zone chemical composition and annealing temperature range, as shown in table 6:
TABLE 6 chemical compositions and annealing temperatures for examples 2-6
According to the chemical compositions and annealing temperatures of examples 2 to 6 in Table 6, an ingot was prepared using a 20kg vacuum induction melting furnace and then a steel block having a thickness of 30mm was cut out for hot rolling; rolling the steel plate to 3mm by multiple hot rolling, wherein the initial rolling temperature is 1150 ℃, and the final rolling temperature is above 900 ℃; then acid washing and cold rolling to 1.2mm to obtain a primary steel plate; heating the primary steel plate to the annealing temperature of the two-phase region and preserving heat for 5min, then air-cooling to 400 ℃ and preserving heat, and air-cooling to room temperature after 5min, wherein the properties of the obtained steel plate are shown in Table 7:
TABLE 7 Properties of the steel sheets obtained in examples 2 to 6
| Tensile strength (MPa) | Elongation (%) | Product of strength and elongation (MPa%) | |
| Example 2 | 1031.1 | 29.1 | 30005.0 |
| Example 3 | 1046.2 | 28.7 | 30025.9 |
| Example 4 | 997.9 | 30.8 | 30735.3 |
| Example 5 | 1020.9 | 29.7 | 30320.7 |
| Example 6 | 1001.5 | 30.1 | 30145.2 |
As can be seen from the data in Table 7, by adopting the target components and the annealing temperature range determined by the invention, the experimental steel can obtain the Fe-Mn-Si-Al-C TRIP series third-generation transformation induced plasticity automobile steel plate with the tensile strength of more than 980MPa and the strength-elongation product of 30 GPa%.
The steel plate of the invention does not need to add trace elements, the total proportion of the alloy elements C, Mn, Si and Al is controlled within 5 percent, and the production cost of the steel plate can be reduced. The invention integrates the phase diagram thermodynamics and the diffusion dynamics calculation into an integral system to realize the scientific design of the target components and the process of the third-generation TRIP original steel and the short-period laboratory preparation, and is the creative work of the invention.
Claims (10)
1. The 30 GPa% -transformation induced Plasticity (PSR) automobile steel plate is characterized by comprising the following chemical components in percentage by mass: 0.29-0.30% of C, 1.80-2.00% of Mn, 1.00-1.10% of Si, 0.50-0.70% of Al and the balance of Fe; the critical annealing temperature of the steel plate is 780-790 ℃.
2. The 30 GPa% -transformation induced plasticity (STM) automobile steel plate according to claim 1, wherein the chemical composition of the steel plate comprises the following components in percentage by mass: 0.30% of C, 1.90% of Mn, 1.00% of Si, 0.60% of Al and 96.20% of Fe; the critical annealing temperature of the steel sheet was 780 ℃.
3. The 30 GPa% -transformation induced plasticity (STM) automobile steel plate according to claim 1, wherein the chemical composition of the steel plate comprises the following components in percentage by mass: 0.29 percent of C, 2.00 percent of Mn, 1.10 percent of Si, 0.50 percent of Al and 96.11 percent of Fe; the critical annealing temperature of the steel sheet was 780 ℃.
4. The 30 GPa% -transformation induced plasticity (STM) automobile steel plate according to claim 1, wherein the chemical composition of the steel plate comprises the following components in percentage by mass: 0.30% of C, 1.80% of Mn, 1.00% of Si, 0.60% of Al and 96.30% of Fe; the critical annealing temperature of the steel sheet was 780 ℃.
5. The 30 GPa% -transformation induced plasticity (STM) automobile steel plate according to claim 1, wherein the chemical composition of the steel plate comprises the following components in percentage by mass: 0.30 percent of C, 2.00 percent of Mn, 1.00 percent of Si, 0.70 percent of Al and 96.00 percent of Fe; the critical annealing temperature of the steel sheet was 790 ℃.
