COLD-ROLLED DUAL-PHASE STEEL SHEET WITH HIGH EXTENSION RATIO AND MANUFACTURING METHOD FOR IT

Description

Technical Field

[0001] The present invention relates to a steel plate and a method for manufacturing the same, in particular to a dual-phase steel plate and a method for manufacturing the same.Background Art

[0002] As weight reduction and safety are required in the automotive industry, the market has an increasing demand for higher-strength steel plates. Dual-phase steel has excellent properties such as low yield strength, high tensile strength and high initial work hardening rate, and is widely used in the production of automotive parts. In view of the rebound of some automotive parts such as car seats in practical use, there is a high demand for 70 kg grade dual-phase steel having a high yield ratio (a yield ratio of greater than 0.8) in the market.

[0003] In the prior art, CN 105063510 A, published November 18, 2015, "High-plasticity 700MPa grade cold-rolled weather-resistant dual-phase steel and preparation method thereof' discloses a weather-resistant dual-phase steel having a chemical composition in mass percentages of 0.07-0.15% C, 0.30-0.80% Si, 1.40-1.70% Mn, <0.01% P, <0.01% S, 0.40-0.60% Cr, 0.20-0.30% Cu, 0.15-0.30% Ni, 0.02-0.05% Nb, 0.02-0.05% Ti, and a balance of Fe and other unavoidable impurities. The method for manufacturing the steel plate comprises heat preservation at 1200°C, finish rolling at 950-1050°C, annealing at 780-820°C, rapid cooling from 660-720°C at a rapid cooling rate of 40°C / s, and termination of rapid cooling at a temperature of 320°C, wherein a 729-747 MPa steel plate having a yield strength of 328-346 MPa and an elongation of 21-22% is obtained. In the design of the composition of the steel plate, relatively large amounts of alloying elements such as Cr, Cu, Ni are used, and the content of Si is relatively high.

[0004] Further, CN 102766812 A, published November 7, 2012, "700 MPa grade low yield ratio hot-rolled dual-phase steel plate and manufacturing method thereof' discloses a 700 MPa grade low yield ratio hot-rolled dual-phase steel plate having a chemical composition in mass percentages of 0.06%-0.09% C, 1.0%-1.2% Si, 1.10%-1.30% Mn, 0.020%-0.050% Al, 0.4%-0.6% Cr, and a balance of Fe. The cast slab used for manufacturing the steel plate is heated in a heating furnace and rolled through a hot continuous rolling unit. After rolling, a laminar cooling process is used for staged cooling, and an ultra-high strength hot-rolled dual-phase steel having a tensile strength of 700 MPa is obtained at the end.

[0005] Moreover, CN 105274432 A and US 9322091 B2 disclose steel plates and manufacturing methods of the same according to prior art.

[0006] In summary, the dual-phase steel products in the prior art are mainly classified into two types: (1) cold-rolled, annealed dual-phase steel plates containing relatively large amounts of such elements as Cu, Ni, Cr, etc.; and (2) low-yield ratio hot-rolled steel plates. These two types of products contain relatively large amounts of alloying elements, while the yield ratio is rather low.

[0007] In view of this situation, it is desirable to provide a dual-phase steel that contains less alloying elements and has a higher yield ratio to meet the market demand for dual-phase steel having a high yield ratio.Summary

[0008] One of the objects of the present invention is to provide a cold-rolled dual-phase steel having a high yield ratio, wherein the dual-phase steel has a low cost, contains less alloying elements, and has a higher strength and a higher yield ratio, so that it can satisfy the market demand for dual-phase steel having a high yield ratio.

[0009] The invention is defined in the appended claims.

