CN109487063B - Controlled rolling and controlled cooling process for Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel - Google Patents
Controlled rolling and controlled cooling process for Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel Download PDFInfo
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Abstract
The invention relates to a controlled rolling and cooling process for Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel, belonging to the technical field of steel rolling. Heating Ti-V-N composite microalloyed low-carbon steel to 1230-1280 ℃, preserving heat, cooling to 1160-1050 ℃, starting rolling in an austenite recrystallization region, rolling the Ti-V-N composite microalloyed low-carbon steel rolled in the recrystallization region in a non-recrystallization region, and quickly cooling after rolling: cooling to 550 +/-30 ℃ at a cooling speed of more than 50 ℃/s, preserving heat for 30 minutes, and then cooling to room temperature. According to the invention, through the rolling process of two stages of recrystallization and non-recrystallization regions and the ultra-fast cooling, not only is repeated recrystallization of austenite promoted and grains refined, but also a large amount of deformation energy storage is stored in steel, so that a large amount of nanoscale second-phase particles are separated out from the steel, the fine grain strengthening increment and precipitation strengthening increment of steel are improved, and the yield strength of the steel is greatly increased.
Description
Technical Field
The invention relates to a controlled rolling and cooling process for Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel, belonging to the technical field of steel rolling.
Background
In recent years, with the increasing resource and environmental pressure, environmental protection and energy conservation are more and more paid attention by the steel industry. In order to meet the requirements of weight reduction and consumption reduction in various industries, the development of high-strength steel is widely concerned at home and abroad. At present, the microalloying technology combined with the TMCP process is one of effective ways for researching and developing low-cost high-strength steel. Under the conditions of proper components and TMCP (thermal mechanical control processing) process, Ti can not only refine grains by dispersing and separating out TiC particle pinning grain boundaries, but also can hinder dislocation movement by deformation induction separation, so that larger precipitation strengthening increment is generated, and the yield strength of steel is improved. However, the single titanium microalloying technology is less applied at present, mainly because Ti has active property and is easy to combine with elements such as O, S in steel to form inclusions with larger size, so that the effective Ti content in the steel is reduced; meanwhile, Ti (C, N) has low solid solubility in steel, is very sensitive to precipitation temperature and cooling rate, is precipitated and precipitated in a high temperature range, is easy to coarsen and grow up in the subsequent process, and loses the precipitation strengthening effect; and Ti precipitates with larger sizes are easy to generate continuous distribution at grain boundaries, so that the strength of the grain boundaries is reduced, and the plastic toughness of the steel is seriously reduced.
In order to improve the comprehensive mechanical property of Ti microalloyed low carbon steel and improve the stability of steel structure, the Chinese invention patent CN108374131 discloses a controlled rolling and controlled cooling process method of ultrafine austenite grains of Ti-Mo composite microalloyed steel, which promotes multiple times of austenite recrystallization by three-pass rolling with different rolling reduction and different strain rates to obtain uniform ultrafine austenite grain structure. However, the number of the nano-scale precipitation phases in the steel structure is limited, and the precipitation strengthening increment is not obviously improved. Chinese invention patent CN108374131 discloses a controlled rolling and cooling process for H-shaped steel with yield strength of 500MPa, the internal structure of which is polygonal ferrite, pearlite, acicular ferrite and a small amount of granular bainite, and the yield strength of which reaches 500 MPa. However, the steel does not contain Ti element, and precipitation strengthening increment is limited, so that the design of the controlled rolling and cooling process of Ti microalloyed low-carbon steel is provided with limited reference. The invention patent CN102500625 discloses a novel TMCP process, which can effectively control the grain growth after the rolling in the complete recrystallization zone, and obtain finer grain structure. However, the process is mainly designed for refining the grain structure in the steel, the precipitation and distribution of a precipitation phase in the steel are basically not considered to be regulated and controlled, and the precipitation strengthening increment is not obvious.
Therefore, aiming at the problems in the TMCP process, a matched TMCP process for regulating and controlling the precipitation of the nano-scale precipitate phase in the steel is needed to be designed for the Ti-V-N microalloyed low-carbon steel, so that the precipitation strengthening increment of the steel is improved, and the Ti-V-N composite microalloyed low-carbon high-strength steel with stable structure performance and large precipitation strengthening increment is obtained.
