CN110592479B - Hot-rolled H-shaped steel and production method thereof - Google Patents
Hot-rolled H-shaped steel and production method thereof Download PDFInfo
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Abstract
The invention relates to hot-rolled H-shaped steel and a production method thereof. The weight percentage of the chemical components is as follows: 0.08-0.10% of C, 0.25-0.35% of Si, 1.00-1.20% of Mn, less than or equal to 0.015% of P, less than or equal to 0.010% of S, 1.00-1.30% of Cr1.30%, 0.30-0.40% of Ni0.30-0.40% of Cu, 0.15-0.25% of Mo0.020-0.040% of Nb0.050%, 0.050-0.080% of V, 0.015-0.030% of Al, and the balance of Fe and inevitable impurities. The production method comprises the steps of blank heating, cogging rolling, universal rolling, rapid cooling after rolling and air cooling. The invention can obtain the hot-rolled H-shaped steel with 460MPa grade yield strength and excellent strength and toughness, fire resistance, weather resistance and seismic performance through reasonable component proportion and process control.
Description
Technical Field
The invention belongs to the technical field of steel production, and particularly relates to hot-rolled H-shaped steel and a production method thereof.
Background
At present, at building structure practical application's hot rolling H shaped steel, its weatherability ability, fire resistance are not good enough, for guaranteeing the safety in service of steel, often need apply paint thick coating or additional other structures with a brush, cause building steel structure's preparation period long, with high costs, additional structure also can restrict the in-service space of steel construction, and follow-up maintenance is inconvenient with the change, and building steel structure also more and more values anti-seismic performance. Therefore, the development of hot-rolled H-shaped steel with good weather resistance, fire resistance and earthquake resistance is beneficial to promoting the development of the building steel structure in China.
The hot rolled plate has certain technology accumulation in the aspect of developing the variety steel with corrosion resistance, fire resistance, shock resistance and other performances. However, hot rolled H-section steel is very different from it in terms of equipment and process, and the composition and process control of the sheet are not suitable. Firstly, hot rolling H-shaped steel belongs to a complex section, continuous casting of a special-shaped blank is adopted, cogging rolling and universal rolling forming are carried out, deformation distribution among each pass is greatly limited for coordinating deformation of flanges and webs, and the total compression ratio is relatively small; secondly, the height and width directions of the beam blank are mainly controlled in the cogging stage, the thickness direction of the flange is basically not pressed, and the single-pass pressing penetration of the reciprocating rolling of the universal section is shallow; and finally, regulating and controlling subsequent no-curl slow cooling or heat treatment.
Because of this, hot-rolled H-section steel has been developed only for the development of various types of steel having weather resistance, fire resistance, low temperature resistance, and the like alone, but there is still a gap in the product and the result for high-strength hot-rolled H-section steel having coupled strong weather resistance, fire resistance, and shock resistance.
At present, the requirements of thin-specification and high-strength hot-rolled H-shaped steel for building steel structures with higher space utilization rate requirements or building steel structures with larger limits on space and structural weight are more and more urgent, and the steel is also required to have weather resistance, fire resistance and shock resistance because subsequent coating maintenance or auxiliary structure replacement cannot be carried out due to space limitations.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide hot-rolled H-shaped steel and a production method thereof, based on the production reality of the hot-rolled H-shaped steel, by reasonable component proportion and process control, through the processes of cogging rolling, universal rolling, post-rolling fast cooling and air cooling, the hot-rolled H-shaped steel with the flange thickness of 4-20 mm, excellent strength and toughness, fire resistance, weather resistance and seismic performance and the yield strength of 460MPa is produced; the combination mode of fine grain strengthening, precipitation strengthening and structure strengthening is adopted to improve the comprehensive mechanical property and good high-temperature strength; the process of rapid cooling and air cooling after rolling is adopted, the finish rolling temperature of universal rolling is higher, the load and the energy consumption of a rolling mill can be reduced, and the production efficiency is improved.