[0010] In order to attain the above object, the present invention provides a cold-rolled dual-phase steel plate having a high yield ratio, comprising the following chemical elements in mass percentages: C: 0.05-0.08%, Mn: 0.9-1.2%, Si: 0.1-0.6%, Nb: 0.030-0.060%, Ti: 0.030-0.060%, Al: 0.015-0.045%, P ≤ 0.015%, S ≤ 0.005%, N ≤ 0.005%, and a balance of Fe and other unavoidable impurities wherein the cold-rolled dual-phase steel plate has a microstructure which is a complex phase structure of martensite+ferrite+[Nb x Ti y (C,N) z ] carbonitride, wherein x + y = z; the martensite has a phase proportion of 20-30%, and the martensite is in the shape of long strips-islands; the [Nb x Ti y (C,N) z ] carbonitride has an irregular spherical shape and is uniformly distributed in ferrite grains, and the [Nb x Ti y (C,N) z ] carbonitride has a phase proportion of 5-10%; and the cold-rolled dual-phase steel plate has a yield strength of 550-660 MPa, a tensile strength of ≥ 660 MPa, an elongation at break of ≥ 15%, and a yield ratio of greater than 0.8.

[0011] In the technical solution of the present invention, the various chemical elements are designed according to the following principles: C: In the high-yield-ratio cold-rolled dual-phase steel of the present invention, carbon is a solid solution strengthening element which can guarantee the high strength of the material, increase the strength of martensite, and influence the content of martensite. If the mass percentage of carbon is too high or too low, it is disadvantageous to the properties of the steel. Therefore, the present invention limits the mass percentage of the carbon element in the high-yield-ratio cold-rolled dual-phase steel to 0.05-0.08%. Mn: Manganese is an element that can strongly improve the hardenability of austenite and effectively increase the strength of steel, but it is not good for welding. If the mass percentage of Mn is lower than 0.9%, the strength of the steel will be insufficient; and if the mass percentage of Mn is higher than 1.2%, the strength of the steel will be too high. Therefore, the present invention limits the mass percentage of Mn in the high-yield-ratio cold-rolled dual-phase steel to 0.9-1.2%. Si: Silicon is a solid solution strengthening element. On the one hand, it can increase the strength of the material. On the other hand, it can accelerate segregation of carbon to austenite, purify ferrite, and function to improve the elongation of the steel. At the same time, Si has a great influence on the structure of the steel. Si tends to accumulate on the surface to form an oxide film (red rust) that is difficult to remove. If the mass percentage of Si is less than 0.1%, the strength of the steel will be insufficient; and if the mass percentage of Si is higher than 0.6%, the surface quality of the steel will be easily affected. Therefore, the present invention limits the mass percentage of Si in the high-yield-ratio cold-rolled dual-phase steel to 0.1-0.6%. Nb: Niobium is an element for precipitation of carbonitrides. It can refine grains and precipitate carbonitrides, and improve the strength of the material. Therefore, the present invention limits the mass percentage of Nb in the high-yield-ratio cold-rolled dual phase steel to 0.030-0.060%. Ti: Titanium is an element for precipitation of carbonitrides. It is used for fixing nitrogen and refining grains. It is conducive to increasing the yield strength of the material. Therefore, the present invention limits the mass percentage of Ti in the high-yield-ratio cold-rolled dual-phase steel to 0.030-0.060%. Al: Al serves to remove oxygen and refine grains in steel. Therefore, the present invention limits the mass percentage of Al in the high-yield-ratio cold-rolled dual-phase steel to 0.015-0.045%.

[0012] Further, in the cold-rolled dual-phase steel having a high yield ratio according to the present invention, the microstructure is a complex phase structure of martensite+ferrite+[Nb x Ti y (C,N) z ] carbonitride.

[0013] Still further, in the cold-rolled dual-phase steel having a high yield ratio according to the present invention, the phase proportion of the martensite is 20-30%, and the martensite is in the shape of long strips-islands (it is island-shaped when observed under a low-magnification metallographic microscope; it is lath or long strip-shaped when observing the fine structure of the martensite).

[0014] In the cold-rolled dual-phase steel having a high yield ratio according to the present invention, the phase proportion of the martensite is 20-30%, and the martensite is in the shape of long strips-islands. The martensite has a function of phase transformation strengthening. If the phase proportion of the martensite is too high or too low, the strength of the steel will be unduly high or low. Therefore, the present invention limits the phase proportion of the martensite in the cold-rolled dual-phase steel having a high yield ratio to 20-30%.

[0015] Further, in the cold-rolled dual-phase steel having a high yield ratio according to the present invention, the [Nb x Ti y (C,N) z ] carbonitride has an irregular spherical shape and is uniformly distributed in the ferrite grains. The phase proportion of the [Nb x Ti y (C,N) z ] carbonitride is 5-10%, wherein x+y=z.