Disclosure of Invention
The invention aims to provide a controlled rolling and controlled cooling process of Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel, which comprises the steps of firstly rolling in a recrystallization region, so that austenite grains can be recrystallized for multiple times, and the austenite grains are refined; then rolling in a non-recrystallization area, so that deformation energy storage in steel can be increased, and a deformation induced precipitated phase is generated; after rolling, the super-fast cooling and the isothermal treatment are carried out after the cooling to a certain temperature, so that the supercooling degree in steel can be increased, the phase change driving force of the second phase precipitation is improved, and an interphase precipitated phase and a ferrite intragranular dispersion precipitated phase are increased. The process specifically comprises the following steps:
(1) and (3) rolling in a recrystallization area: heating Ti-V-N composite microalloyed low carbon steel to 1230-1280 ℃, preserving the heat for 600s, then cooling to 1160-1050 ℃, and starting the rolling of an austenite recrystallization region, wherein the cooling speed is 10 ℃/s; the strain rate of the first pass rolling is 10-15 s-1And the deformation is 40%, rolling for the second time is carried out after the interval of 1-5 s, and the rolling parameters are as follows: strain rate of 5-10 s-1The deformation is 20 percent, and the finishing temperature is controlled to be more than 980 ℃;
(2) rolling in a non-recrystallization area: cooling the Ti-V-N composite microalloyed low-carbon steel obtained in the step (1) to 880-920 ℃ at the speed of 10 ℃/s, the initial rolling temperature of 850-800 ℃, and the first-pass rolling strain rate of 1-5 s-1The deformation amount is 30%; and (3) carrying out second pass rolling after the interval of 1-5 s, wherein the rolling parameters are as follows: strain rate of 1-5 s-1The deformation is 20 percent, and the finishing temperature is 780-720 ℃;
(3) cooling to 550 +/-30 ℃ at a cooling speed of more than or equal to 50 ℃/s, preserving heat for 30 minutes, and then air-cooling to room temperature to obtain the Ti-V-N composite microalloyed nano particle reinforced low-carbon steel.
The Ti-V-N composite microalloyed low carbon steel comprises, by mass, 0.05-0.2% of C, 0.1-0.3% of Si, 0.5-2% of Mn, 0.4-1.1% of Cr, 0.08-0.19% of Ti, 0.3-0.6% of V, 0.1-0.3% of Ni and the balance of N: 0.1-0.3%, P less than 0.03%, S less than 0.03%, and the balance of Fe and residual trace impurities.
The rolling equipment can be a four-roller double-stand rolling mill, and the heating equipment can be a heating furnace.
The microalloyed low carbon steel can be a plate blank, a square billet, a round billet and the like.
The principle of the invention is as follows: the invention adopts Ti-V-N composite microalloying technology combined with matched TMCP controlled rolling and controlled cooling technology to ensure that nano-scale V (C, N) particles are dispersed and separated in the steel to play a remarkable precipitation strengthening role, and the grain size in the steel can be remarkably refined and the comprehensive mechanical property of the microalloyed steel can be improved through the function of pinning the grain boundary of TiN particles and the rolling process of two stages. Because a certain amount of Ti, V and N alloy elements are added into the steel, in order to ensure that the alloy elements are dissolved into the steel as much as possible in a solid manner, the austenitizing temperature is set to be 1230-1280 ℃; the TiC particle precipitated phase generated in the single Ti microalloyed steel cannot refine austenite grains through the function of pinning grain boundaries because the TiC particle precipitated phase does not have the thermodynamic condition of precipitation before hot rolling. Compared with a TiC precipitated phase, TiN particles are easier to precipitate before heat preservation at 1230-1280 ℃ because of smaller equilibrium solid solubility product, so a certain amount of N is added on the basis of Ti microalloyed steel, a certain amount of TiN is precipitated from steel, and the function of refining austenite grains is achieved; however, excessive N content in the steel may cause excessive N and V to combine to form VN precipitate phase, and the VN precipitate phase is easy to coarsen due to high precipitation temperature range, so the adding amount of the N element in the steel is comprehensively considered to be 0.1-0.3%. Further, in the invention, Ti is not used as a main precipitation strengthening element, and the excessive Ti content can cause large-size precipitate particles in the steel and reduce the plasticity and toughness of the steel, so the mass percent of Ti in the steel is comprehensively considered to be controlled to be 0.08-0.19%. V is used as a main precipitation strengthening element in the invention, and V is easy to combine with elements such as C, N and the like in steel to form V (C, N) or VC precipitate particles with smaller size, the V is uniformly distributed and dispersed, the yield strength of steel can be greatly improved, and the influence on the plasticity and toughness of the steel is smaller, so that the content of V is controlled to be 0.3-0.6% after the factors in various aspects such as production cost, performance requirements and the like are comprehensively considered. The main functions of the invention are that the two-stage rolling, the rapid cooling after rolling and the isothermal treatment after cooling to a certain temperature are as follows: the recrystallization rolling process mainly promotes repeated recrystallization of austenite grains for many times and refines the austenite grain structure; the non-recrystallization rolling process mainly generates a large amount of crystal defects in steel through cold deformation, so that V (C, N) grains are deformed and induced to be separated out, and meanwhile, austenite grains can generate serious cold deformation to play a role in promoting ferrite nucleation; the reason that the non-recrystallization region is rapidly cooled and isothermally kept after rolling is mainly to prevent excessive V (C, N) and VC from being separated out in a higher temperature range to influence the precipitation strengthening effect.