The technical scheme adopted by the invention is as follows:
a hot-rolled H-shaped steel comprises the following chemical components in percentage by weight: 0.08-0.10% of C, 0.25-0.35% of Si, 1.00-1.20% of Mn, less than or equal to 0.015% of P, less than or equal to 0.010% of S, 1.00-1.30% of Cr1.30%, 0.30-0.40% of Ni0.30-0.40% of Cu, 0.15-0.25% of Mo0.020-0.040% of Nb0.050%, 0.050-0.080% of V, 0.015-0.030% of Al, and the balance of Fe and inevitable impurities.
The hot-rolled H-shaped steel is hot-rolled H-shaped steel with flange thickness of 4-20 mm.
According to the hot-rolled H-shaped steel, the weather resistance of the steel is improved by utilizing a Cr-Ni-Cu alloy system, the fire resistance of the steel is improved by utilizing a Mo-Nb-Cu-V alloy system, the hardenability is greatly improved by utilizing Mn and Cr, the steel is quickly cooled after being rolled, and good comprehensive mechanical properties and high-temperature strength are obtained through a mode of fine grain strengthening, precipitation strengthening and tissue strengthening (the bainite or ferrite proportion is not higher than 20%).
Specifically, the action and the proportion of each element are as follows:
carbon (C): has obvious solid solution strengthening effect and improves the hardenability of the steel. In order to obtain higher strength and reduce the control difficulty of steel-making and decarburization, the lower limit is set to be 0.08 wt%; however, too high a content seriously deteriorates plasticity, toughness, weather resistance and weldability, and the upper limit is set to 0.10 wt%.
Silicon (Si): has stronger solid solution strengthening effect and has certain beneficial effect on weather resistance. To obtain higher strength, a lower limit of 0.25 wt% is set; however, if the content is too high, the high-temperature delamination is accelerated, the toughness and weldability are deteriorated, and the surface quality of the steel is adversely affected, and the upper limit is set to 0.35 wt%.
Manganese (Mn): the hardenability is improved, and the toughness and the strength of the steel are improved within a certain range. Considering that the hardenability can be greatly improved by matching with Cr, and the effect of rapid cooling after rolling is greatly improved, the lower limit is set to be 1.00 wt%; however, the content is too high, macrosegregation is easy to generate, the toughness of the steel is obviously reduced, even the phenomenon of layering occurs, and in order to avoid adverse factors, the upper limit is set to be 1.20 wt%.
Phosphorus (P): the impurity elements have certain effect of improving the weather resistance, but are easy to generate local serious segregation to deteriorate the plasticity, the toughness and the weldability of steel, and the upper limit is set to be 0.015 wt% in consideration of reducing the control difficulty of steel-making de-P.
Sulfur (S): impurity elements are easy to segregate and enrich, MnS inclusions are formed at the same time, the MnS inclusions are easy to roll into long-strip round cakes, the contact interface of the MnS inclusions and a matrix is large, the disordered atomic arrangement energy of the contact surface is high, cracks and pitting corrosion are easy to generate, the toughness, the lamellar tearing resistance and the corrosion resistance of the steel are seriously deteriorated, and the set upper limit is 0.010 wt%.
Chromium (Cr): the steel has high hardenability, strength, fire resistance and weather resistance, and high cost performance. In order to obtain good room temperature strength, reduce yield ratio and greatly improve weather resistance, the lower limit is set to be 1.00 wt% in order to obtain actual effect; however, if the content is too high, the weldability of the steel deteriorates and the alloy cost increases particularly by adding other alloying elements, and the upper limit is set to 1.30 wt%.
Nickel (Ni): the lattice constant is close to that of face-centered cubic iron, so that continuous solid solution can be realized, the sliding is promoted, the dislocation motion resistance is reduced, the stress is relaxed, the ductility and toughness of steel are improved, the compactness and stability of a rust layer and the binding force with a matrix can be improved, and the hardenability can be improved. In order to obtain good low-temperature toughness, form a stable rust layer to improve weather resistance and solve the surface quality problem caused by Cu brittleness, the lower limit is set to be 0.30 wt%; however, the content is too high, which not only causes incomplete descaling before cogging and will have certain influence on the weldability of steel, but also sets the upper limit to 0.40 wt% considering the higher price.
