CN115710612A - Production method of vanadium-titanium-containing steel - Google Patents
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Abstract
The invention discloses a production method of vanadium-titanium-containing steel, which adopts the production processes of converter smelting, LF refining, RH refining, continuous casting and hot continuous rolling. The steel provided by the invention does not need to be subjected to heat treatment, and has the characteristics of low production cost, good equipment adaptability and capability of being produced on a common hot continuous rolling line. The microstructure of the steel provided by the invention is ferrite + precipitated phase, the strength and toughness are considered, and the formability is more excellent compared with high-strength steel with a martensite structure. The invention provides the key points of controlling the microstructure and the precipitated phase size of the steel, and provides a specific control idea for realizing the stable production of the ultra-high-strength hot rolled steel at the level of 1000 MPa.
Description
Technical Field
The invention relates to a production method of high-strength hot continuous rolling steel, in particular to a method for controlling the average grain size of vanadium-titanium-containing steel within 3 mu m and controlling the proportion of small-size nanometer precipitated phases to be more than 70%.
Background
In recent years, with the improvement of the steel smelting level in China and the development of steel microalloying technology, the application of vanadium and titanium in steel is effectively popularized. The process has been developed from a single vanadium or titanium microalloying mode to a vanadium-titanium composite microalloying mode. The strength grade of the steel is also developed from the traditional 600-700MPa grade to 800MPa and above. Wherein, 1000MPa grade hot-rolled high-strength steel is mainly heat-treated steel in the market at present, and few steel with ferrite base and precipitation strengthening exists.
By retrieval, CN 109023111B discloses 1000 MPa-grade hot-rolled automobile beam steel and a production method thereof, and the components of the hot-rolled automobile beam steel in percentage by weight are as follows: c:0.10-0.20%, mn:1.5-1.7%, si is less than or equal to 0.10%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, nb:0.045-0.055%, ti:0.08-0.10%, N is not more than 40ppm, als:0.025-0.06%, H is less than or equal to 0.002%, and the balance of Fe and inevitable impurities. By adopting the production process of deep desulfurization pretreatment, converter smelting, LF refining, RH refining, continuous casting, slab heating, rough rolling, finish rolling and ultra-fast cooling, the finished steel with yield strength of more than or equal to 750MPa, tensile strength of more than or equal to 1000MPa, elongation of more than or equal to 10 percent, qualified 180-degree cold bending d =4a and martensite proportion of more than or equal to 80 percent is obtained. According to the invention, nb-Ti composite micro-alloying is adopted, and a rapid cooling process is combined to obtain the steel with most martensite of matrix structure, and tempering heat treatment is not carried out, so that the steel is expected to have low toughness, poor formability and limited application field.
CN 201380021909.9 discloses a high strength thin steel plate and a manufacturing method thereof, wherein the high strength thin steel plate comprises the following components in percentage by weight: c:0.08-0.20%, mn:0.1-3.0%, si:0.3% or less, al:0.10% or less, P:0.10% or less, S:0.030% or less, N:0.010%, V:0.20-0.80 percent, and then one or two groups of Ti, nb/Mo, B and Cr/Ni are added, and the thin steel plate with the yield strength of more than 1000MPa is obtained after heating, rough rolling, finish rolling and coating annealing.
In conclusion, most of the existing 1000 MPa-grade heat treatment steels have the problem of low forming performance due to the addition of high hardenability elements, or the adoption of a heat treatment process or a rapid cooling process to obtain martensite steel. Therefore, it is necessary to develop a ferrite-based ultrahigh-strength hot continuous rolling steel and a production method thereof, which have matched strength and formability and are simple in production process.
Disclosure of Invention
The invention aims to provide a method for producing vanadium-titanium-containing steel, the microstructure of the steel is ferrite, the tensile strength is higher than 1000MPa, the average grain size is controlled within 3 mu m, and the proportion of small-size precipitated phases below 40nm is higher than 70%.