The invention has the beneficial effects that:
(1) according to the method, austenite is promoted to be recrystallized for multiple times through recrystallization zone rolling, austenite grains are refined, precipitation of nano-scale precipitates in steel is increased through non-recrystallization zone rolling and low-temperature isothermal, precipitation strengthening increment of steel is improved, and therefore yield strength of the steel is greatly improved.
(2) The method of the invention utilizes the mechanisms of fine grain strengthening, precipitation strengthening and solid solution strengthening, improves the comprehensive mechanical property of steel, obviously reduces the addition of alloy elements and reduces the production cost;
(3) provides TMCP technological parameter guidance for the production and manufacture of Ti microalloyed low-carbon high-strength steel, and improves the performance stability of Ti microalloyed nano-particle reinforced high-strength steel.
(4) The low-carbon steel produced by the controlled rolling and controlled cooling process has fine grain size and a large amount of nano-scale V (C, N) and VC precipitates are dispersed and distributed in the structure.
Drawings
FIG. 1 is a process flow diagram of the present invention;
FIG. 2 is a metallographic structure graph of the Ti-V-N composite microalloyed low carbon steel in example 1 after being subjected to TMCP treatment;
FIG. 3 is an SEM image of the morphology of a nano precipitated phase in the Ti-V-N composite microalloyed low carbon steel after TMCP treatment in example 1.
Detailed Description
The invention is described in further detail below with reference to the figures and the embodiments, but the scope of the invention is not limited to the description.
Example 1
A controlled rolling and controlled cooling (TMCP) process for Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel comprises the following chemical components in percentage by mass: c: 0.09%; 0.9 percent of Mn; si: 0.15 percent; cr: 0.73 percent; 0.12 percent of Ti; 0.46 percent of V; 0.25 percent of N; 0.21 percent of Ni; 0.002% of P; 0.006 percent of S, the balance of Fe and inevitable impurities, and the microalloyed steel is a thin slab, wherein the TMCP process comprises the following steps:
(1) and (3) rolling in a recrystallization area: heating the microalloy low-carbon steel to 1250 ℃, preserving heat for 600s, cooling to 1100 ℃ to start austenite recrystallization zone rolling, wherein the cooling speed is 10 ℃/s, and the strain rate of the first pass rolling is 10s-1The deformation amount is 40%; and (3) carrying out second pass rolling after the interval of 3s, wherein the rolling parameters are as follows: strain rate 5s-1The deformation is 20%, and the finishing temperature is controlled at 1000 ℃.
(2) Rolling in a non-recrystallization area: cooling the Ti-V-N composite micro-alloyed low-carbon steel rolled in the recrystallization zone to 920 ℃ at the speed of 10 ℃/s, the initial rolling temperature of 830 ℃, and the first-pass rolling strain rate of 3s-1The deformation amount is 30%; and (3) carrying out second pass rolling after the interval of 3s, wherein the rolling parameters are as follows: strain rate 2s-1The deformation is 20 percent, and the finishing temperature is 750 ℃.
(3) And (3) rapidly cooling after rolling: cooling to 550 ℃ at the cooling speed of 55 ℃/s, preserving the heat for 30 minutes, and then air-cooling to room temperature to obtain the Ti-V-N composite microalloyed nano particle reinforced low-carbon steel.
