CN110923550A - Hot-rolled structural steel with high surface quality, high strength and toughness produced by adopting short process and production method - Google Patents
Hot-rolled structural steel with high surface quality, high strength and toughness produced by adopting short process and production method Download PDFInfo
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Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
- B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/02—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
- B21B45/0203—Cooling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/04—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for de-scaling, e.g. by brushing
- B21B45/08—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for de-scaling, e.g. by brushing hydraulically
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2201/00—Special rolling modes
- B21B2201/06—Thermomechanical rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides a hot-rolled structural steel with high surface quality, high toughness and produced by adopting a short process and a production method, and the hot-rolled structural steel comprises the following components: 0.15-0.23%, Si: 0.005-0.05%, Mn: 0.20-1.20%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Als: 0.010-0.045%, B: 0.0005-0.0030%, N < 0.002%, and the balance Fe and inevitable impurities. Compared with the prior art, the product has the matrix structure of bainite and ferrite, wherein the bainite proportion is 65-75%, the thickness is 2.5-4.5 mm, the yield strength is 400-520 MPa, the tensile strength is more than or equal to 530MPa, the elongation is more than or equal to 24%, the product cost is lower, the product has good economy, the requirement of direct use is met, and the product can also be used as a substrate of various coating products such as zinc plating and the like.
Description
Technical Field
The invention belongs to the technical field of metal material processing, and particularly relates to hot-rolled structural steel with high surface quality, high toughness and short production process and a production method thereof.
Background
In recent years, with the increasing approach of the depletion time schedule of traditional fossil energy sources such as coal, petroleum, natural gas and the like, photovoltaic power generation has gained more and more attention, has become one of the projects with the most commercial popularization prospect in the energy field, and is rapidly developed at home and abroad at present. In the past five years, the cost of photovoltaic power generation is reduced by one third, the photovoltaic power generation is kept at the same level with the retail price in south America and other countries, even is lower than the retail price, and the cost of photovoltaic power generation is further highlighted in the future.
As an important component in photovoltaic power generation equipment, namely a photovoltaic bracket, part of the photovoltaic bracket is made of hot galvanized steel plates, and part of the photovoltaic bracket is made of hot rolled structural steel plates, and the hot rolled plates are required to have high strength, high toughness and good platability. The traditional high-strength structural steel improves the strength by adding alloy elements such as Ti, Nb and the like, has higher material cost, or is strengthened by high Mn and high Si, so that the platability of the steel plate is poor, or is strengthened by adding P, so that the low-temperature performance of the steel plate is poor.
The following brief analysis is made on the production method and the technical current situation of the domestic structural steel which is disclosed in the prior art:
"high-strength carbon-manganese structural steel with 400MPa tensile strength and manufacturing method thereof", published in 1 month and 15 months in 2014 and having Chinese patent number CN 103509996A, discloses a cold-rolled high-strength carbon-manganese structural steel plate obtained by adjusting chemical components of C, Si, Mn, P, S and Als and matching with the control of process flows such as converter smelting, continuous casting, hot rolling and the like. However, when the Si content is high, the platability of the hot dip galvanizing process is adversely affected.
The 590MPa grade high-strength structural steel plate and the manufacturing method thereof which are published in 6, 25 and 6 months in 2014 and have the Chinese patent number CN 103882322A, describe that the steel plate comprises the following components: carbon: 0.10-0.22%; silicon: 0.10-0.55%; manganese: 0.80-1.70%; copper is less than or equal to 0.55 percent; phosphorus is less than or equal to 0.025 percent; sulfur is less than or equal to 0.005 percent; 0.012 to 0.060 percent of niobium; vanadium: 0.015-0.075%; titanium: 0.012-0.045%; aluminum: 0.012-0.045%; chromium: 0.10-0.55%; molybdenum is less than or equal to 0.55 percent; boron is less than or equal to 0.0045 percent; the balance of Fe and inevitable impurities. And the steel plate has high strength, eliminates internal structural stress, improves the ductility and toughness index and has the elongation rate of 17-25 percent by the processes of LF external refining, RH vacuum degassing secondary refining, alloy element protection addition, plate blank heating, rough rolling, finish rolling, controlled rolling and controlled cooling, straightening, quenching and tempering. However, the hot rolled steel plate manufactured by the method is 6-60 mm thick, and is thick, and alloy elements such as Ti, Cr, Mo and the like are added in chemical components, so that the cost is high.
