CN114574782A - 450 MPa-grade wear-resistant corrosion-resistant steel and manufacturing method thereof - Google Patents
450 MPa-grade wear-resistant corrosion-resistant steel and manufacturing method thereof Download PDFInfo
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- 239000010935 stainless steel Substances 0.000 title claims abstract description 22
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 14
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 56
- 239000010959 steel Substances 0.000 claims abstract description 56
- 238000005299 abrasion Methods 0.000 claims abstract description 9
- 239000000126 substance Substances 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 238000005096 rolling process Methods 0.000 claims description 31
- 238000010438 heat treatment Methods 0.000 claims description 17
- 238000001816 cooling Methods 0.000 claims description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 14
- 238000000034 method Methods 0.000 claims description 13
- 238000009749 continuous casting Methods 0.000 claims description 11
- 230000008569 process Effects 0.000 claims description 8
- 229910052787 antimony Inorganic materials 0.000 claims description 6
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 238000007664 blowing Methods 0.000 claims description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 4
- 238000003723 Smelting Methods 0.000 claims description 4
- 230000009467 reduction Effects 0.000 claims description 4
- 238000003756 stirring Methods 0.000 claims description 4
- 238000006477 desulfuration reaction Methods 0.000 claims description 3
- 230000023556 desulfurization Effects 0.000 claims description 3
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 claims description 2
- 229910052786 argon Inorganic materials 0.000 claims description 2
- 239000000446 fuel Substances 0.000 claims description 2
- 238000004321 preservation Methods 0.000 claims description 2
- 238000010079 rubber tapping Methods 0.000 claims description 2
- 238000002791 soaking Methods 0.000 claims description 2
- 238000009847 ladle furnace Methods 0.000 claims 2
- 230000007797 corrosion Effects 0.000 abstract description 17
- 238000005260 corrosion Methods 0.000 abstract description 17
- 238000005728 strengthening Methods 0.000 description 13
- 238000001556 precipitation Methods 0.000 description 12
- 230000000694 effects Effects 0.000 description 9
- 229910045601 alloy Inorganic materials 0.000 description 8
- 239000000956 alloy Substances 0.000 description 8
- 229910052804 chromium Inorganic materials 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 5
- 239000003245 coal Substances 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 230000009471 action Effects 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 229910052721 tungsten Inorganic materials 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000002378 acidificating effect Effects 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000011362 coarse particle Substances 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000003912 environmental pollution Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000008595 infiltration Effects 0.000 description 1
- 238000001764 infiltration Methods 0.000 description 1
- 230000037427 ion transport Effects 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910000510 noble metal Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000002161 passivation Methods 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 239000010970 precious metal Substances 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000002689 soil Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
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- 239000013585 weight reducing agent Substances 0.000 description 1
Classifications
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
-
- 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
- C21D8/0226—Hot rolling
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides 450 MPa-grade wear-resistant corrosion-resistant steel and a manufacturing method thereof, wherein the steel comprises the following chemical components in percentage by weight: 0.061-0.082% of C, 0.51-0.79% of Si, 0.45-0.89% of Mn, less than or equal to 0.018% of P, less than or equal to 0.006% of S, 0.81-1.31% of Cr0.14-0.24% of Cu, 0.041-0.075% of Sb0.15-0.35% of W, 0.051-0.072% of Ti0.015-0.045% of Als, less than or equal to 0.004% of N, and the balance of Fe and inevitable impurities. The steel plate has good corrosion resistance, abrasion resistance and excellent formability, and is suitable for manufacturing lightweight containers.
Description
Technical Field
The invention relates to the field of corrosion-resistant steel, in particular to 450 MPa-grade wear-resistant corrosion-resistant steel and a manufacturing method thereof.