Example 2
A controlled rolling and controlled cooling (TMCP) process for Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel comprises the following chemical components in percentage by mass: c: 0.11 percent; 1.2 percent of Mn; si: 0.18 percent; cr: 0.81 percent; 0.14 percent of Ti; 0.55 percent of V; 0.29 percent of N; 0.28 percent of Ni; 0.004% of P; 0.005% of S, the balance of Fe and inevitable impurities, and the microalloyed steel is a thin slab, wherein the TMCP process comprises the following steps:
(1) and (3) rolling in a recrystallization area: mixing the aboveHeating microalloy low-carbon steel to 1280 ℃, preserving heat for 600s, cooling to 1130 ℃ to start austenite recrystallization zone rolling, wherein the cooling speed is 10 ℃/s, and the strain rate of the first pass rolling is 15s-1The deformation amount is 40%; and (3) carrying out second pass rolling after the interval of 2s, wherein the rolling parameters are as follows: strain rate 10s-1The deformation is 20 percent, and the finishing temperature is controlled at 1020 ℃.
(2) Rolling in a non-recrystallization area: cooling the Ti-V-N composite micro-alloyed low-carbon steel rolled in the recrystallization zone to 900 ℃ at the speed of 10 ℃/s, the initial rolling temperature of 850 ℃, and the strain rate of the first rolling of 5s-1The deformation amount is 30%; and (3) carrying out second pass rolling after an interval of 5s, wherein the rolling parameters are as follows: strain rate 3s-1The deformation is 20%, and the finishing temperature is 730 ℃.
(3) And (3) rapidly cooling after rolling: cooling to 520 ℃ at the cooling speed of 54 ℃/s, preserving the heat for 30 minutes, and then air-cooling to room temperature to obtain the Ti-V-N composite microalloyed nano particle reinforced low-carbon steel.
Example 3
A controlled rolling and controlled cooling (TMCP) process for Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel comprises the following chemical components in percentage by mass: c: 0.07 percent; 1.5 percent of Mn; si: 0.21 percent; cr: 0.85 percent; 0.16 percent of Ti; 0.58 percent of V; 0.22 percent of N; 0.21 percent of Ni; 0.005 percent of P; 0.006 percent of S, the balance of Fe and inevitable impurities, and the microalloyed steel is a thin slab, wherein the TMCP process comprises the following steps:
(1) and (3) rolling in a recrystallization area: heating the microalloy low-carbon steel to 1240 ℃, preserving heat for 600s, cooling to 1070 ℃, starting austenite recrystallization zone rolling, wherein the cooling speed is 10 ℃/s, and the first-pass rolling strain rate is 12s-1The deformation amount is 40%; and (3) carrying out second pass rolling after an interval of 5s, wherein the rolling parameters are as follows: strain rate 8s-1The deformation is 20%, and the finishing temperature is controlled at 1000 ℃.
(2) Rolling in a non-recrystallization area: cooling the Ti-V-N composite micro-alloyed low-carbon steel rolled in the recrystallization zone to 910 ℃ at the speed of 10 ℃/s, the initial rolling temperature of 800 ℃, and the first-pass rolling strain rate of 3s-1The deformation amount is 30%; after an interval of 2sRolling in the second pass, wherein the rolling parameters are as follows: strain rate 2s-1The deformation is 20%, and the finishing temperature is 720 ℃.
(3) And (3) rapidly cooling after rolling: cooling to 530 ℃ at a cooling speed of 58 ℃/s, preserving the heat for 30 minutes, and then air-cooling to room temperature to obtain the Ti-V-N composite microalloyed nano particle reinforced low-carbon steel.