[0016] In the cold-rolled dual-phase steel having a high yield ratio according to the present invention, the [Nb x Ti y (C,N) z ] carbonitride has an irregular spherical shape and is uniformly distributed in the ferrite grains to achieve dispersion precipitation strengthening and increase the yield ratio.

[0017] If the phase proportion of the [Nb x Ti y (C,N) z ] carbonitride is less than 5%, it cannot achieve the effect of increasing the yield ratio. After the phase proportion of the [Nb x Ti y (C,N) z ] carbonitride is increased to be higher than 10%, the yield ratio of the steel will not change much. Therefore, the present invention limits the phase proportion of the [Nb x Ti y (C,N) z ] carbonitride in the cold-rolled dual-phase steel having a high yield ratio to 5-10%.

[0018] Further, in the cold-rolled dual-phase steel having a high yield ratio according to the present invention, the [Nb x Ti y (C,N) z ] carbonitride has a size of less than 2 µm.

[0019] In the cold-rolled dual-phase steel having a high yield ratio according to the present invention, among the unavoidable impurities, the mass percentages of the P, S and N elements are: P≤0.015%; S≤0.005%; N≤0.005%, according to the following principles: P: P is an impurity element in steel. The lower the mass percentage of P, the better. With the requirements of both the production cost and process conditions taken into account, the present invention limits the mass percentage of P in the cold-rolled dual-phase steel having a high yield ratio to P≤ 0.015%.

[0020] S: S is an impurity element in steel. The lower the mass percentage of S, the better. With the requirements of both the production cost and process conditions taken into account, the present invention limits the mass percentage of S in the cold-rolled dual-phase steel having a high yield ratio to S≤ 0.005%.

[0021] N: N is an impurity element in steel. If its amount is too high, the surface of a slab tends to crack. Therefore, the lower the mass percentage of N, the better. With the requirements of both the production cost and process conditions taken into account, the present invention limits the mass percentage of N in the cold-rolled dual-phase steel having a high yield ratio to N≤ 0.005%.

[0022] Further, the cold-rolled dual-phase steel having a high yield ratio according to the present invention has a yield ratio of greater than 0.8.

[0023] Further, the cold-rolled dual-phase steel having a high yield ratio according to the present invention has a yield strength of 550-660 MPa, a tensile strength of ≥660 MPa, and an elongation at break of ≥ 15%.

[0024] Accordingly, another object of the present invention is to provide a method for manufacturing the above-mentioned cold-rolled dual-phase steel having a high yield ratio. The cold-rolled dual-phase steel having a high-yield ratio obtained by this method has a higher strength and a higher yield ratio.

[0025] To attain the above object, the present invention proposes a method for manufacturing a cold-rolled dual-phase steel plate having a high yield ratio, comprising the following steps: (1) Smelting and casting; (2) Hot rolling: controlling a cast blank for soaking at a temperature of 1200-1250°C; rolling with a finish rolling temperature being controlled at 840-930°C; cooling at a rate of 20-70°C / s after the rolling; then coiling with a coiling temperature being controlled at 570-630°C; (3) Cold rolling with a cold rolling reduction rate is controlled to be 50-70%; (4) Annealing: annealing at an annealing soaking temperature of 750-790°C for an annealing time of 40-200s; and then cooling at a rate of 30-80°C / s, wherein the cooling begins at a temperature of 650-730°C, an aging temperature is 200-260°C, and an over-aging time is 100-400s; and (5) Temper rolling with a temper rolling reduction rate being controlled to be 0.3-1.0%.