Background
In recent years, with the rapid development of society and economy, energy conservation, consumption reduction, pollution reduction and resource conservation become very urgent problems. For the railway container, the self weight is reduced, so that the energy can be saved, the consumption can be reduced, the environmental pollution can be reduced, and the load capacity of the container can be increased. To meet this demand, it is currently common to use higher strength steel plates, thereby reducing the thickness of the steel plates used and achieving the goal of weight reduction. However, as the steel sheet is used in higher grades, the manufactured parts are partially worn and corroded seriously due to insufficient hardness when transporting ore or coal, and the safety is seriously affected when the manufactured parts are continuously thinned.
Patent document CN112159934A discloses a "steel plate with resistance to corrosion, wear and abrasion and its preparation method", which is a new steel plate with excellent resistance to corrosion, wear and abrasion in acidic environment prepared by using martensite as matrix structure obtained by alloy composition design and heat treatment process. The patent document CN107653423B entitled "coal water abrasion corrosion resistant steel plate for coal vehicle for railway and manufacturing method thereof" controls the contents of C, Cr and Ni to satisfy 1.6% or more and 12C + Cr/Ni or less and 2.8%, and the abrasion corrosion rate of Q450NQR1 is 20% -30%. More Ni element is added, so that the cost is higher, and the popularization and the application are not facilitated. CN104662193A discloses "a wear-resistant steel sheet excellent in low-temperature toughness and resistance to corrosive wear", which is a steel sheet having a structure in which the content of Cr and Mo dissolved in a solid solution in the steel is controlled so as to be 0.05 to 2.5Mo and 2.0 to 0 (%) and the primary phase is a quenched martensite phase and the prior austenite grain size is 30 μm or less, whereby the resistance to corrosive wear is greatly improved, but the environment of use is wear caused by contact between sand and soil containing water in construction sites such as buildings, civil engineering, mines, etc. The patent document CN101423916B entitled "Low-alloy wear-resistant and corrosion-resistant Steel and method for manufacturing the same" discloses a low-alloy wear-resistant and corrosion-resistant steel suitable for use in marine silt-wear corrosion environments, which is obtained by modifying Mn-Si-Cr-Mo-Al series carbide-free Bainite steel through appropriate adjustment of carbon content and addition of Al and Nb elements which are helpful for improving corrosion resistance of the alloy, and rare earth. The high-Si and high-Al alloy mainly adopts high-Si and high-Al component design to inhibit the formation of carbide, and elements such as Cr, Ni and Mo are added to improve the corrosion resistance, and the noble metals Mo, Ni and Nb are added, so that the cost is higher.
In the prior art, the wear-resistant steel plate or the wear-resistant corrosion-resistant steel plate with martensite as a matrix structure is mainly obtained by adopting a heat treatment process, or more precious metals are added, so that the cost is higher, and the research on producing the wear-resistant corrosion-resistant steel plate by adopting a hot rolling process is less. Therefore, how to obtain the wear-resistant corrosion-resistant steel by adopting a hot rolling process is one of the technical difficulties to be solved urgently in the field.
Disclosure of Invention
The invention aims to provide 450 MPa-grade wear-resistant corrosion-resistant steel and a manufacturing method thereof, wherein the steel plate has good corrosion resistance, wear resistance and excellent formability and is suitable for manufacturing lightweight containers.
In order to achieve the purpose, the invention adopts the following technical scheme:
the 450 MPa-grade wear-resistant corrosion-resistant steel comprises the following chemical components in percentage by weight: 0.061-0.082% of C, 0.51-0.79% of Si, 0.45-0.89% of Mn, less than or equal to 0.018% of P, less than or equal to 0.006% of S, 0.81-1.31% of Cr, 0.14-0.24% of Cu, 0.041-0.075% of Sb, 0.15-0.35% of W, 0.051-0.072% of Ti, 0.015-0.045% of Als, less than or equal to 0.004% of N, and the balance of Fe and inevitable impurities.
The invention selects the above alloy element types and contents because:
c is a key element for obtaining high strength and hardness of the steel plate, and can form fine carbide TiC with Ti to play a role in precipitation strengthening. However, more C is detrimental to the welding, toughness and plasticity of the steel plate. The content of C in the invention is limited to 0.061% -0.082%.