A production method of hot-rolled structural steel for a coating with 460MPa yield strength, which is disclosed in Chinese patent No. CN 101623714B at 1/13/2010, discloses that a hot-rolled structural steel plate with excellent galvanizing performance, mechanical performance and welding performance is obtained by adopting the design of low-carbon, extremely-low-silicon and micro-alloying components mainly including manganese solid solution strengthening elements and auxiliary niobium elements, and hot rolling and controlled rolling, wherein the chemical components and the weight percentages in the steelmaking process are as follows: c: 0.05-0.10%; si is less than or equal to 0.04; mn: 1.30-1.65%; p is less than or equal to 0.030 percent; s is less than or equal to 0.012 percent; ALs: 0.01-0.06%; nb: 0.035-0.060%; the balance of Fe and inevitable impurities. However, the invention has higher Mn content, influenced platability, contains alloy element Nb and has higher cost.
In the production method of boron-containing structural steel, disclosed in chinese patent No. CN 102080179 a published in 6/1/2011, the chemical components in percentage by weight are C: 0.08 to 0.20, Si: 0.10 to 0.30%, Mn: 0.80-1.50%, P: less than or equal to 0.010 percent, S: less than or equal to 0.010 percent, B: 0.0008 to 0.0030 percent, and the balance of Fe and inevitable impurities. The boron-added structural steel mainly comprises ferrite, bainite and a small amount of pearlite. The invention is obtained by laboratory simulation, does not carry out industrial production, has higher Si content, is easy to generate selective oxidation in the hot galvanizing process to cause plating leakage, does not carry out N control treatment, is easy to form BN, and causes poor thermoplasticity of steel.
In the high-toughness boron-containing carbon structural steel plate coil and the production method thereof disclosed in Chinese patent No. CN 103627951A published 3/12/2014, the chemical components comprise, by weight, not more than 0.30% of carbon, and silicon: less than or equal to 0.50 percent, manganese: less than or equal to 1.70 percent, phosphorus: less than or equal to 0.035%, sulfur: less than or equal to 0.035%, aluminum: 0.015-0.050% and 8-50 ppm of boron, and the balance of iron and trace impurities. The elongation property, normal temperature and low temperature impact toughness of the existing carbon structural steel and low alloy steel with yield strength of 215-345 MPa and represented by Q235 and SS400 are improved through boron microalloying and tissue homogenization. The steel grade related by the invention has low yield strength, the thickness of 20-25.4 mm, no N control treatment and poor thermoplasticity.
The above analysis shows that the prior art can obtain a high-strength steel plate from the aspects of component design and process control and a production method thereof, has the problems of high cost, poor platability, poor thermoplasticity and the like, and has no systematic method for obtaining a hot-rolled structural steel plate which is economical and has excellent performance and a manufacturing method thereof.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide the hot-rolled structural steel with high surface quality, high toughness and the production method thereof, which is produced by adopting a short process, and the hot-rolled structural steel has the advantages that the steel plate structure is bainite and ferrite through C-Mn reinforcement, boron microalloying, low silicon, ultralow nitrogen and process control, the thermoplasticity and the platability of the steel plate are improved, the surface quality of the produced steel plate is better, and the produced steel plate has good strength and toughness.
The specific technical scheme of the invention is as follows:
the invention provides a hot-rolled structural steel with high surface quality, high toughness and high toughness, which is produced by adopting a short process, and comprises the following chemical components in percentage by mass:
c: 0.15-0.23%, Si: 0.005-0.05%, Mn: 0.20-1.20%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Als: 0.010-0.045%, B: 0.0005-0.0030%, N < 0.002%, and the balance Fe and inevitable impurities.
Preferably, the invention comprises the following chemical components in percentage by mass:
c: 0.16-0.20%, Si: 0.01-0.04%, Mn: 0.60-1.00%, P: less than or equal to 0.015 percent, S: less than or equal to 0.005 percent, Als: 0.015 to 0.030%, B: 0.0006 to 0.0012 percent, less than 0.0012 percent of N, and the balance of Fe and inevitable impurities.