[0026] In the manufacturing method of the present invention, in Step (2), in order to ensure the stability of the rolling load, the temperature for heating the cast blank is controlled to be 1200°C or higher. On the other hand, with the solid solubilities of Ti(C, N) and Nb(C, N) ) in austenite taken into consideration, in order to ensure that the carbonitrides Ti(C,N) and Nb(C,N) can be precipitated at a high temperature, the upper limit of the temperature for heating the cast blank is controlled to be 1250°C. That is, the cast blank is controlled to be soaked at a temperature of 1200-1250°C, preferably for a soaking time of 5-6 hours, followed by rolling. In addition, in view of the formability after the annealing and the possibility that coarse grains will result in a nonuniform structure, the finish rolling temperature is controlled to be 840-930°C. After the rolling, cooling is performed at a rate of 20-70°C / s, preferably to 570-630°C, and then coiling is performed. The coiling temperature may be viewed as the precipitation temperature of the carbonitrides in ferrite, and the precipitation temperature is one of the main factors that control the size of the precipitates. The lower the precipitation temperature, the smaller the critical nucleus size for precipitation nucleation, and the finer the precipitates. In addition, the diffusion of Ti and Nb is slow. As a result, the growth rate of Ti and Nb is also small. From the perspective of kinetics, due to the high diffusion activation energies of Ti and Nb, the precipitation process of Ti(C,N) and Nb(C,N) is a result of long-range diffusion, and full precipitation needs sufficient time. If the cooling rate is too fast, the precipitation process of the second phase particles will be inhibited, and at the same time, the solid solution content will be increased. This is unfavorable for the precipitation process of Ti(C,N) and Nb(C,N), and the precipitation amount will be reduced. The coiling temperature is preferably 570-630°C.

[0027] In addition, in Step (4), the annealing soaking temperature and annealing time determine the degree of austenitization, and ultimately determine the phase proportions of martensite and ferrite in the steel structure. If the annealing soaking temperature is too high, the phase proportion of martensite will be so high that the strength of the final steel plate will be unduly high. If the annealing soaking temperature is too low, the phase proportion of martensite will be so low that the strength of the final steel plate will be unduly low. In addition, if the annealing soaking time is too short, the degree of austenitization will be insufficient; and if the annealing soaking time is too long, the austenite grains will become coarse. Therefore, in the manufacturing method according to the present invention, in Step (4), the annealing soaking temperature is controlled to be 750-790°C; the annealing time is 40-200s; and then cooling is performed at a rate of 30-80°C / s. The starting temperature of the cooling is 650-730°C; the aging temperature is 200-260°C; and the over-aging time is 100-400s.

[0028] Further, in the manufacturing method according to the present invention, in Step (3), the cold rolling reduction rate is controlled to be 50-70%; and / or in Step (5), the temper rolling reduction rate is controlled to be 0.3-1.0%.

[0029] In the manufacturing method according to the present invention, in Step (3), in some embodiments, the mill scale on the steel surface may be removed by pickling, and then cold rolling is performed. In order to produce more polygonal ferrite in the steel structure, the cold rolling reduction rate is controlled to 50-70%. In addition, in Step (5), in order to ensure the flatness of the steel plate, the steel plate needs to be temper rolled to a certain degree. If it's temper rolled excessively, the yield strength will increase unduly. Therefore, in the manufacturing method according to the present invention, in Step (5), the temper rolling reduction rate is controlled to be 0.3-1.0%.

[0030] Compared with the prior art, the cold-rolled dual-phase steel having a high yield ratio and the manufacturing method thereof according to the present invention have the following beneficial effects: (1) The cold-rolled dual-phase steel having a high yield ratio according to the present invention comprises less alloying elements (for example, it's free of Cr, Ni, Cu, and the Si content is also low), has a low cost, and is advantageous for improving the surface quality and phosphorization property of the cold-rolled dual-phase steel having a high yield ratio according to the present invention, such that it meets the requirements of automobile manufacturing. (2) The cold-rolled dual-phase steel having a high-yield ratio according to the present invention has a higher strength and a higher yield ratio as well as a lower carbon equivalent, widely useful for structural parts and safety parts in the automobile industry. (3) The cold-rolled dual-phase steel having a high yield ratio according to the present invention has a yield ratio of greater than 0.8, a yield strength of 550-660 MPa, a tensile strength of ≥660 MPa, and an elongation at break of ≥15%. (4) The method for manufacturing the cold-rolled dual-phase steel having a high yield ratio according to the present invention also has the above-mentioned beneficial effects, which will not be repeated here. Description of the Drawings