Si can be dissolved in ferrite and austenite to improve the hardness and strength of steel, but if the content is too high, red iron scales on the surface of a rolled steel plate are serious, and the welding of the steel plate is not facilitated. The content of Si is limited to 0.51-0.79% in the invention.
The main role of Mn in steel is solid solution strengthening, which acts to improve the strength of the steel sheet. The invention can obviously reduce the transformation temperature of austenite to ferrite, refine the microstructure of steel, ensure the strength index and wear resistance of steel plate, but the hardenability is increased due to excessive Mn content, thereby causing the weldability and the toughness of welding heat affected zone to be deteriorated, and simultaneously considering the cost factor, the invention controls the content of the Mn content to be 0.45-0.89%.
P and S are impurity elements in steel, so that the ductility and the welding performance are obviously reduced, and the performance is improved by controlling the content of P, S to be lower. The steel of the invention controls P to be less than or equal to 0.018 percent and S to be less than or equal to 0.006 percent.
Cr forms a compact oxide film on the surface of steel, and the passivation capability of the steel is improved. When added into steel together with Cu, the corrosion resistance effect is particularly obvious. In addition, Cr element can form cementite and various carbides in steel, and can obviously improve the strength, hardness and wear resistance of the steel. The content range of the invention is limited to 0.81-1.31%.
Cu is the most important of the atmospheric corrosion resistant steels for improving the atmospheric corrosion resistance, and can also improve the strength of the steel, and the content is too high, so that hot brittleness is easily caused. The content range of the invention is limited to 0.14-0.24%.
Sb is often continuously enriched in steel as a harmful element, and seriously affects the quality of steel. In the invention, Sb is an effective element for improving corrosion resistance, and is synergistically enriched in the rust layer through the composite addition of Sb, Cr and W, except for forming WO3The Sb is promoted outside the protective product film2O5With the formation of CuO, aggressive ion transport is significantly impeded. The content range of the invention is limited to 0.041% -0.075%.
W can form tungstate radical or W carbide, promote the formation of protective product film or passive film, partially dissolve into iron to form solid solution, can obviously improve the wear resistance of steel, comprehensively consider cost factor, the invention limits the content range to 0.15% -0.35%.
Ti is a strong carbonitride forming element and is an important microalloy strengthening element in the invention, not only can effectively refine grains, but also can form fine carbide, nitride or carbonitride with C and N, and particularly, the nano TiC precipitated in the coiling and slow cooling processes has very high precipitation strengthening effect. The TiC can not only strengthen the strength of the matrix, but also improve the wear resistance of the steel plate. The invention limits the range to 0.051-0.072%.
And Als: is a common deoxidizer, and the range of the deoxidizer is limited to 0.015 to 0.045 percent.
N is an element existing in the smelting process, and because one of the characteristics of the invention is that Ti microalloying technology is adopted to improve the wear resistance of the steel plate, and Ti is an element with strong activity, the Ti reacts with elements such as O, N, S in the steel, if the content of N is too high, TiN with coarse size can be separated out in molten steel, the austenite grain can not be prevented from growing, the precipitation strengthening effect can not be achieved, and the refined grain of Ti and the precipitation strengthening effect can be reduced. Therefore, in the invention, N is controlled to be less than or equal to 0.004 percent.
The yield strength of the wear-resistant corrosion-resistant steel is more than 450MPa, the tensile strength is more than 550MPa, and the elongation is more than 22%.