In order to achieve the aim, the invention provides a production method of vanadium-titanium-containing steel, which adopts the production process of converter smelting, LF refining, RH refining, continuous casting and hot rolling of the vanadium-titanium-containing steel, and comprises the following steps:
(1) The method comprises the following steps of obtaining a casting blank from molten steel in a converter smelting-LF refining-RH refining-continuous casting mode, wherein the vanadium-titanium-containing steel comprises the following main alloy elements in percentage by weight: ti:0.10-0.16%, V:0.08-0.12%, mn:1.7-2.0%, C:0.08-0.10%, mo:0.15-0.23%, si:0.50-0.30%, als:0.010-0.050%, nb is less than or equal to 0.040%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, and the balance of Fe and inevitable impurity elements;
wherein, in the continuous casting process of the vanadium-titanium-containing steel, low superheat degree casting is adopted, the low superheat degree is less than or equal to 30 ℃, and the preferred temperature is 20-30 ℃;
(2) Stacking and slowly cooling the obtained casting blank, then loading the casting blank into a heating furnace for reheating, then carrying out hot rolling, and then carrying out controlled cooling to obtain vanadium-titanium-containing steel;
wherein, the slow cooling initial temperature of the vanadium-containing titanium steel stack is not lower than 600 ℃, and is preferably 650-750 ℃; the slow cooling time is not less than 24 hours, preferably 24 to 48 hours;
in the hot rolling process, the rough rolling compression ratio is 4.7-7.2, and the finish rolling temperature is 900-960 ℃;
in the cooling process, the final cooling temperature is 580-630 ℃.
Further, the thickness of the vanadium-titanium-containing steel casting blank is 200-250mm.
Furthermore, the vanadium-titanium-containing steel plate blank is reheated at 1220-1260 ℃, and the soaking time is more than or equal to 30min, preferably 30-60min.
Further, the finished steel plate after the vanadium-titanium-containing steel is finish rolled has a thickness of 1.8-10 mm.
Further, the thickness of the vanadium-titanium-containing steel intermediate billet is as follows: when the thickness of the finished steel plate is 1.8-4 mm, the thickness of the intermediate blank is 34 +/-2 mm; when the thickness of the finished steel plate is 4-5.9 mm, the thickness of the intermediate blank is 38 +/-2 mm; when the thickness of the finished steel plate is 6-10 mm, the thickness of the intermediate billet is 47 +/-2 mm.
Further, the hot rolling process of the vanadium and titanium containing steel comprises the following steps: the initial rolling temperature of rough rolling is 1100-1160 ℃, the final rolling temperature of rough rolling is 1000-1050 ℃, the reduction ratio of rough rolling is 4.7-7.2, the initial rolling temperature of finish rolling is 990-1030 ℃, the final rolling temperature of finish rolling is 900-960 ℃, and the reduction ratio of finish rolling is 5.0-18.0.
Further, the vanadium-titanium-containing steel is subjected to heat preservation through a heat preservation cover after rough rolling and before finish rolling.
Furthermore, the vanadium-titanium-containing steel is rolled at an increased speed during finish rolling, and the outlet speed of a rolling mill is more than or equal to 5m/s.
Further, the laminar cooling mode of the vanadium-titanium-containing steel is front-section cooling, and the cooling speed is more than or equal to 20 ℃/s.
Further, the vanadium-titanium-containing steel is coiled after being cooled, and is sent into a slow cooling pit for heat preservation for 60-80h after being coiled, wherein the pit entering temperature of the slow cooling pit is not lower than 550 ℃.
Compared with the prior art, the invention has the beneficial effects that:
(1) The steel provided by the invention does not need to be subjected to heat treatment, and has the characteristics of low production cost, good equipment adaptability and capability of being produced on a common hot continuous rolling line.
(2) The microstructure of the steel provided by the invention is ferrite + precipitated phase, the strength and toughness are considered, and the formability is more excellent compared with high-strength steel with a martensite structure.
(3) The invention provides the key points of controlling the microstructure and the precipitated phase size of the steel, and provides a specific control idea for realizing the stable production of the ultra-high-strength hot rolled steel at the level of 1000 MPa.
Drawings
FIG. 1 is a microstructure of the steel prepared in example 1.
FIG. 2 is a microstructure of the steel prepared in example 2.
FIG. 3 is a microstructure of the steel prepared in example 3.
FIG. 4 is the microstructure of the steel prepared in example 4.
Fig. 5 is the nano TiC precipitate morphology of the steel prepared in example 1.
FIG. 6 is a distribution of nano TiC precipitates for the steel prepared in example 1.