Preferably, the hot-rolled structural steel with high surface quality, high toughness and high toughness produced by adopting a short process comprises the following chemical components in percentage by mass:
c: 0.1886%, Si: 0.0354%, Mn: 0.9870%, P: 0.0144%, S: 0.0025%, Als: 0.0242%, B: 0.0009 percent of N, 0.0007 percent of N, and the balance of Fe and inevitable impurities.
C: 0.1761%, Si: 0.0376%, Mn: 0.8745%, P: 0.0130%, S: 0.0022%, Als: 0.0202%, B: 0.0010%, 0.0006% of N, and the balance of Fe and inevitable impurities.
C: 0.1903%, Si: 0.0253%, Mn: 0.6968%, P: 0.0147%, S: 0.0020%, Als: 0.0176%, B: 0.0009%, N: 0.0010%, and the balance of Fe and inevitable impurities.
C: 0.1698%, Si: 0.0390%, Mn: 0.9987%, P: 0.0133%, S: 0.0016%, Als: 0.0253%, B: 0.0012%, 0.0009% of N, and the balance of Fe and inevitable impurities.
The invention provides a production method of hot-rolled structural steel with high surface quality, high toughness and short production process, which comprises the following steps:
1) pretreating molten iron;
2) smelting in a converter;
3) an alloy fine tuning station;
4) refining in an LF furnace;
5) CSP continuous casting;
6) discharging;
7) removing phosphorus by using high-pressure water;
8) hot continuous rolling;
9) finish rolling;
10) cooling;
11) and (4) coiling.
Step 1) molten iron pretreatment: and (3) desulfurizing by using a blowing method, wherein the temperature range of the molten iron before desulfurization is 1290-1370 ℃, the [ S ] content is required to be less than or equal to 0.01 percent after desulfurization, slagging is required to be clean after desulfurization, and the molten iron surface is more than 90 percent after slagging.
Step 2) converter smelting: the converter smelting adopts a double-slag method, argon is supplied in the whole process in a converter bottom blowing mode, the tapping temperature range of the converter is 1650-1680 ℃, the tapping time is controlled to be 150-250 s, deoxidation alloying is adopted for tapping, slag blocking operation is enhanced, and the content range of [ FeO + MnO ] in slag in molten steel at the end point of the converter is 16-24%.
Step 3) an alloy fine-tuning station: blowing argon and stirring strongly to reduce the top slag.
Step 4) refining in an LF furnace: the content of [ FeO + MnO ] in the LF refining slag is less than 1%. White slag is produced, and top slag is fully reduced; controlling the content of [ Ca ] in the steel to be 0.0015-0.0030 percent; performing calcium treatment to ensure that the total weak stirring time before and after the calcium feeding line is not less than 11 min.
Step 5) CSP continuous casting: the temperature of the tundish is controlled at the liquidus temperature TLThe temperature is 15-35 ℃ above 1514.4 ℃, the pulling speed is 2.5-3.1 m/min, and the secondary cooling adopts a strong cooling water distribution system.
And 6) controlling the tapping temperature at 1110-1150 ℃.
The step 7) is specifically as follows: the dephosphorization water pressure is 320 bar-380 bar.
The step 8) is specifically as follows: and (3) carrying out hot continuous rolling by adopting 7 stands, and further, removing phosphorus water between the F1 stand and the F2 stand and between the F2 stand and the F3 stand, wherein the pressure of the phosphorus water is 8-10 bar. The screw-down rates of the F1 frame to the F7 frame are respectively 45-50%, 50-55%, 40-45%, 30-35%, 25-30%, 20-25% and 15-20%.
And step 9), controlling the finishing temperature to be 850-890 ℃.
Step 10) cooling: and adopting water curtain laminar flow cooling at the cooling speed of 70-100 ℃/s.
Step 11), the coiling temperature is controlled to be 590-650 ℃.
The production of the product is mainly based on the following principle:
carbon (C): c is an important solid solution strengthening element in steel, but the Fe-Zn reaction is intensified along with the increase of the C content in the hot galvanizing process, so that the galvanizing performance of the steel plate is deteriorated, and the C content avoids a peritectic zone (0.07-0.15 percent) as much as possible, so that the peritectic reaction is reduced, and the generation of edge cracks is avoided. Therefore, the content of the C element is preferably controlled to be 0.16 to 0.20%.