[0031] Fig. 1 is a microstructure diagram of a cold-rolled dual-phase steel having a high yield ratio in Example 2.Detailed Description

[0032] The cold-rolled dual-phase steel having a high yield ratio according to the present invention and the method for manufacturing the same will be further explained and illustrated with reference to the accompanying drawing of the specification and the specific examples. Nonetheless, the explanation and illustration are not intended to unduly limit the technical solution of the present invention.Examples 1-6 and Comparative Examples 1-15

[0033] Table 1-1 and Table 1-2 list the mass percentages (wt%) of the chemical elements in the high-yield-ratio cold-rolled dual-phase steels of Examples 1-6 and Comparative Examples 1-15. Table 1-1. (wt%, the balance is Fe and other unavoidable impurities except for P, S and N)No.CSiMnPSNbTiEx. 10.0520.331.050.0140.0030.0580.044Ex. 20.0550.180.990.0110.0040.0480.038Ex. 30.0610.351.170.0090.0030.0420.045Ex. 40.0660.241.010.0120.0020.0390.036Ex. 50.0740.180.920.010.0010.0450.033Ex. 60.0780.350.980.0130.0050.0340.047Comp. Ex. 10.044 0.291.080.0110.0020.0440.043Comp. Ex. 20.092 0.361.120.0090.0040.0380.045Comp. Ex. 30.0650.270.78 0.0120.0040.0430.035Comp. Ex. 40.0560.251.26 0.010.0020.0370.043Comp. Ex. 50.0750.381.080.0110.0050.025 0.056Comp. Ex. 60.0580.291.190.0080.0020.065 0.045Comp. Ex. 70.0660.471.110.0130.0040.0380.023 Comp. Ex. 80.0620.520.960.0120.0030.0550.068 Comp. Ex. 90.0730.291.080.0110.0020.0440.043Comp. Ex. 100.0680.331.060.0090.0010.0410.039Comp. Ex. 110.0710.460.950.0120.0040.0360.033Comp. Ex. 120.0620.321.050.0130.0020.0320.037Comp. Ex. 130.0680.290.990.0090.0030.0390.041Comp. Ex. 140.0720.401.120.0010.0010.0480.051Comp. Ex. 150.0770.381.150.0140.0030.0430.046 Table 1-2. (wt%, the balance is Fe and other unavoidable impurities except for P, S and N) No.AlNC+(Mn+Si) / 6phase proportion of ferrite (%)phase proportion of martensite (%)phase proportion of [NbxTiy(C,N)z] carbonitride (%)average size of [NbxTiy(C,N)z] carbonitride (µm)Ex. 10.0210.00350.28269.224.36.51.2Ex. 20.0330.00440.25069.922.77.40.8Ex. 30.0280.00370.31464.628.27.20.7Ex. 40.0420.00280.27469.621.68.81.0Ex. 50.0380.00320.25766.524.59.01.5Ex. 60.0170.00470.30068.226.25.60.6Comp. Ex. 10.0340.00280.27277.615.6 6.80.8Comp. Ex. 20.0270.00440.3395438.5 7.51.1Comp. Ex. 30.0320.00370.24079.212.5 8.30.9Comp. Ex. 40.0230.00280.3085141.2 7.81.6Comp. Ex. 50.0350.00420.3187025.64.4 2.8 Comp. Ex. 60.0420.00360.30567.918.913.2 0.4Comp. Ex. 70.0280.00420.32974.721.53.8 3.0 Comp. Ex. 80.0260.00360.30962.822.914.3 0.5Comp. Ex. 90.0340.00280.30176.716.7 6.60.6Comp. Ex. 100.0220.00290.30055.537.4 7.13.1 Comp. Ex. 110.0430.00330.30669.425.84.8 1.0Comp. Ex. 120.0410.00440.29070.624.94.5 1.2Comp. Ex. 130.0380.00220.28174.916.8 8.30.9Comp. Ex. 140.0290.00350.32555.636.8 7.61.5Comp. Ex. 150.0300.00470.33269.224.36.51.4

