CN103343209A - Controlled rolling and controlled cooling technique for improving performance of Q235 steel plate - Google Patents
Controlled rolling and controlled cooling technique for improving performance of Q235 steel plate Download PDFInfo
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- CN103343209A CN103343209A CN201310298184XA CN201310298184A CN103343209A CN 103343209 A CN103343209 A CN 103343209A CN 201310298184X A CN201310298184X A CN 201310298184XA CN 201310298184 A CN201310298184 A CN 201310298184A CN 103343209 A CN103343209 A CN 103343209A
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Abstract
The invention discloses a controlled rolling and controlled cooling technique for improving performance of a Q235 steel plate. The controlled rolling and controlled cooling technique comprises the following steps of: (1) melting the following chemical components by weight percent: 0.10-0.20% of C, less than or equal to 0.30% of Si, 0.30-0.70% of Mn, less than or equal to 0.045% of P, less than or equal to 0.045% of S, and the balance of iron and inevitable impurities, and continuously casting into blanks with 115mm in thickness; (2) heating the blanks at the temperature of 1100 DEG C, and preserving heat for 1-2h; (3) carrying out high-temperature rolling: rolling at the temperature of 1000-1100 DEG C, wherein the total deformation quantity can be guaranteed to be more than 80%, the single deformation quantity is not less than 10%, and the finally rolling temperature is controlled to be 900 DEG C-950 DEG C; and (4) immediately cooling ultra-quickly after being rolled at the cooling speed being more than 100 DEG C/s; controlling the final cooling temperature at 500-600 DEG C, and then carrying out air-cooling to room temperature. According to the controlled rolling and controlled cooling technique, the rolling energy consumption can be greatly reduced, and the production period of the steel can be shortened.
Description
Technical field
The invention belongs to field of metallurgy, be specifically related to a kind of cooling controlling and rolling controlling process of the Q235 of improvement plate property.
Background technology
Since the economic crisis, the bad present situation that the common steel grade production capacity of China's Iron And Steel Industry is serious superfluous highlights more, and enterprise also strives realizing that minimizing produces to guarantee benefit moving heaven and earth.Wherein, for traditional steel grades such as Q235, because its profit margin itself is just very low, therefore the optimization by rolling technology improves, and realizes that the upgrading of product and then the benefit space of expansion product just seem most important under the prerequisite of or fine setting constant in chemical ingredients.In addition, the upgrading of the intensity of steel grade also directly brings the weight loss effect of prepared structural part, can save the steel usage quantity, improves material use efficiency, reduces the production cycle cost of steel.
Under the traditional processing technology, for guaranteeing the obdurability of Q345 steel plate, need to add 1%～1.6% alloying element Mn usually, part producer is because the appointed condition restriction also need be added expensive alloy element such as an amount of Nb, V, Ti.But the increase of Mn element produces easily the MnS plasticity of elongating and is mingled with in Rolling Production, causes that the vertical, horizontal poor mechanical property is big, banded structure is serious; Can cause significantly improving of production cost and add alloying elements such as Nb, V, Ti.Therefore, in the technology of Q235 upgrading Q345 is explored, more employings be TMCP (controlled rolling control cooling) technology, by two stage rolling, i.e. roughing and finish rolling realize in conjunction with accelerating to cool off.Wherein, 1050～1100 ℃ of the start rolling temperatures of rolling sequence roughing process, main purpose is to obtain tiny, uniform austenite crystal at austenite high temperature recrystallization zone repeat-rolling; And finish rolling start rolling temperature interval is 800～900 ℃, the finish rolling finishing temperature is at 730～830 ℃, and finish rolling open rolling and finishing temperature are wanted strict control, to obtain the Strain Accumulation effect in low temperature non-recrystallization district, increase the phase driving force that austenite intracrystalline imperfection, strain-hardening and residual strain are brought out.Simultaneously, cooperate follow-up acceleration cooling, promote austenite/ferrite transformation, the thin brilliant ferrite+pearlitic structure of final acquisition realizes the existing product upgrading.