A manufacturing method of 450 MPa-grade wear-resistant corrosion-resistant steel is manufactured by molten iron pre-desulfurization, converter top and bottom combined blowing, LF external refining, slab continuous casting, slab heating, hot continuous rolling, laminar cooling and coiling, and the wear-resistant corrosion-resistant steel plate containing the chemical components is specifically manufactured by the following steps:
1) heating the continuous casting blank to 1251-1278 ℃ through a heating furnace, wherein the heating steel burning atmosphere is a reducing atmosphere, and the air-fuel ratio is lower than 2.0; slowly heating at the temperature of below 1100 ℃, wherein the heating rate is 7.9-8.9 ℃/min; quickly burning at a high temperature of over 1100 ℃, wherein the heating rate is 12.5-14.5 ℃/min; the heat preservation time of the soaking section is 25-40 min, and the total in-furnace time is not more than 180 min; the surface defects caused by the precipitation of low-melting-point elements Cu and Sb on the surface of the strip steel are prevented, so that the fine defects generated on the low-melting-point elements Cu and Sb on the surface of the plate blank can be fully oxidized to form loose and easily-removed iron scales, and the surface quality of the strip steel is improved.
2) In the step of controlled rolling, two-stage controlled rolling is adopted, a 3+3 mode is adopted for rough rolling, descaling is carried out on each pass of rough rolling, and the outlet temperature of the rough rolling is more than 1100 ℃.
3) The finish rolling adopts 7 stands for continuous rolling, the start temperature of the finish rolling is 1075-1090 ℃, and the finish rolling temperature is 901-935 ℃.
4) And (3) carrying out laminar cooling after finish rolling, cooling to 601-635 ℃ at a cooling rate of 21-31 ℃/s, coiling, and then air cooling to room temperature. And front-section centralized cooling is adopted in laminar cooling.
Rough rolling is carried out in the temperature range higher than 1100 ℃, band steel is not allowed to swing, finish rolling is started at 1075-1090 ℃, the start rolling temperature of the finish rolling is higher than 1090 ℃, crystal grains of a finished product are not easy to refine, and the fine grain strengthening effect is not good; the temperature of the tail part of the strip steel is quickly reduced below 1075 ℃, so that the load of a finish rolling machine frame is increased, and accidents are easily caused; when the finish rolling temperature is lower, the method is beneficial to the refinement of ferrite grain size and the improvement of fine-grain strengthening effect, but simultaneously, the lower finish rolling temperature can induce the deformation induced precipitation of the carbonitride. Although such precipitates inhibit austenite grain growth and perform a certain fine grain strengthening action and a precipitation strengthening action, they are relatively large in size compared with nano-sized grains precipitated from ferrite, and the precipitation strengthening action is reduced. Therefore, the finishing temperature of the invention is preferably controlled between 901 and 935 ℃. And after rolling, carrying out laminar cooling and coiling. The laminar flow adopts front-stage concentrated cooling, the cooling speed is too low, Ti carbide can be precipitated in the cooling process, coarse particles are increased in the finished product, the precipitation strengthening effect after coiling is insufficient, and in order to ensure that a large amount of fine secondary phase precipitated particles are obtained after coiling, the cooling speed is set to be 21-31 ℃/s. The coiling temperature is too high, the precipitation obtained after coiling is relatively thick, and the precipitation strengthening effect is weak; when the coiling temperature is too low, precipitation of precipitates becomes insufficient, and a desired strength cannot be obtained. Therefore, the coiling temperature of the invention is preferably controlled to be 601-635 ℃.
The molten iron pretreatment adopts converter smelting, top blowing or top-bottom combined blowing, LF furnace desulfurization treatment, and continuous casting adopts electromagnetic stirring and dynamic soft reduction to improve the quality of continuous casting slabs. In the converter process, a mode of adding antimony ingots after tapping is adopted, and argon is used for stirring, so that the alloy is completely melted and the components are uniform.
The thickness of the continuous casting billet is 200-230 mm.