Silicon (Si): si has a strong strengthening effect in steel, the content of Si is too low, the strengthening effect is not obvious, but Si is easy to form oxides, which is not beneficial to acid cleaning, the surface is easy to form oxidation color after annealing, and the coating property of the steel plate is also reduced. Therefore, the present invention employs low silicon control, Si: 0.005-0.05%; the preferable control range of the Si element is 0.01-0.04%.
Manganese (Mn): mn is the most effective element for improving strength, but addition of Mn in an excessive amount increases hardenability of steel, and tends to increase the degree of segregation during continuous casting, resulting in occurrence of a band-shaped structure, which is disadvantageous in plasticity, weldability, and fatigue properties. Therefore, the Mn element accounts for 0.20-1.20% in the invention, and the preferable percentage content control range is 0.60-1.00%.
Phosphorus (P): p is inevitable harmful impurities in the steel, has adverse effects on the stamping performance, cold brittleness, secondary processing brittleness and the like of the steel, and the content of the P element in the steel is strictly controlled. Therefore, the P element is less than or equal to 0.020%, and the preferable percentage content control range is less than or equal to 0.015%.
Sulfur (S): s is an inevitable harmful impurity in steel, excessive S and Mn can form MnS inclusion, the surface quality of a product is seriously influenced, the welding performance, the cold bending performance and the toughness of the steel are all adversely affected, and the content of the S element in the steel is strictly controlled. Therefore, the S element is less than or equal to 0.010 percent, and the percentage content control range is preferably less than or equal to 0.005 percent.
Aluminum (Al): al is added for deoxidation, and when the content of Als is less than 0.01%, the effect cannot be exerted; on the other hand, addition of a large amount of aluminum tends to form alumina inclusions. Therefore, the Als element of the invention is 0.010-0.045%, and the preferable percentage content control range is 0.015-0.030%.
Boron (B): the trace B element can refine grains and increase the uniformity of the structure; the B element has a partial aggregation function on an austenite crystal boundary, can inhibit the nucleation of ferrite, enables a C curve to move to the right, and inhibits the transformation of pearlite; the B element may also inhibit the segregation of the P element in the grain boundary to improve the secondary work brittleness of the steel, but when B is too high, it is easy to form non-metallic inclusions such as O, N. Therefore, the content of the B element in the alloy is 0.0005-0.0030%, and the preferable percentage content control range is 0.0006-0.0012%.
Nitrogen (N): n can improve the strength, low-temperature toughness and weldability of steel, but when N is too high, BN is formed with B, the size of BN is about 50nm, the crystal boundary pinning effect is realized, the thermoplasticity is poor, and when N is too high, AlN forms an AlN low-melting point compound with Als, AlN can be continuously separated out at the austenite crystal boundary of a casting blank and a corner area, the local plasticity of the blank is reduced, and hot cracks are easily generated. Therefore, the invention adopts ultra-low N to control N to be less than 0.002%, and the content of N element is preferably controlled to be less than 0.0012%.
The steel-making process comprises the following steps: the proper molten iron pretreatment (desulphurization) process can improve the cleanliness of molten steel; the dephosphorization rate is higher by adopting a double-slag method; the converter bottom blowing mode adopts the whole-process argon supply, which is favorable for reducing the partial pressure of nitrogen and increasing the free surface area, thereby being favorable for denitrification, the tapping process is also the nitrogen increasing process, the tapping time is controlled, the nitrogen increasing can be inhibited, and the control of ultralow nitrogen is realized. Proper converter tapping temperature and proper slag in molten steel at end point [ FeO + MnO ]]The content is favorable for reducing the end point [ O ] of the converter]The content of the impurities is beneficial to reducing the generation of the impurities, and the cleanliness of the molten steel is improved; FeO + MnO in LF refining slag]The content is less than 1 percent, and the desulfurization efficiency can be improved; calcium treatment can modify the aluminum oxide inclusions into CaO-Al2O3The slag is a low-melting-point spherical compound, so that the floating of the slag is further promoted, the total time of weak stirring before and after the calcium feeding line is ensured, and impurities can be ensured to float sufficiently, so that the cleanliness of molten steel is improved.