Copper (Cu): the rust layer, the oxidation position or the crack position are easy to be enriched, the corrosion medium is prevented from further contacting, the conversion of gamma-Fe 2O 3/gamma-FeOOH to the stable rust layer phase alpha-FeOOH is promoted, and the weather resistance of the steel is obviously improved. In order to obtain good weather resistance, the alloy needs to be matched with Cr and Ni, the high-temperature strength of the steel is improved by considering the characteristics of normal-temperature solid solution and fire precipitation, and the lower limit is set to be 0.30 wt%; however, the content is too high, cracks are easy to appear on the surface of the beam blank, and the upper limit is set to be 0.40 wt%.
Molybdenum (Mo): the fire resistance and hardenability of the steel are significantly improved. The matrix is directly strengthened through solid solution strengthening so as to improve the high-temperature strength, meanwhile, the thermal stability of the structure is enhanced at the defect positions such as the matrix interface and the like through segregation, MC phase nano particles are separated out and refined in cooperation with Nb, V and the like, the defects of the interface, dislocation and the like are pinned, the high-temperature strength is directly improved through precipitation strengthening, the thermal stability of the structure is also improved, and the high-temperature strength is indirectly improved, wherein the lower limit is set to be 0.15 wt% for obtaining the substantial effect; however, the content is too high, and not only the toughness and weldability of the steel are deteriorated, but also the alloy cost is high, and the upper limit is set to 0.25 wt%.
Niobium (Nb): the crystal grains are refined, the high-temperature structure stability is improved, and the weldability is facilitated. Solid solution Nb is easy to be segregated at the interface and dislocation defect to prevent austenite grains from coarsening, MC containing Nb separated out by heating can stabilize a high-temperature structure together with Nb separated out by precipitation, and the lower limit is set to be 0.020 wt% for obtaining a substantial effect; however, the content is too high, the internal fillet of the continuous casting beam blank is easy to crack, the surface quality of the final product is affected, the cost is high, and the upper limit is set to be 0.040 wt%.
Vanadium (V): the MC phase can be formed independently with C, and can also be separated out with Nb, Mo and the like in a synergistic manner, the room-temperature yield strength and the fire resistance are improved mainly by the action of pinning dislocation and interface of MC phase nano particles, and the lower limit is set to be 0.050 wt% for obtaining the actual effect; however, too high a content deteriorates the ductility and toughness of the steel and adversely affects the weldability, and the upper limit is set to 0.080 wt%.
Aluminum (Al): refined grains and strong oxidizing elements are important steelmaking deoxidizing elements. Can play a role of refining austenite grains, and the lower limit is set to be 0.015 wt% for obtaining the substantial effect; however, if the content is too high, more spinel inclusions will be produced, and the plasticity and toughness of the steel will be seriously deteriorated, with the upper limit set to 0.030 wt%.
A production method of hot-rolled H-shaped steel comprises the following steps:
A. heating the blank: the heating temperature of the special-shaped blank in the heating furnace is 1210-1250 ℃, the furnace time is 90-150 min, the alloy elements are ensured to be fully dissolved, and overburning and austenite excessive coarsening are avoided;
B. cogging and rolling: the initial rolling temperature is 1100-1150 ℃, the final rolling temperature is not higher than 980 ℃, the waiting time for the initial rolling of the universal section is shortened, and meanwhile, the austenite grains in the flange area are prevented from being coarsened excessively;
C. universal rolling: the initial rolling temperature is 930-970 ℃, the final rolling temperature is not lower than 880 ℃, the accumulated flange reduction rate is not lower than 80%, and the structure is fully refined through strain accumulation, so that preparation is provided for subsequent rapid cooling and refining of the structure and promotion of precipitation and precipitation;
D. and (3) rapidly cooling after rolling: entering a rapid cooling area immediately after universal rolling is finished, ensuring that the cooling speed is not lower than 30 ℃/s and the final cooling temperature of a rolled piece is below 600 ℃, rapidly passing through a high-temperature area without deformation, entering a super-cooling austenite area, and refining the structure;
E. air cooling: after the rapid cooling, the mixture is put into a cooling bed for air cooling, so that the precipitation dispersion precipitation and bainite precipitation processes are sufficient.