Compared with the prior art, the invention has the beneficial effects that:
the invention adopts the alloy component design of high Si, corrosion resisting elements Cr, Cu and Sb and micro-alloy elements Ti and W, and forms a certain amount of FeMnCrC, TiC and WC through the synergistic effect of the elements Si, Mn, Cr and W, thereby improving the wear resistance of the steel plate in the atmospheric environment, and the wear resistance of the steel plate reaches 25 to 35 percent of that of the prior steel. In addition, the preparation method of the corrosion-resistant and wear-resistant steel plate is simple, does not need a heat treatment process, can be widely applied to point-to-point transportation of ores, coal and the like, and is convenient and quick.
Detailed Description
The present invention is described in more detail by way of examples, which are merely illustrative of the best mode of carrying out the invention and are not intended to limit the scope of the invention in any way.
The present invention will be described in more detail with reference to examples.
Table 1 shows the chemical compositions in wt% of examples 1 to 8
| Serial number | C | Si | Mn | P | S | Als | Cr | Cu | W | Ti | Sb | N |
| Example 1 | 0.061 | 0.51 | 0.45 | 0.018 | 0.005 | 0.015 | 0.81 | 0.14 | 0.15 | 0.072 | 0.041 | 0.0032 |
| Example 2 | 0.064 | 0.55 | 0.53 | 0.016 | 0.004 | 0.035 | 1.25 | 0.22 | 0.32 | 0.069 | 0.054 | 0.0035 |
| Example 3 | 0.067 | 0.59 | 0.61 | 0.017 | 0.004 | 0.025 | 1.19 | 0.19 | 0.29 | 0.066 | 0.071 | 0.0034 |
| Example 4 | 0.071 | 0.62 | 0.69 | 0.015 | 0.005 | 0.027 | 0.95 | 0.23 | 0.25 | 0.064 | 0.060 | 0.0035 |
| Example 5 | 0.073 | 0.67 | 0.77 | 0.018 | 0.004 | 0.020 | 0.99 | 0.16 | 0.24 | 0.061 | 0.075 | 0.0036 |
| Example 6 | 0.075 | 0.70 | 0.79 | 0.013 | 0.003 | 0.030 | 1.12 | 0.17 | 0.22 | 0.058 | 0.058 | 0.0039 |
| Example 7 | 0.078 | 0.75 | 0.81 | 0.014 | 0.005 | 0.040 | 0.88 | 0.15 | 0.18 | 0.054 | 0.065 | 0.0037 |
| Example 8 | 0.082 | 0.79 | 0.89 | 0.016 | 0.004 | 0.045 | 1.31 | 0.24 | 0.35 | 0.051 | 0.044 | 0.0036 |
Examples 1-8 having the chemical compositions of table 1 were made by the following procedure:
smelting in a converter, then carrying out external refining, and casting to obtain a continuous casting billet. The thickness of the continuous casting billet is 200mm-230mm, the continuous casting billet is sent to a hot rolling production line, the heating outlet temperature of the casting billet is 1251-.
The rolling process parameters of the steels of the examples of the invention are shown in table 2.
TABLE 2 Rolling Process parameters for examples 1-8
TABLE 3 mechanical Properties of examples 1 to 8
As can be seen from Table 3, the yield strengths of the steels of the examples of the invention are all more than 450MPa, the tensile strengths are all more than 550MPa, the elongations are all more than 22%, the cold bending properties are all qualified, and the wear resistance rate reaches about 25% -35% of SPA-H. Table 3 shows that the steel of the present invention has excellent mechanical properties as a whole.
TABLE 4 Corrosion resistance results (g/m) for inventive and comparative steels2.h)
| Serial number | 72h | 10H2SO4+3.5NaCl，24h |
| Example 1 | 1.0728 | 0.8529 |
| Example 2 | 1.2972 | 0.8788 |
| Example 3 | 1.2451 | 0.8659 |
| Example 4 | 1.3284 | 0.8428 |
| Example 5 | 1.1235 | 0.8688 |
| Example 6 | 1.0824 | 0.8631 |
| Example 7 | 1.0969 | 0.8988 |
| Example 8 | 1.3039 | 0.8458 |
| SPA-H | 1.6421 | 2.1391 |
| Q345B | 3.1957 | 5.9052 |
A72 hour periodic infiltration corrosion test was performed according to TB/T2375 + 1993. A10H 2SO4+3.5NaCl soak test was performed for 24H, see JB/T7901-1999. Table 4 shows the results of the atmospheric corrosion resistance of the steels of the examples according to the invention and the comparative steels SPA-H and Q345B. As can be seen from Table 4, the weather resistance of the steel of the embodiment of the invention is obviously superior to that of SPA-H and Q345B, and the service life of the steel plate when the thickness is reduced can be effectively ensured.