Casting blank drawing speed: the pulling speed is generally determined according to the steel grade and the molten steel temperature of a tundish, casting blank cracks are easily caused when the pulling speed is too high, production efficiency is affected when the pulling speed is too low, the pulling speed is not proper, a banded structure appears in steel, and the proper pulling speed needs to be selected in production. Therefore, the casting blank pulling speed control range is 2.5-3.1 m/min.
And (3) dephosphorization process: the high-pressure water dephosphorization mainly utilizes the difference of cooling shrinkage rates of a substrate material and an iron oxide scale layer to form shearing force during high-pressure water impact so that the iron oxide scale falls off from the surface of the substrate, and the pressing-in of the iron oxide scale is greatly reduced in the rolling process, so that good surface quality is obtained, and the high-pressure water dephosphorization mainly comprises three processes of crushing, stripping and flushing; after the dephosphorization by high-pressure water, part of iron scale fragments are always remained on the surface of the steel plate, and the dephosphorization between the frames aims to remove the iron scale on the surface of the strip steel to a greater extent and obtain higher surface quality.
A mill distribution system: the reasonable load distribution coefficient of the stand is beneficial to inhibiting the vibration of the rolling mill and reducing the press-in of the iron scale; the reasonable reduction rate is beneficial to controlling good convexity and wedge degree, and the thickness control target is achieved.
Rolling and cooling control: the occurrence of a banded structure in low-carbon steel is a common phenomenon in hot-rolled steel plates, and the banded structure causes various anisotropy of steel and influences the impact toughness, plasticity, cold bending performance and the like of the material. The finishing temperature is properly reduced, austenite grains can be refined, and a banded structure is reduced; by appropriately increasing the cooling rate, the long-distance diffusion of carbon on the original band-shaped structure can be suppressed, thereby eliminating or alleviating the band-shaped structure. Therefore, the control range of the finish rolling temperature is 850-890 ℃, and the cooling speed is controlled to be 70-100 ℃/s.
High surface quality control principle: compared with the conventional process, the short process has the advantages of high solidification speed, difficult surface quality control and easy generation of defects of impurities, iron scale and edge cracks. The C content is controlled, so that the components can avoid a crystal covering area, and the generation of the hot rolling edge rolling crack defect can be avoided; the content of B + N, Als + N is controlled by ultra-low N control, so that the production of BN and AlN is reduced, the generation of thermal cracks is avoided, and the generation of the hot rolling edge-curling crack defect is reduced; the Mn and S element content is controlled, the quantity of MnS inclusions is reduced, and a molten iron pretreatment process and a converter smelting process are controlled, so that the molten steel cleanliness is improved, and the inclusion defects on the surface of the hot-rolled strip steel are reduced. The generation of the iron scale defect can be reduced by controlling the distribution system, the dephosphorization process and the hot rolling temperature system of the hot rolling mill. In conclusion, the composition control is matched with the control of the steelmaking and hot rolling processes, so that higher surface quality can be obtained.
Compared with the prior art, the method has the advantages that chemical components are reasonably designed, the steel-making, continuous casting, hot rolling, cooling, coiling processes and the like are controlled, the hot-rolled structural steel product with high surface quality and high toughness is produced, the matrix structure is bainite and ferrite, the bainite ratio is 65-75%, the thickness is 2.5-4.5 mm, the yield strength is 400-520 MPa, the tensile strength is larger than or equal to 530MPa, the elongation is larger than or equal to 24%, the product cost is lower, the economy is good, the direct use requirement is met, and the method can be used as a substrate of various coating products such as zinc plating, aluminum silicon plating, zinc aluminum magnesium plating and the like.
Drawings
FIG. 1 is a metallographic structure of example 1;
FIG. 2 is a metallographic structure of example 2;
FIG. 3 is a metallographic structure of example 3;
FIG. 4 is a metallographic structure obtained in example 4;
FIG. 5 shows a metallographic structure of comparative example 1;
FIG. 6 shows a metallographic structure of comparative example 2;
FIG. 7 shows a metallographic structure of comparative example 3;
FIG. 8 is the scale thickness of example 1;
fig. 9 shows the scale thickness of comparative example 2.