[0034] The method for manufacturing the high-yield-ratio cold-rolled dual-phase steels of Examples 1-6 and Comparative Examples 1-15 is as follows (the specific process parameters are listed in Table 2-1 and Table 2-2): (1) Smelting and casting: Smelting and casting were carried out with the chemical elements listed in Table 1-1 and Table 1-2. (2) Hot rolling: A cast blank was controlled for soaking at a temperature of 1200-1250°C for 5-6 hours, and then rolled, wherein the finish rolling temperature was controlled at 840-930°C. After the rolling, the steel was cooled at a rate of 20-70°C / s to 570-630°C. Then, the steel was coiled, wherein the coiling temperature was controlled at 570-630°C. (3) Cold rolling: The cold rolling reduction rate was controlled at 50-70%. (4) Annealing: The annealing soaking temperature was 750-790°C; and the annealing time was 40-200s. Then, the steel was cooled at a rate of 30-80°C / s, wherein the cooling began at a temperature of 650-730°C. The aging temperature was 200-260°C, and the over-aging time was 100-400s. (5) Temper rolling: The temper rolling reduction rate was 0.3-1.0%. Table 2-1. Specific process parameters for the method for manufacturing the high-yield-ratio cold-rolled dual-phase steels of Examples 1-6 and Comparative Examples 1-15 No.Step (2)Step (3)Soaking Temperature (°C)Finish Rolling Temperature (°C)Cooling Rate (°C / s)Coiling Temperature (°C)Cold Rolling Reduction Rate (%)Ex. 112409254058562Ex. 212308603059070Ex. 312509006061565Ex. 412159055562555Ex. 512208555058058Ex. 612309253057065Comp. Ex. 112308906059550Comp. Ex. 212208756562064Comp. Ex. 312009157058068Comp. Ex. 412408453559056Comp. Ex. 512508803057055Comp. Ex. 612009106562060Comp. Ex. 712458603059562Comp. Ex. 81225935 4560554Comp. Ex. 91190 9054059062Comp. Ex. 101265 9003557550Comp. Ex. 11124585560550 55Comp. Ex. 12122086565640 65Comp. Ex. 1312258955560068Comp. Ex. 1412308754561070Comp. Ex. 1512409256558552 Table 2-2. Specific process parameters for the method for manufacturing the high-yield-ratio cold-rolled dual-phase steels of Examples 1-6 and Comparative Examples 1-15 No.Step (4)Step (5)Annealing Soaking Temperature (°C)Annealing Time (s)Cooling Rate (°C / s)Initial Cooling Temperature (°C)Aging Temperature (°C)Over-aging Time (s)Temper Rolling Reduction Rate (%)Ex. 176540757002301000.8Ex. 278080606602402000.6Ex. 3785120556502004000.9Ex. 4774160707302502001.0Ex. 578240456702301000.5Ex. 675880706602403000.9Comp. Ex. 1778120456502403000.6Comp. Ex. 2785160506702004000.7Comp. Ex. 375540606602502000.8Comp. Ex. 479080556502301000.9Comp. Ex. 5775120357302403001.0Comp. Ex. 6768160806702004000.5Comp. Ex. 778680656702603000.8Comp. Ex. 8766100306602202000.6Comp. Ex. 977540457202502000.7Comp. Ex. 1078580707002301000.8Comp. Ex. 11768120456802403000.5Comp. Ex. 12755160506502402000.9Comp. Ex. 13745 40456952001001.0Comp. Ex. 14805 80557052503000.8Comp. Ex. 15774160607302303001.2

[0035] The high-yield-ratio cold-rolled dual-phase steels of Examples 1-6 and Comparative Examples 1-15 were tested for their properties. The test results are listed in Table 3. Table 3No.Yield Strength (MPa)Tensile Strength (MPa)Elongation At Break (%)Yield RatioEx. 158069019.50.84Ex. 257568618.40.84Ex. 360472018.20.84Ex. 465276415.60.85Ex. 564375115.30.86Ex. 662870817.50.89Comp. Ex. 1525 650 21.20.81Comp. Ex. 2693 79014.3 0.88Comp. Ex. 3508 632 22.60.80Comp. Ex. 4685 81413.8 0.84Comp. Ex. 556475416.10.75 Comp. Ex. 663272417.60.87Comp. Ex. 755570818.80.78 Comp. Ex. 860269719.30.86Comp. Ex. 9532 646 21.80.82Comp. Ex. 10683 79614.1 0.86Comp. Ex. 1156473417.90.77 Comp. Ex. 1256872717.60.78 Comp. Ex. 13565638 21.70.89Comp. Ex. 14684 78514.6 0.87Comp. Ex. 15699 77415.20.90