FIG. 7 is a microstructure of the steel prepared in comparative example 1.
Fig. 8 is a microstructure of the steel prepared in comparative example 2.
FIG. 9 is a microstructure of the steel prepared in comparative example 3.
Detailed Description
The invention provides a production method of the vanadium-titanium-containing steel, and the reasons for the limitation of the production process of the steel grade are explained below.
The superheat degree of a tundish in a steelmaking process has large influence on the grain size of a casting blank structure and the component segregation in the casting blank, and when the superheat degree of the tundish is too high, the as-cast structure is easily coarse and is inherited into finished steel, so that grains are coarse; meanwhile, the segregation of the components of the casting blank is easily aggravated due to the excessively high superheat degree of the tundish, and a mixed crystal structure is easily formed in the rolling process of the finished steel. Therefore, the invention limits the enclosed heat degree within 30 ℃, preferably 20-30 ℃.
The purpose of stacking slow cooling is to make the as-cast structure uniform and fine, otherwise, the as-cast structure which is coarse is easy to be inherited into the finished steel by hot charging, so that the crystal grains are coarse, and the strength of the finished steel is reduced; and secondly, the 600-800 ℃ interval is a ferrite and austenite two-phase region, steel is generally difficult to avoid being loaded in the temperature interval when hot charging is carried out by hot conveying, part of austenite in a casting blank is converted into ferrite at the moment, and coarse austenite and fine ferrite coexist to form a mixed crystal structure, and the abnormal structure is difficult to remove in the subsequent heating and rolling processes and can be inherited into a finished steel plate, so that the grains of the finished steel are uneven, and the strength and the toughness of the finished steel are reduced. Therefore, the invention limits the casting blank to be loaded into the furnace after stacking and slow cooling, and the slow cooling starting temperature is not lower than 600 ℃, the slow cooling time is not lower than 24h, preferably the stacking slow cooling starting temperature is 650-750 ℃, and the slow cooling time is 24-48h.
The slab reheating has the function of enabling alloy elements such as vanadium, titanium and the like to be in solid solution and fully precipitated in the subsequent rolling and cooling processes. If the heating temperature is too low, the precipitation ratio of the alloying element is lowered, and if the heating temperature is too high, the structure tends to be coarse. Therefore, the heating temperature of the plate blank is controlled to be 1220-1260 ℃, and the soaking time is limited to be more than 30min, preferably 30-60min.
In the rough rolling process, the rough and large as-cast austenite structure can be crushed through rolling reduction, the dynamic recrystallization of austenite is promoted, relatively fine austenite crystal grains are formed, and meanwhile, the cast dendritic crystal segregation can be crushed, and the component segregation is reduced. The invention determines the thickness of the intermediate blank according to the thickness of different finished steel plates, adopts lower thickness of the intermediate blank, ensures larger rough rolling compression ratio, and controls the rough rolling compression ratio within the range of 4.7-7.2.
In the finish rolling process, crystal deformation can be realized through austenite without binding, nucleation energy and nucleation mass points are provided for subsequent phase transformation, and grain refinement is promoted. Research shows that austenite deformation of a finish rolling area is reduced, the equilibrium concentration of C on the gamma side of a gamma/alpha phase boundary can be reduced, and the concentration of C on the gamma side near the phase boundary can reach the equilibrium concentration by moving the gamma/alpha phase boundary a short distance, namely, the interphase precipitation surface spacing is reduced, and interphase precipitation is promoted. In conclusion, the reduction of the austenite deformation amount in the finish rolling area is beneficial to reducing deformation induced precipitation (more than 20 nm) and promoting interphase precipitation (less than 20 nm), namely, the proportion of small-size precipitated phases less than 20nm is increased, so that the tensile strength of the finished steel is improved. Therefore, the invention adopts lower intermediate billet thickness and reduces the austenite deformation amount of the finish rolling area.
In addition, when a higher finish rolling temperature is adopted, the temperature corresponding to the finish rolling process is also higher, so that deformation induced precipitation is favorably inhibited, and meanwhile, the supercooling degree in the phase change process is also increased, so that interphase precipitation is favorably promoted. Therefore, the finish rolling temperature is limited to a higher range of 900-960 ℃, and meanwhile, the finish rolling temperature is possibly low due to the temperature drop of the tail part of the steel coil in the rolling process, so that the heat preservation of the steel coil needs to be carried out through a heat preservation cover before finish rolling, and the tail temperature drop is reduced by adopting the accelerated rolling during finish rolling.