Detailed Description
Example 1
A hot-rolled structural steel with high surface quality, high toughness and high toughness produced by adopting a short process comprises the following chemical components in percentage by mass:
c: 0.1886%, Si: 0.0354%, Mn: 0.9870%, P: 0.0144%, S: 0.0025%, Als: 0.0242%, B: 0.0009 percent of N, 0.0007 percent of N, and the balance of Fe and inevitable impurities.
The production method of the hot-rolled structural steel with high surface quality, high strength and toughness, which is produced by adopting the short process, comprises the following steps:
1) pretreating molten iron: and (3) desulfurizing by using a blowing method, wherein the temperature range of the molten iron before desulfurization is 1290 ℃, the [ S ] content is required to be less than or equal to 0.01 percent after desulfurization, slagging is required to be clean after desulfurization, and the molten iron surface is more than 90 percent after slagging.
2) Smelting in a converter: the converter smelting adopts a double-slag method, argon is supplied in the whole process in a converter bottom blowing mode, the tapping temperature range of the converter is 1650 ℃, the tapping time is controlled at 150s, the tapping adopts deoxidation alloying, the slag stopping operation is enhanced, and the content range of [ FeO + MnO ] in slag in molten steel at the end point of the converter is 16-24%.
3) Alloy fine adjustment station: blowing argon and stirring strongly to reduce the top slag.
4) LF: the content of [ FeO + MnO ] in the LF refining slag is less than 1%. White slag is produced, and top slag is fully reduced; controlling the content of [ Ca ] in the steel to be 0.0015-0.0030 percent; performing calcium treatment to ensure that the total time of weak stirring before and after calcium feeding is 11 min.
5) CSP continuous casting: the temperature of the middle ladle is controlled to be 15-35 ℃ above the liquidus temperature (TL (1514.4 ℃), and the pulling speed is 2.5 m/min. And the second cooling adopts a strong cooling water distribution system.
6) The tapping temperature was controlled to 1148 ℃.
7) Dephosphorization by high-pressure water: the dephosphorization water pressure is 320 bar.
8) And (3) adopting 7 stands for hot continuous rolling, and adopting dephosphorization water between stands between the F1 stand and the F2 stand and between the F2 stand and the F3 stand, wherein the dephosphorization water pressure is 8bar and 10bar respectively. The pressing rates of the F1 machine frame to the F7 machine frame are respectively 45%, 50%, 40%, 30%, 25%, 20% and 15%.
9) The finishing temperature was controlled at 884 ℃.
10) And (3) cooling: and adopting water curtain laminar flow cooling with the cooling speed of 80 ℃/s.
11) The coiling temperature was controlled at 603 ℃.
Examples 2 to 4
A hot-rolled structural steel with high surface quality, high toughness and high toughness produced by adopting a short process comprises the following chemical components in percentage by mass: the balance being Fe and inevitable impurity elements, as shown in Table 1.
The main process parameters and final properties of the production method of the hot-rolled structural steel with high surface quality, high toughness and high toughness, which is produced by adopting the short process, are shown in tables 2 to 3. Not shown in Table 2 is the same as example 1.
The inclusion rating of the hot rolled structural steel produced by the short process and having high surface quality and high toughness is shown in table 4, and it can be seen from the table that: the inclusion content was small in examples 1 to 4.
Comparative examples 1 to 3
The hot-rolled structural steel comprises the following chemical components in percentage by mass: the balance being Fe and inevitable impurity elements, as shown in Table 1.