Based on the production practice of hot-rolled H-shaped steel, the invention produces hot-rolled H-shaped steel with flange thickness of 4-20 mm, excellent strength and toughness, fire resistance, weather resistance and seismic performance, and yield strength of 460MPa grade through cogging rolling, universal rolling, fast cooling after rolling and air cooling processes by reasonable component proportion and process control; the combination mode of fine grain strengthening, precipitation strengthening and structure strengthening is adopted to improve the comprehensive mechanical property and good high-temperature strength; the process of rapid cooling and air cooling after rolling is adopted, the finish rolling temperature of universal rolling is higher, the load and the energy consumption of a rolling mill can be reduced, and the production efficiency is improved.
Drawings
FIG. 1 is a gold phase diagram of a room temperature microstructure of a hot-rolled H-section steel produced in example 1 of the present invention;
FIG. 2 is a gold phase diagram of a room temperature microstructure of a hot-rolled H-section steel produced in accordance with embodiment 3 of the present invention;
FIG. 3 is a gold phase diagram of a room temperature microstructure of a hot-rolled H-section steel produced in accordance with embodiment 5 of the present invention;
FIG. 4 is a gold phase diagram of a room temperature microstructure of a hot-rolled H-section steel produced in accordance with embodiment 7 of the present invention;
Detailed Description
The chemical compositions, specifications, I values of the fire indexes and Pcm values of the hot rolled H-shaped steels of examples 1 to 8 of the present invention are shown in Table 1,
the invention discloses a production method of 1-8-grade hot-rolled H-shaped steel, which comprises the following steps:
A. heating the blank: the heating temperature of the special-shaped blank in the heating furnace is 1210-1250 ℃, and the furnace time is 90-150 min (the furnace time of the examples 1-8 is 145, 140, 135, 130, 120, 110, 100min respectively);
B. cogging and rolling: the initial rolling temperature is 1100-1150 ℃, and the final rolling temperature is not higher than 980 ℃ (particularly 960-;
C. universal rolling: the initial rolling temperature is 930-970 ℃, and the final rolling temperature is not lower than 880 ℃ (specifically 880 plus 910 ℃);
D. and (3) rapidly cooling after rolling: immediately entering a rapid cooling area after universal rolling is finished, ensuring that the cooling speed is not lower than 30 ℃/s (specifically 30-50 ℃/s) and the final cooling temperature of a rolled piece is below 600 ℃ (specifically 550-;
E. air cooling: and after the rapid cooling, the mixture is put on a cooling bed for air cooling.
The main specific process parameters involved in the steps of the production methods A-D are shown in Table 2.
The test results of the room-temperature tensile and low-temperature impact properties of the embodiments 1-8 of the invention are shown in Table 3 (the sampling position of the flange of the hot-rolled H-shaped steel specified in GB/T2975-2018), the tensile properties after the heat preservation at 600 ℃ for 3 hours are shown in Table 4, and the test results of the tables 3 and 4 show that the yield strength at room temperature of the hot-rolled H-shaped steel is 472-502 MPa, the tensile strength is 590-604 MPa, the elongation is 21.0-23.5%, and the impact work at-40 ℃ is 103-172J, which shows that the product has good room-temperature strength, plasticity and low-temperature toughness; the room temperature yield ratio is 0.80-0.83, which shows that the product has good anti-seismic performance; the product is insulated for 3 hours at 600 ℃, and the yield strength is not lower than 2/3 of the yield strength at room temperature, which shows that the product has good fire resistance; the value of the atmospheric corrosion resistance index I calculated according to GB/T4171-2008 appendix D is not lower than 7.0, which shows that the product has good atmospheric corrosion resistance. The requirements of the building structural steel market on high-performance hot-rolled H-shaped steel with flange thickness of 4-20 mm are met.