The laminar cooling process can generate phase change and interphase precipitation, and the adoption of a faster cooling speed is favorable for promoting the refinement of ferrite tissues and the interphase precipitation, so the laminar cooling mode is limited to front-stage cooling, and the cooling speed is required to be more than or equal to 20 ℃/s. Meanwhile, since about 600 ℃ is the nose point temperature of TiC precipitation, the coiling temperature is set to 580-630 ℃ in the present invention to promote the supersaturated precipitation of ferrite.
The slow cooling pit heat preservation is mainly used for further promoting the supersaturated precipitation of ferrite and increasing the quantity of small-size nanometer precipitated phases less than 20nm, so that the heat preservation time must be sufficient, and meanwhile, the temperature of a hot bright steel coil must be sufficient, so that the nanometer precipitation can be promoted. Therefore, the invention requires the slow cooling time to be 60-80h, and the pit entering temperature of the slow cooling pit is not lower than 550 ℃.
The following examples are provided to further illustrate the embodiments of the present invention and are not intended to limit the scope of the present invention.
Table 1 shows the compositions of the inventive examples and comparative examples, table 2 shows the hot rolling process parameters of the inventive examples and comparative examples, and Table 3 shows the mechanical properties of the inventive examples and comparative steels.
The vanadium-titanium-containing steel disclosed in the embodiments 1 to 4 and the comparative examples 1 to 3 of the invention has the chemical components shown in the table 1, adopts converter smelting, LF refining, RH refining and continuous casting to form a casting blank with the thickness of 230mm, then carries out stacking and slow cooling, then the casting blank is put into a slab heating furnace, and is subjected to hot continuous rolling and rapid cooling to obtain a finished steel plate, wherein the tensile strength is more than 1000MPa, the elongation is more than 16%, and the finished steel plate is qualified in a 180-degree cold bending test d =2 a.
FIGS. 1 to 4 show the microstructures of the steels prepared in examples 1 to 4, in which the average grain size is within 3 μm, and FIGS. 5 and 6 show the morphology and distribution of nano TiC precipitates, and the TiC nano-precipitate phase ratio of less than 40nm can reach 70% or more.
Compared with the examples 1 to 4, the comparative examples 1 to 4 adopt similar components, the chemical components have small difference, and the difference is mainly reflected in the process. FIGS. 7 to 9 show the microstructures of comparative examples 1 to 3, respectively.
Comparative example 1 has adopted higher well package superheat degree and lower slab reheating temperature, and well package superheat degree easily causes the composition segregation to aggravate when high, leads to the casting blank tissue comparatively thick, and inhomogeneous, and slab reheating temperature is on the low side in addition, can't make the composition segregation homogenization in the casting blank completely, so cause to roll the back structure thick, and inhomogeneous, and then lead to comparative example 1 finished product steel sheet tensile strength on the low side.
The comparative example 2 adopts higher finish rolling initial rolling temperature, lower rolling speed and lower finish rolling temperature, so that the deformation induced precipitation of high-temperature rolling is increased, the phase precipitation is reduced during phase change, and precipitation with enough fineness is not formed to refine relative phase change tissues to cause thick tissues, and meanwhile, the comparative example 2 also adopts higher finish cooling temperature to cause the supersaturated precipitation of ferrite to be reduced, so that the tensile strength of the finished steel plate of the comparative example 2 is lower due to the reasons.
Comparative example 3 has adopted longer soaking time, thicker intermediate billet thickness, soaking time overlength easily leads to original austenite thick, is unfavorable for the refinement of follow-up tissue, when adopting thicker intermediate billet simultaneously, the rough rolling cumulative compression is less, is difficult for making the casting blank segregation carry out the homogenization, simultaneously, finish rolling cumulative compression is bigger, can increase gamma/alpha phase boundary gamma side C equilibrium concentration, make gamma/alpha phase boundary move long distance and just can make near phase boundary gamma side C concentration reach equilibrium concentration, increase alternate precipitation face interval promptly, reduce alternate precipitation. Thus, the microstructure of the finished steel of comparative example 3 showed ferrite banding with a lower tensile strength.