Table 1 chemical compositions in wt% of examples 1 to 4 and comparative examples 1 to 3
| Categories | C | Si | Mn | P | S | Als | B | N |
| Example 1 | 0.1886 | 0.0354 | 0.9870 | 0.0144 | 0.0025 | 0.0242 | 0.0009 | 0.0007 |
| Example 2 | 0.1761 | 0.0376 | 0.8745 | 0.0130 | 0.0022 | 0.0202 | 0.0010 | 0.0006 |
| Example 3 | 0.1903 | 0.0253 | 0.6968 | 0.0147 | 0.0020 | 0.0176 | 0.0009 | 0.0010 |
| Example 4 | 0.1698 | 0.0390 | 0.9987 | 0.0133 | 0.0016 | 0.0253 | 0.0012 | 0.0009 |
| Comparative example 1 | 0.1209 | 0.0136 | 0.3613 | 0.0149 | 0.0090 | 0.0553 | 0.0035 | 0.0130 |
| Comparative example 2 | 0.1506 | 0.0215 | 0.6123 | 0.0230 | 0.0219 | 0.0630 | 0.0020 | 0.0010 |
| Comparative example 3 | 0.1606 | 0.0510 | 1.5061 | 0.0143 | 0.0223 | 0.0226 | 0.0019 | 0.0012 |
TABLE 2 Steel-smelting and hot-rolling processes and surface quality and platability conditions of examples 1 to 4 and comparative examples 1 to 3
TABLE 3 thickness, shape and mechanical Properties of examples 1 to 4 and comparative examples 1 to 3
| Categories | Thickness of | Convexity value (μm) | Yield strength (MPa) | Tensile strength (MPa) | Elongation (%) |
| Example 1 | 4.5 | 30 | 500 | 593 | 26.3 |
| Example 2 | 3.5 | 30 | 413 | 576 | 27.1 |
| Example 3 | 3.0 | 40 | 462 | 585 | 24.1 |
| Example 4 | 2.5 | 40 | 483 | 603 | 26.9 |
| Comparative example 1 | 3.0 | 50 | 380 | 500 | 21.0 |
| Comparative example 2 | 3.5 | 50 | 386 | 510 | 20.0 |
| Comparative example 3 | 4.5 | 50 | 550 | 613 | 16 |
TABLE 4 Inclusion rating of examples 1-4 and comparative examples 1-3
| Categories | A is thin | Coarse A | B is thin | B coarse | Fine diameter of C | Coarse fraction of C | D is thin | D coarse | DS |
| Example 1 | 0 | 0 | 0 | 0 | 0 | 0 | 0.5 | 0 | 0 |
| Example 2 | 0 | 0 | 0 | 0 | 0.5 | 0 | 0 | 0 | 0 |
| Example 3 | 0 | 0 | 0 | 0 | 0 | 0 | 0.5 | 0 | 0 |
| Example 4 | 0 | 0 | 0 | 0 | 0.5 | 0 | 0 | 0 | 0 |
| Comparative example 1 | 0 | 0 | 1.5 | 1.0 | 0 | 0 | 0.5 | 0 | 0.5 |
| Comparative example 2 | 1.0 | 0.5 | 1.5 | 1.5 | 0 | 0 | 0.5 | 0 | 1.0 |
| Comparative example 3 | 1.5 | 0.5 | 0 | 0 | 1.5 | 1.0 | 0 | 0.5 | 1.5 |
FIGS. 1 to 4 show metallographic structures of examples, in which bainite + ferrite was observed as the structure, the bainite ratio was 65% to 75%, and the grain size rating was 9.5. FIGS. 5 to 7 show the crystal phase structures of comparative examples 1 to 3, and it can be seen that the structures are pearlite + bainite + ferrite, and that a band-like structure is clearly present in the structures. FIG. 8 shows the thickness of the scale of example 1, measured at three locations of 5.15 μm, 5.15 μm and 4.56 μm, with an average of 4.95 μm; FIG. 9 shows the thickness of the scale in comparative example 2, which was 8.77 μm, 8.30 μm, and 8.42 μm in the three measured positions, respectively, and the average thickness was 8.50 μm compared to the example.
The invention provides a hot-rolled structural steel plate coil with high surface quality, high toughness and high toughness produced by adopting a short process and a method thereof through reasonable chemical component design and matching with steel making, continuous casting, hot rolling, cooling and coiling process control. The core production process is suitable for producing hot-rolled structural steel plates, and is also suitable for producing other coating and plating products and annealed products needing an annealing process.
The above description is only for specific exemplary description of the present invention, and it should be noted that the specific implementation of the present invention is not limited by the above manner, and it is within the protection scope of the present invention as long as various insubstantial modifications are made by using the technical idea and technical solution of the present invention, or the technical idea and technical solution of the present invention are directly applied to other occasions without modifications.