TABLE 1 chemical composition of examples 1 to 8 (unit: wt%)
TABLE 2 Main Process parameters (temperature Unit:. degree. C.) of examples 1 to 8
TABLE 3 tensile and Low temperature impact Properties at Room temperature for examples 1-8
| ReL/MPa | Rm/MPa | A/％ | -40℃KV2/J | Yield ratio | |
| Example 1 | 497 | 599 | 23.5 | 158、172、132 | 0.83 |
| Example 2 | 502 | 604 | 23.0 | 148、136、155 | 0.83 |
| Example 3 | 492 | 600 | 22.5 | 125、143、131 | 0.82 |
| Example 4 | 489 | 596 | 21.5 | 123、125、111 | 0.82 |
| Example 5 | 486 | 600 | 22.5 | 137、110、122 | 0.81 |
| Example 6 | 481 | 601 | 21.0 | 125、112、103 | 0.80 |
| Example 7 | 479 | 591 | 21.5 | 104、126、121 | 0.81 |
| Example 8 | 472 | 590 | 21.0 | 124、120、115 | 0.80 |
TABLE 4 tensile Properties of examples 1 to 8 after incubation at 600 ℃ for 3h
| ReL/MPa | Rm/MPa | |
| Example 1 | 337 | 402 |
| Example 2 | 346 | 441 |
| Example 3 | 344 | 421 |
| Example 4 | 333 | 447 |
| Example 5 | 340 | 432 |
| Example 6 | 331 | 421 |
| Example 7 | 349 | 455 |
| Example 8 | 339 | 460 |
Claims (6)
1. A hot-rolled H-shaped steel comprises the following chemical components in percentage by weight: 0.08-0.10% of C, 0.25-0.35% of Si, 1.00-1.20% of Mn, less than or equal to 0.015% of P, less than or equal to 0.010% of S, 1.00-1.30% of Cr1.30%, 0.30-0.40% of Ni0.30-0.40% of Cu, 0.15-0.25% of Mo0.020-0.040% of Nb0.050%, 0.050-0.080% of V, 0.015-0.030% of Al, and the balance of Fe and inevitable impurities;
the production method of the hot-rolled H-shaped steel comprises the following steps:
A. heating the blank: the heating temperature of the special-shaped blank in the heating furnace is 1210-1250 ℃, and the furnace time is 90-180 min;
B. cogging and rolling: the initial rolling temperature is 1100-1150 ℃, and the final rolling temperature is not higher than 980 ℃;
C. universal rolling: the initial rolling temperature is 930-970 ℃, the final rolling temperature is not lower than 880 ℃, and the accumulated flange reduction rate is not lower than 80%;
D. and (3) rapidly cooling after rolling: entering a rapid cooling area immediately after universal rolling is finished, ensuring that the cooling speed is not lower than 30 ℃/s and the final cooling temperature of a rolled piece is below 600 ℃;
E. air cooling: and after the rapid cooling, the mixture is put on a cooling bed for air cooling.
2. The hot-rolled H-section steel according to claim 1, wherein: the hot-rolled H-shaped steel is hot-rolled H-shaped steel with flange thickness of 4-20 mm.
3. The production method of hot-rolled H-section steel according to claim 1 or 2, comprising the steps of:
A. heating the blank: the heating temperature of the special-shaped blank in the heating furnace is 1210-1250 ℃, and the furnace time is 90-180 min;
B. cogging and rolling: the initial rolling temperature is 1100-1150 ℃, and the final rolling temperature is not higher than 980 ℃;
C. universal rolling: the initial rolling temperature is 930-970 ℃, the final rolling temperature is not lower than 880 ℃, and the accumulated flange reduction rate is not lower than 80%;
D. and (3) rapidly cooling after rolling: entering a rapid cooling area immediately after universal rolling is finished, ensuring that the cooling speed is not lower than 30 ℃/s and the final cooling temperature of a rolled piece is below 600 ℃;
E. air cooling: and after the rapid cooling, the mixture is put on a cooling bed for air cooling.
4. The production method according to claim 3, wherein: the finishing temperature in the step B is 960-.
5. The production method according to claim 3, wherein: and C, the accumulated flange reduction rate in the step C is 80-95%.
6. The production method according to claim 3, wherein: the cooling speed in the step D is 30-50 ℃/s, and the final cooling temperature of the rolled piece is 550-600 ℃.
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