TABLE 1
| C | Si | Mn | P | S | V | Ti | Nb | Mo | Als | |
| Example 1 | 0.092 | 0.10 | 1.77 | 0.009 | 0.002 | 0.09 | 0.150 | / | 0.17 | 0.014 |
| Example 2 | 0.093 | 0.08 | 1.75 | 0.014 | 0.003 | 0.10 | 0.151 | / | 0.18 | 0.022 |
| Example 3 | 0.082 | 0.09 | 1.88 | 0.010 | 0.002 | 0.10 | 0.118 | 0.031 | 0.22 | 0.028 |
| Example 4 | 0.092 | 0.29 | 1.77 | 0.009 | 0.002 | 0.09 | 0.150 | / | 0.17 | 0.014 |
| Comparative example 1 | 0.092 | 0.29 | 1.77 | 0.009 | 0.002 | 0.09 | 0.150 | / | 0.17 | 0.014 |
| Comparative example 2 | 0.093 | 0.08 | 1.75 | 0.014 | 0.003 | 0.10 | 0.151 | / | 0.18 | 0.022 |
| Comparative example 3 | 0.082 | 0.09 | 1.88 | 0.010 | 0.002 | 0.10 | 0.118 | 0.031 | 0.22 | 0.028 |
TABLE 2
Table 2 (continuation)
TABLE 3
Claims (9)
1. The production method of the vanadium-titanium-containing steel is characterized by comprising the following steps:
(1) The method comprises the following steps of obtaining a casting blank from molten steel in a converter smelting-LF refining-RH refining-continuous casting mode, wherein the casting blank comprises the following chemical components in percentage by weight: ti:0.10-0.16%, V:0.08 to 0.12%, mn:1.7-2.0%, C:0.08-0.10%, mo:0.15-0.23%, si:0.50-0.30%, als:0.010-0.050%, nb is less than or equal to 0.040%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, and the balance of Fe and inevitable impurities;
in the continuous casting process, low superheat degree casting is adopted, and the low superheat degree is less than or equal to 30 ℃;
(2) Stacking and slowly cooling the obtained casting blank, then heating the casting blank in a heating furnace, performing hot rolling, and then controlling cooling to obtain vanadium-titanium-containing steel;
the heating temperature of the casting blank is 1220-1260 ℃, and the soaking time is more than or equal to 30min;
in the hot rolling process, the rough rolling reduction ratio is 4.7-7.2, and the finish rolling temperature is 900-960 ℃;
in the cooling process, the final cooling temperature is 580-630 ℃.
2. The production method according to claim 1, wherein the hot rolling process is: the initial rolling temperature of rough rolling is 1100-1160 ℃, the final rolling temperature of rough rolling is 1000-1050 ℃, the reduction ratio of rough rolling is 4.7-7.2, the initial rolling temperature of finish rolling is 990-1030 ℃, the final rolling temperature of finish rolling is 900-960 ℃, and the reduction ratio of finish rolling is 5.0-18.0.
3. The production method according to claim 1, wherein a front-end cooling mode is adopted, and the cooling speed is more than or equal to 20 ℃/s.
4. The production method according to claim 1, wherein the thickness of the cast slab is 200 to 250mm.
5. The production method according to claim 1, wherein the finished steel sheet after finish rolling has a thickness of 1.8 to 10mm.
6. The production method as claimed in claim 1 or 5, wherein when the thickness of the finished steel sheet is 1.8 to 4mm, the thickness of the intermediate slab is 34 ± 2mm; when the thickness of the finished steel plate is 4-5.9 mm, the thickness of the intermediate blank is 38 +/-2 mm; when the thickness of the finished steel plate is 6-10 mm, the thickness of the intermediate billet is 47 +/-2 mm.
7. The production method according to claim 1, wherein the rough rolling is followed by heat preservation by a heat-preserving cover before finish rolling.
8. The production method according to claim 1, wherein the exit speed of the rolling mill is 5m/s or more in the finish rolling.
9. The production method of claim 1, wherein the vanadium-titanium-containing steel is coiled after being cooled, and the coiled steel is sent into a slow cooling pit for heat preservation for 60-80h, wherein the pit entering temperature of the slow cooling pit is not lower than 550 ℃.
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