[0036] As can be seen from Table 3, the high-yield-ratio cold-rolled dual-phase steels of Examples 1-6 have a tensile strength of ≥ 660 MPa, an elongation at break of ≥ 15%, and a yield ratio of greater than 0.8. Thus, it can be seen that the cold-rolled dual-phase steel having a high yield ratio according to the present invention has the advantages of high strength, low carbon equivalent and high yield ratio.

[0037] Fig. 1 is a microstructure diagram of a cold-rolled dual-phase steel having a high yield ratio in Example 2.

[0038] As can be seen from Fig. 1, the microstructure of the high-yield-ratio cold-rolled dual-phase steel of Example 2 is a complex phase structure of martensite + ferrite + [Nb x Ti y (C,N) z ] carbonitride, wherein the martensite has a phase proportion of 20-30%, and has a function of phase transformation strengthening. The martensite structure is in the shape of long strips-islands (it is island-shaped when observed under a low-magnification metallographic microscope; it is lath or long strip-shaped when observing the fine structure of the martensite). Meanwhile, the [Nb x Ti y (C,N) z ] carbonitride has an irregular spherical shape and is uniformly distributed in the ferrite grains. The carbonitride has a size of less than 2 µm, and has a function of dispersion precipitation strengthening in the structure.

[0039] It should be noted that the above-listed Examples are only specific embodiments of the present invention. Obviously, the present invention is not limited to the above Examples.

Claims

1. A cold-rolled dual-phase steel plate having a high yield ratio, comprising the following chemical elements in mass percentages: C: 0.05-0.08%, Mn: 0.9-1.2%, Si: 0.1-0.6%, Nb: 0.030-0.060%, Ti: 0.030-0.060%, Al: 0.015-0.045%, P ≤ 0.015%, S ≤ 0.005%, N ≤ 0.005%, and a balance of Fe and other unavoidable impurities; wherein the cold-rolled dual-phase steel plate has a microstructure which is a complex phase structure of martensite+ferrite+[NbxTiy(C,N)z] carbonitride, wherein x + y = z; the martensite has a phase proportion of 20-30%, and the martensite is in the shape of long strips-islands; the [NbxTiy(C,N)z] carbonitride has an irregular spherical shape and is uniformly distributed in ferrite grains, and the [NbxTiy(C,N)z] carbonitride has a phase proportion of 5-10%; and the cold-rolled dual-phase steel plate has a yield strength of 550-660 MPa, a tensile strength of ≥ 660 MPa, an elongation at break of ≥ 15%, and a yield ratio of greater than 0.8.

2. The cold-rolled dual-phase steel plate having a high yield ratio according to claim 1, wherein the [NbxTiy(C,N)z] carbonitride has a size of less than 2 µm.

3. A manufacturing method for the cold-rolled dual-phase steel plate having a high yield ratio according to claim 1 or 2, wherein the method comprises the following steps: (1) Smelting and casting; (2) Hot rolling: controlling a cast blank for soaking at a temperature of 1200-1250°C; rolling with a finish rolling temperature being controlled at 840-930°C; cooling at a rate of 20-70°C / s after the rolling; then coiling with a coiling temperature being controlled at 570-630°C; (3) Cold rolling with a cold rolling reduction rate is controlled to be 50-70%; (4) Annealing: annealing at an annealing soaking temperature of 750-790°C for an annealing time of 40-200s; and then cooling at a rate of 30-80°C / s, wherein the cooling begins at a temperature of 650-730°C, an aging temperature is 200-260°C, and an over-aging time is 100-400s; and (5) Temper rolling with a temper rolling reduction rate being controlled to be 0.3-1.0%.

4. The manufacturing method according to claim 3, wherein in Step (2), a soaking time is 5-6 hours; the steel is cooled to 570-630 °C after the rolling; and then the coiling is performed.