It can be known from metallographic structure diagram and SEM image analysis that the Ti-V-N composite micro-alloyed nano particle reinforced low-carbon steel prepared in embodiments 1 to 3 of the present invention has a structure mainly based on soft and tough ferrite structure, and a large amount of dispersed nano-scale VC and V (C, N) particles are distributed in ferrite grains, and meanwhile, a very small amount of Ti (C, N) precipitate particles with large size exist in a ferrite matrix, and these Ti (C, N) particles with large size are mainly precipitated in the high temperature austenitizing process and the recrystallization rolling process, and are coarsened in the subsequent treatment process, and the precipitation strengthening effect is basically lost. The Ti-V-N composite microalloyed nano particle reinforced low carbon steel of the example 1 is explained in detail,
the metallographic structure diagram of the Ti-V-N composite microalloyed low carbon steel after being processed by TMCP is shown in figure 2, and the diagram shows that the structure of the Ti-V-N composite microalloyed low carbon steel is mainly polygonal ferrite and granular ferrite, the grain size is smaller, the steel does not basically contain precipitate particles with larger sizes, the structure distribution is more uniform, and the comprehensive performance of the steel is better; the SEM image of the nanometer precipitated phase morphology of the Ti-V-N composite microalloyed low carbon steel after TMCP treatment is shown in figure 3, and the SEM and V (C, N) precipitate particles with the size range of 10-100nm are dispersed and distributed in ferrite grains, but the Ti-V-N composite microalloyed low carbon steel does not contain the precipitate particles with the size of more than 100nm basically. The shape of the precipitate particles with smaller size mainly takes regular sphericity as a main part, and the precipitate particles are mainly dispersed and precipitated in the low-temperature isothermal process after cooling is controlled, because the ferrite crystal has larger supercooling degree and accumulates certain deformation energy storage after rapid cooling, and the larger supercooling degree and the deformation energy storage provide phase change driving force for the precipitation of VC and V (C, N), and simultaneously reduce the surface energy required to be overcome by nucleation, so that VC and V (C, N) are uniformly nucleated in the ferrite crystal; because the temperature is lower at the moment, the micro-alloy elements basically do not diffuse, and precipitates do not coarsen and grow after nucleation; the interfacial energies of the surfaces of the precipitate particles in all directions are substantially the same, and therefore the shape of the resulting precipitate is mostly regular spherical. The spherical precipitate particles can improve the strength of steel by blocking the movement of dislocation, and the material cannot generate stress concentration in the stress process and has small influence on the plastic toughness.
A large amount of nano-scale precipitated phase particles are dispersed in the matrix structure of the Ti-V-N composite microalloyed low-carbon steel prepared by the method, and meanwhile, the grain structure is fine, so that large fine grain strengthening increment and precipitation strengthening increment are obtained, and the comprehensive mechanical property of the steel is obviously improved. The mechanical properties are shown in table 1:
TABLE 1
Claims (1)
1. A controlled rolling and controlled cooling process for Ti-V-N composite microalloyed nano-particle reinforced low-carbon steel is characterized by comprising the following steps:
(1) and (3) rolling in a recrystallization area: heating Ti-V-N composite microalloyed low carbon steel to 1230-1280 ℃, preserving the heat for 600s, then cooling to 1160-1050 ℃, and starting the rolling of an austenite recrystallization region, wherein the cooling speed is 10 ℃/s; the strain rate of the first pass rolling is 10-15 s-1And the deformation is 40%, rolling for the second time is carried out after the interval of 1-5 s, and the rolling parameters are as follows: strain rate of 5-10 s-1The deformation is 20 percent, and the finishing temperature is controlled to be more than 980 ℃;
(2) rolling in a non-recrystallization area: cooling the Ti-V-N composite microalloyed low-carbon steel obtained in the step (1) to 880-920 ℃ at the speed of 10 ℃/s, the initial rolling temperature of 850-800 ℃, and the first-pass rolling strain rate of 1-5 s-1The deformation amount is 30%; and (3) carrying out second pass rolling after the interval of 1-5 s, wherein the rolling parameters are as follows: strain rate of 1-5 s-1The deformation is 20 percent, and the finishing temperature is 780-720 ℃;
(3) cooling to 550 +/-30 ℃ at a cooling speed of more than or equal to 50 ℃/s, preserving heat for 30 minutes, and then air-cooling to room temperature to obtain Ti-V-N composite microalloyed nano particle reinforced low-carbon steel;
the Ti-V-N composite microalloyed low-carbon steel comprises, by mass, 0.05-0.2% of C, 0.1-0.3% of Si, 0.5-2% of Mn, 0.4-1.1% of Cr, 0.08-0.19% of Ti, 0.3-0.6% of V, 0.1-0.3% of Ni and the following chemical components in percentage by mass: 0.1-0.3%, P less than 0.03%, S less than 0.03%, and the balance of Fe and residual trace impurities.
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| CN108486496A (en) * | 2018-03-13 | 2018-09-04 | 昆明理工大学 | A kind of cooling controlling and rolling controlling process method of Ti-Zr-Mo combined microalloyings steel fine austenite grain |
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| CN105543680A (en) * | 2015-12-21 | 2016-05-04 | 秦皇岛首秦金属材料有限公司 | Micro-boron treatment wide and thick plate with tensile strength grade of 700MPa and production method of wide and thick plate |
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