Patent Grant
12215397
This application is a 371 U.S. National Phase of PCT International Application No. PCT/CN2019/120247 filed on Nov. 22, 2019, which claims benefit and priority to Chinese patent application no. CN 201811404464.3 filed on Nov. 23, 2018, the contents of both are incorporated by reference herein in their entireties.
The present disclosure relates to a steel and a method for manufacturing the same, in particular to a dual-phase steel and a method for manufacturing the same.
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.
In the prior art, a Chinese patent application document bearing a publication number of 105063510A, a publication date of Nov. 18, 2015, and a title of “High-plasticity 700 MPa 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.
Another Chinese patent application document bearing a publication number of 102766812A, a publication date of Nov. 7, 2012, and a title of “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.
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.
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.
One of the objects of the present disclosure 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.
In order to attain the above object, the present disclosure provides a cold-rolled dual-phase steel having a high yield ratio, comprising the following chemical elements in mass percentages:
In the technical solution of the present disclosure, the various chemical elements are designed according to the following principles:
Further, in the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure, the microstructure is a complex phase structure of martensite+ferrite+[NbxTiy(C,N)z] carbonitride.
Still further, in the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure, 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).
In the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure, 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 disclosure limits the phase proportion of the martensite in the cold-rolled dual-phase steel having a high yield ratio to 20-30%.
Further, in the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure, the [NbxTiy(C,N)z] carbonitride has an irregular spherical shape and is uniformly distributed in the ferrite grains. The phase proportion of the [NbxTiy(C,N)z] carbonitride is 5-10%, wherein x+y=z.
In the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure, the [NbxTiy(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.
If the phase proportion of the [NbxTiy(C,N)z] carbonitride is less than 5%, it cannot achieve the effect of increasing the yield ratio. After the phase proportion of the [NbxTiy(C,N)z] carbonitride is increased to be higher than 10%, the yield ratio of the steel will not change much. Therefore, the present disclosure limits the phase proportion of the [NbxTiy(C,N)z] carbonitride in the cold-rolled dual-phase steel having a high yield ratio to 5-10%.
Further, in the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure, the [NbxTiy(C,N)z] carbonitride has a size of less than 2 μm.
Further, in the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure, among the unavoidable impurities, the mass percentages of the P, S and N elements meet at least one of the following: P≤0.015%; S≤0.005%; N≤0.005%.
In the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure, among the unavoidable impurities, the mass percentages of the P, S and N elements meet at least one of the following: P≤0.015%; S≤0.005%; N≤0.005%, according to the following principles:
Further, the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure has a yield ratio of greater than 0.8.
Further, the cold-rolled dual-phase steel having a high yield ratio according to the present disclosure has a yield strength of 550-660 MPa, a tensile strength of ≥660 MPa, and an elongation at break of ≥15%.
Accordingly, another object of the present disclosure 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.
To attain the above object, the present disclosure proposes a method for manufacturing a cold-rolled dual-phase steel having a high yield ratio, comprising the following steps:
In the manufacturing method of the present disclosure, 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.
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 disclosure, in Step (4), the annealing soaking temperature is controlled to be 750-790° C.; the annealing time is 40-200 s; 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 100-400 s.
Further, in the manufacturing method according to the present disclosure, 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%.
In the manufacturing method according to the present disclosure, 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 disclosure, in Step (5), the temper rolling reduction rate is controlled to be 0.3-1.0%.
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 disclosure have the following beneficial effects:
The cold-rolled dual-phase steel having a high yield ratio according to the present disclosure 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 disclosure.
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.
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):
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.
As can be seen from Table 3, the high-yield-ratio cold-rolled dual-phase steels of Examples 1-6 and Comparative Examples 1-15 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 disclosure has the advantages of high strength, low carbon equivalent and high yield ratio.
As can be seen from
It's to be noted that the prior art portions in the protection scope of the present disclosure are not limited to the examples set forth in the present application file. All the prior art contents not contradictory to the technical solution of the present disclosure, including but not limited to prior patent literature, prior publications, prior public uses and the like, may all be incorporated into the protection scope of the present disclosure.
In addition, the ways in which the various technical features of the present disclosure are combined are not limited to the ways recited in the claims of the present disclosure or the ways described in the specific examples. All the technical features recited in the present disclosure may be combined or integrated freely in any manner, unless contradictions are resulted.
It should also be noted that the above-listed Examples are only specific embodiments of the present disclosure. Obviously, the present disclosure is not limited to the above Examples, and similar changes or modifications can be directly derived from or easily associated with the disclosure of the present disclosure by those skilled in the art, and should fall within the protection scope of the present disclosure.
| Number | Date | Country | Kind |
|---|---|---|---|
| 201811404464.3 | Nov 2018 | CN | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2019/120247 | 11/22/2019 | WO |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2020/103927 | 5/28/2020 | WO | A |
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|---|---|---|---|
| 20130213529 | Kimura | Aug 2013 | A1 |
| 20150017472 | Kimura et al. | Jan 2015 | A1 |
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| Number | Date | Country | |
|---|---|---|---|
| 20220010394 A1 | Jan 2022 | US |