6. An experimental method for 30 GPa% -transformation induced plasticity (TPI) of an automobile steel plate, which is characterized by comprising the following steps:
a. the chemical components and the critical annealing temperature range of the experimental steel plate are drawn up:
the steel plate comprises the following chemical components in percentage by mass: 0.20 to 0.30 percent of C, 1.50 to 2.00 percent of Mn, 1.00 to 1.50 percent of Si, 0.50 to 1.00 percent of Al and the balance of Fe; the critical annealing temperature of the steel plate is 760-820 ℃;
b. determining characteristic parameters and writing a program file for developing integrated batch calculation:
utilizing a Thermo-Calc calculation software package, writing a program file capable of carrying out characteristic parameter calculation under different components and temperature conditions by adopting a TC-Python interface and using Python language, wherein the characteristic parameter 1 is AF and represents austenite content under different critical annealing temperatures, the characteristic parameter 2 is AC and represents carbon content in austenite under different critical annealing temperatures, and the characteristic parameter 3 is tCRepresents the time required for the diffusion of carbon elements in austenite to equilibrate; the key instructions in the program file comprise that thermodynamic and kinetic data are read simultaneously, and thermodynamic calculation of characteristic parameters 1 and 2 and kinetic calculation of characteristic parameter 3 of different alloy systems are completed; automatic assignment of alloy components and temperature is realized by adopting a cycle statement, and batch calculation is completed; limiting the calculation error range to obtain effective data, and finishing the output of the calculation result;
c. determining calculation conditions, operating a calculation program to screen components:
setting the calculation step length of each alloy element based on the component range determined in the step a, and acquiring AF and t by adopting a program file I for integrally calculating the characteristic parameters 1 and 3 in the step bCBased on the principle of maximizing the product of the two, selecting components corresponding to 20 percent of the first calculated result to carry out annealing temperature screening;
d. determining calculation conditions, operating a calculation program to screen annealing temperature:
setting the calculation step length of the annealing temperature based on the temperature range determined in the step a, adopting a program file II for integrally calculating a characteristic parameter 1 and a characteristic parameter 2 in the step b to obtain the calculation results of AF and AC, and selecting corresponding components and the annealing temperature as target components and the target annealing temperature based on the principle of maximizing the product of the AF and the AC, namely the chemical components of the steel plate comprise: 0.29-0.30% of C, 1.80-2.00% of Mn, 1.00-1.10% of Si, 0.50-0.70% of Al and the balance of Fe; the critical annealing temperature of the steel plate is 780-790 ℃;
e. preparing the transformation induced plasticity steel according to the screened target components and the target annealing temperature:
and d, according to the target components and the target annealing temperature screened in the step d, carrying out smelting, hot rolling, acid pickling and cold rolling and continuous annealing treatment to obtain the transformation induced plasticity steel with the tensile strength of over 980MPa and the strength-elongation product of 30 GPa%.
7. The experimental method of 30 GPa% -transformation induced plasticity (TOplasticity) of the automobile steel plate according to claim 6, wherein the smelting in the step e is to prepare an ingot by using a vacuum induction smelting furnace and then cut out a steel block with the thickness of 30 mm.
8. The experimental method of 30 GPa% -transformation induced plasticity (STM) of the automobile steel plate as recited in claim 6, wherein the hot rolling in the step e is to hot-roll the smelted steel block into a hot-rolled steel plate with a thickness of 3mm, the initial rolling temperature is 1150 ℃, and the final rolling temperature is above 900 ℃.
9. The experimental method for 30 GPa% -transformation induced plasticity (STM) of the automobile steel plate according to claim 6, wherein the pickling cold rolling in the step e is to cold-roll the hot-rolled steel plate obtained by the hot rolling treatment into a cold-rolled steel plate with the thickness of 1.2 mm.
10. The experimental method for 30 GPa% -percent phase change induced plasticity of automobile steel plate as recited in claim 6, wherein the continuous annealing treatment in step e is performed by heating the cold-rolled steel plate obtained by cold rolling to 780-790 ℃ for 3-5min, then cooling to 370-430 ℃ by air, and cooling to room temperature after 5 min.
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