The shortcoming of prior art mainly contains: the explained hereafter cycle is longer.Go to toward the air cooling cooling that needs for some time or water-cooled cooling to finish rolling after the roughing; In addition, owing to adopt the laminar flow cooling, speed of cooling is restricted, and makes that also the time of cooling section is longer.Finish rolling stage steel temperature is lower, the required power height.
Summary of the invention
The cooling controlling and rolling controlling process that the purpose of this invention is to provide a kind of Q235 of improvement plate property not only reduces required power, shortens the rolling cycle, by adjusting and optimize the cooling controlling and rolling controlling process of Q235 steel, realizes the performance upgrade of product.
For realizing purpose of the present invention, the technical scheme of employing is embodied as:
A kind of cooling controlling and rolling controlling process that improves the Q235 plate property, it may further comprise the steps:
(1) be C0.10～0.20% according to chemical component weight per-cent, Si≤0.30%, Mn0.30～0.70%, P≤0.045%, S≤0.045%, all the other are iron and unavoidable impurities, smelting also, continuous casting is 115mm thick stock material;
(2) blank heating: Heating temperature is 1100 ℃, insulation 1～2h;
(3) high temperature rolling: 1000～1100 ℃ of start rolling temperatures; Guarantee total deformation＞80%, and single pass heavy deformation is not less than 10%; Finishing temperature control is at 900 ℃～950 ℃;
(4) roll after ultrafast cooling immediately, speed of cooling＞100 ℃/s; And final cooling temperature control is at 500～600 ℃, and air cooling is to room temperature immediately.
Patent of the present invention is treated warm link owing to avoided middle, and directly adopts the high temperature rolling technology, only need determine start rolling temperature and pass deformation, and finishing temperature can remain on more than 900 ℃, reduces required power significantly; And adopt roll after ultra fast cooling technology immediately, further shorten cooling time, also shortened the production cycle of steel to a certain extent, reduce production costs.
Description of drawings
Fig. 1 is the microstructure picture of embodiment 1 light plate;
Fig. 2 is the microstructure picture of embodiment 2 light plates;
Fig. 3 is the microstructure picture of embodiment 3 light plates.
Embodiment
Specifically set forth the present invention below in conjunction with embodiment.
Embodiment 1:
This steel (wt%) composed of the following components: C:0.15%, Si:0.14%, Mn:0.38%, P:0.011%, S:0.017%, all the other are Fe and unavoidable impurities.
(1) smelting also according to above-mentioned chemical component weight per-cent, continuous casting is 115mm thick stock material;
(2) blank heating: Heating temperature is 1100 ℃, the removal scale on surface of coming out of the stove behind the insulation 1h;
(3) high temperature rolling: 1050 ℃ of start rolling temperatures; Reduction schedule is allocated as follows: 115-100-85-70-60-50-40-35-28-22-15-11-9-6-4, and total deformation is 96.5%; And single pass heavy deformation is greater than 10%, 910 ℃ of finishing temperatures;
(4) roll after ultrafast cooling immediately, speed of cooling is 200 ℃/s; And 530 ℃ of final cooling temperatures, air cooling is to room temperature immediately.The optical microstructure of gained steel plate as shown in Figure 1, relevant mechanical property (steel plate A) as shown in table 1.
Embodiment 2:
This steel (wt%) composed of the following components: C:0.15%, Si:0.18%, Mn:0.40%, P:0.011%, S:0.017%, all the other are Fe and unavoidable impurities.
(1) smelting also according to above-mentioned chemical component weight per-cent, continuous casting is 115mm thick stock material;
(2) blank heating: Heating temperature is 1100 ℃, the removal scale on surface of coming out of the stove behind the insulation 2h;
(3) high temperature rolling: 1000 ℃ of start rolling temperatures; Reduction schedule is allocated as follows: 115-100-85-70-60-50-40-35-28-22-15-11-9-6-4, and total deformation is 96.5%; And single pass heavy deformation is greater than 10%, 900 ℃ of finishing temperatures;
(4) roll after ultrafast cooling immediately, speed of cooling is 235 ℃/s; And 500 ℃ of final cooling temperatures, air cooling is to room temperature immediately.The scanning electron microscope microstructure of gained steel plate as shown in Figure 2, relevant mechanical property (steel plate B) as shown in table 1.