Claims (10)
1. The hot-rolled structural steel with high surface quality and high toughness produced by adopting the short process is characterized by comprising the following chemical components in percentage by mass:
c: 0.15-0.23%, Si: 0.005-0.05%, Mn: 0.20-1.20%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Als: 0.010-0.045%, B: 0.0005-0.0030%, N < 0.002%, and the balance Fe and inevitable impurities.
2. A method of producing a hot rolled structural steel with high surface quality and high toughness produced by a short process according to claim 1, comprising the steps of:
1) pretreating molten iron;
2) smelting in a converter;
3) an alloy fine tuning station;
4) refining in an LF furnace;
5) CSP continuous casting;
6) discharging;
7) removing phosphorus by using high-pressure water;
8) hot continuous rolling;
9) finish rolling;
10) cooling;
11) coiling;
step 1) molten iron pretreatment: and (3) desulfurizing by using a blowing method, wherein the temperature range of the molten iron before desulfurization is 1290-1370 ℃.
3. The production method according to claim 2, wherein step 2) converter smelting: the tapping temperature range of the converter is 1650-1680 ℃, and the tapping time is controlled between 150s and 250 s.
4. The production method according to claim 2, characterized in that step 5) CSP continuous casting: the temperature of the tundish is controlled to be 15-35 ℃ above the liquidus temperature, and the pulling speed is 2.5-3.1 m/min.
5. The production method according to claim 2, wherein the tapping temperature in step 6) is controlled to 1110 ℃ to 1150 ℃.
6. The production method according to claim 2, wherein step 7) is in particular: the dephosphorization water pressure is 320 bar-380 bar.
7. The production method according to claim 2, wherein step 8) is in particular: hot continuous rolling is carried out by adopting 7 stands, phosphorus removing water between the stands is adopted between the F1 stand and the F2 stand, and between the F2 stand and the F3 stand, and the phosphorus removing water pressure is 8-10 bar; the screw-down rates of the F1 frame to the F7 frame are respectively 45-50%, 50-55%, 40-45%, 30-35%, 25-30%, 20-25% and 15-20%.
8. The production method according to claim 2, wherein the finishing temperature in step 9) is controlled to 850 ℃ to 890 ℃.
9. The production method according to claim 2, characterized in that step 10) cools: and adopting water curtain laminar flow cooling at the cooling speed of 70-100 ℃/s.
10. The production method according to claim 2, wherein the coiling temperature in step 11) is controlled to be 590 ℃ to 650 ℃.
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| CN112538594A (en) * | 2020-11-10 | 2021-03-23 | 江苏省沙钢钢铁研究院有限公司 | Low-cost hot-rolled coil with yield strength of 500MPa and preparation method thereof |
| CN113263051A (en) * | 2021-04-16 | 2021-08-17 | 首钢集团有限公司 | Method for reducing press-in defects of iron sheet on surface of B-carbon-containing structural steel pickling plate |
| CN114411062A (en) * | 2022-01-21 | 2022-04-29 | 吉林建龙钢铁有限责任公司 | Steel for high-strength packing belt and preparation method thereof |
| CN114410875A (en) * | 2022-03-10 | 2022-04-29 | 马鞍山钢铁股份有限公司 | Steel with good low-temperature toughness for easily galvanized power transmission tower and manufacturing method thereof |
| CN115029636A (en) * | 2022-06-20 | 2022-09-09 | 武汉钢铁有限公司 | 450 MPa-grade high-corrosion-resistance coating thin steel plate produced by adopting short process and method |
| CN115491601A (en) * | 2022-09-20 | 2022-12-20 | 武汉钢铁有限公司 | Economical magnet yoke steel with yield strength of 350MPa grade produced by CSP production line and production method |
| CN116287957A (en) * | 2023-04-11 | 2023-06-23 | 攀枝花学院 | Vanadium-containing hot dip galvanized steel and smelting method thereof |
| CN116287957B (en) * | 2023-04-11 | 2024-05-17 | 攀枝花学院 | Vanadium-containing hot dip galvanized steel and smelting method thereof |
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Application publication date: 20200327 |