Embodiment 3:
This steel (wt%) composed of the following components: C:0.16%, Si:0.30%, Mn:0.70%, P:0.011%, S:0.017%, all the other are Fe and unavoidable impurities.
(1) smelting also according to above-mentioned chemical component weight per-cent, continuous casting is 115mm thick stock material;
(2) blank heating: Heating temperature is 1100 ℃, the removal scale on surface of coming out of the stove behind the insulation 1h;
(3) high temperature rolling: 1050 ℃ of start rolling temperatures; Reduction schedule is allocated as follows: 115-100-85-70-60-50-40-35-28-22-19, and total deformation is 83.5%; And single pass heavy deformation is greater than 10%, 950 ℃ of finishing temperatures;
(4) roll after ultrafast cooling immediately, speed of cooling is 115 ℃/s; And 580 ℃ of final cooling temperatures, air cooling is to room temperature immediately.The scanning electron microscope microstructure of gained steel plate as shown in Figure 3, relevant mechanical property (steel plate C) as shown in table 1.
Embodiment 4:
This steel (wt%) composed of the following components: C:0.20%, Si:0.14%, Mn:0.40%, P:0.011%, S:0.017%, all the other are Fe and unavoidable impurities.
(1) smelting also according to above-mentioned chemical component weight per-cent, continuous casting is 115mm thick stock material;
(2) blank heating: Heating temperature is 1100 ℃, the removal scale on surface of coming out of the stove behind the insulation 1h;
(3) high temperature rolling: 1050 ℃ of start rolling temperatures; Reduction schedule is allocated as follows: 115-100-85-70-60-50-40-35-28-22-15-11, and total deformation is 90.4%; And single pass heavy deformation is greater than 10%, and finishing temperature is controlled at 940 ℃;
(4) roll after ultrafast cooling immediately, speed of cooling is 135 ℃/s; And 600 ℃ of final cooling temperatures, air cooling is to room temperature immediately.
Embodiment 5:
This steel (wt%) composed of the following components: C:0.18%, Si:0.24%, Mn:0.58%, P:0.011%, S:0.017%, all the other are Fe and unavoidable impurities.
(1) smelting also according to above-mentioned chemical component weight per-cent, continuous casting is 115mm thick stock material;
(2) blank heating: Heating temperature is 1100 ℃, the removal scale on surface of coming out of the stove behind the insulation 1h;
(3) high temperature rolling: 1050 ℃ of start rolling temperatures; Reduction schedule is allocated as follows: 115-100-85-70-60-50-40-35-28-22-15-11-9-6, and total deformation is 94.7%; And single pass heavy deformation is greater than 10%, and finishing temperature is controlled at 900 ℃;
(4) roll after ultrafast cooling immediately, speed of cooling is 150 ℃/s; And 530 ℃ of final cooling temperatures, air cooling is to room temperature immediately.
In the various embodiments described above, the rolling pass number in high temperature rolling under the condition of capacity of equipment permission, guarantees few rolling pass number, to enhance productivity without limits as far as possible.
The present invention on the basis that does not increase cost, realizes the upgrading of Q235 steel by the optimization of rolling technology.
Table 1 is the mechanical property of embodiments of the invention 1～3 made steel plate
The different steel plate mechanical properties of table 1
Fig. 1 is the figure of optical microstructure (* 500) of example 1 gained steel plate A cross section.As seen, organizational composition is ferrite, perlite and intracrystalline carbide among the figure.Wherein, the about 20 μ m of ferrite average grain size; Perlite is the disperse of fritter shape and is distributed in the crystal boundary position; Ferrite crystal grain disperse a large amount of carbide that distribute, it is much smaller that carbide size is compared to ferrite crystal grain.Analyze accordingly, the build up mode of gained steel plate is mainly precipitation strength, and the lifting of intensity mainly ascribes the precipitation strength effect of intracrystalline carbide to.
Fig. 2 is the scanning electron microscope micro-organization chart (* 2000) of example 2 gained steel plate B cross sections.As seen, organizational composition also is ferrite, perlite and intracrystalline carbide among the figure.Wherein, the about 20 μ m of ferrite average grain size; Perlite is the disperse of fritter shape and is distributed in the crystal boundary position; Ferrite crystal grain disperse a large amount of carbide that distribute, it is much smaller that carbide size is compared to ferrite crystal grain.Analyze accordingly, the build up mode of gained steel plate is mainly precipitation strength, and the lifting of intensity mainly ascribes the precipitation strength effect of intracrystalline carbide to.
Fig. 3 is the scanning electron microscope micro-organization chart (* 2000) of example 3 gained steel plate C cross sections.As seen, organizational composition is ferrite, perlite and intracrystalline carbide among the figure.Wherein, ferrite grain size is bigger, and is to a certain degree strip, and the long axis direction mean sizes surpasses 50 μ m, and the short-axis direction mean sizes is about 20 μ m; Perlite also is strip and is distributed in the crystal boundary position; It is more tiny that ferrite crystal grain disperse a large amount of superfine carbide that distribute, carbide size are compared to ferrite crystal grain.Think that accordingly the build up mode of gained steel plate is still based on precipitation strength, the lifting of intensity mainly ascribes the precipitation strength effect of intracrystalline carbide to.
The present invention is by the fast speed rolling of high temperature and the rolling straight carbon steel of supper-fast process for cooling, not only can realize the performance upgrade of existing kind, in the applying of other alloy steel grade Rolling Production, the low-cost minimizing that can also at utmost realize related products is rolling, help to realize the minimizing of high-grade steel production process composition, conserve expensive alloying element, and technology minimizing, the purpose of shortened process.
Claims (1)
1. cooling controlling and rolling controlling process that improves the Q235 plate property, it is characterized in that: it may further comprise the steps:
(1) be C0.10～0.20% according to chemical component weight per-cent, Si≤0.30%, Mn0.30～0.70%, P≤0.045%, S≤0.045%, all the other are iron and unavoidable impurities, smelting also, continuous casting is 115mm thick stock material;
(2) blank heating: Heating temperature is 1100 ℃, insulation 1～2h;
(3) high temperature rolling: 1000～1100 ℃ of start rolling temperatures; Guarantee total deformation＞80%, and single pass heavy deformation is not less than 10%; Finishing temperature control is at 900 ℃～950 ℃;
(4) roll after ultrafast cooling immediately, speed of cooling＞100 ℃/s; And final cooling temperature control is at 500～600 ℃, and air cooling is to room temperature immediately.
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| CN103966502A (en) * | 2014-05-15 | 2014-08-06 | 河北钢铁股份有限公司唐山分公司 | Low-cost yield strength 400MPa-grade steel strip and production method thereof |
| CN106521125A (en) * | 2016-12-20 | 2017-03-22 | 东北大学 | Method for improving strength by ultrarapid cooling of angle steel after rolling |
| CN112239830A (en) * | 2020-08-31 | 2021-01-19 | 盐城市联鑫钢铁有限公司 | Low-cost high-ductility disc strip for CRB600H and rolling process thereof |
| CN114540713A (en) * | 2022-03-01 | 2022-05-27 | 新疆八一钢铁股份有限公司 | Production method of Q235KZ anti-seismic section steel |
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| CN112239830A (en) * | 2020-08-31 | 2021-01-19 | 盐城市联鑫钢铁有限公司 | Low-cost high-ductility disc strip for CRB600H and rolling process thereof |
| CN114540713A (en) * | 2022-03-01 | 2022-05-27 | 新疆八一钢铁股份有限公司 | Production method of Q235KZ anti-seismic section steel |
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