The above-mentioned embodiments are merely illustrative of the technical ideas and features of the present invention, and are not intended to limit the present invention, so as to enable those skilled in the art to understand the contents of the present invention and to implement the present invention accordingly. All equivalent changes and modifications made according to the spirit of the present invention should be covered within the protection scope of the present invention.
Claims (5)
1. The 450 MPa-grade wear-resistant corrosion-resistant steel is characterized by comprising the following chemical components in percentage by weight: 0.061-0.082% of C, 0.51-0.79% of Si, 0.45-0.89% of Mn, less than or equal to 0.018% of P, less than or equal to 0.006% of S, 0.81-1.31% of Cr, 0.14-0.24% of Cu, 0.041-0.075% of Sb, 0.15-0.35% of W, 0.051-0.072% of Ti, 0.015-0.045% of Als, less than or equal to 0.004% of N, and the balance of Fe and inevitable impurities.
2. The 450MPa grade abrasion and corrosion resistant steel according to claim 1, wherein the yield strength of the abrasion and corrosion resistant steel is more than 450MPa, the tensile strength is more than 550MPa, and the elongation is more than 22%.
3. The method for manufacturing the 450MPa grade abrasion and corrosion resistant steel according to claim 1 or 2, which is characterized by comprising the following steps:
1) heating the continuous casting blank to 1251-1278 ℃ through a heating furnace, wherein the heating steel burning atmosphere is a reducing atmosphere, and the air-fuel ratio is lower than 2.0; slowly heating at the temperature of below 1100 ℃, wherein the heating rate is 7.9-8.9 ℃/min; quickly burning at a high temperature of over 1100 ℃, wherein the heating rate is 12.5-14.5 ℃/min; the heat preservation time of the soaking section is 25-40 min, and the total in-furnace time is not more than 180 min;
2) two-stage controlled rolling is adopted, a 3+3 mode is adopted for rough rolling, descaling is carried out on each pass of rough rolling, and the outlet temperature of the rough rolling is more than 1100 ℃;
3) the finish rolling adopts continuous rolling, the start rolling temperature of the finish rolling is 1075-1090 ℃, and the finish rolling temperature is 901-935 ℃;
4) and (3) carrying out laminar cooling after finish rolling, cooling to 601-635 ℃ at a cooling rate of 21-31 ℃/s, coiling, and then air cooling to room temperature.
4. The method for manufacturing the 450 MPa-grade wear-resistant corrosion-resistant steel according to claim 3, characterized in that the molten iron pretreatment comprises the steps of smelting in a converter, top blowing or top-bottom combined blowing, desulfurization in an LF (ladle furnace), continuous casting by adopting electromagnetic stirring and dynamic soft reduction, and stirring by using argon in a manner of adding antimony ingots after tapping in a converter process.
5. The manufacturing method of 450MPa grade abrasion and corrosion resistant steel according to claim 3 or 4, wherein the thickness of the continuous casting billet is 200-230 mm.
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| CN115747637A (en) * | 2022-10-18 | 2023-03-07 | 武汉钢铁有限公司 | Economical marine atmospheric corrosion resistant steel and production method thereof |
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| CN101705425A (en) * | 2009-11-06 | 2010-05-12 | 武汉钢铁(集团)公司 | Ti-contained sulphuric acid dew-point corrosion resisting steel with tensile strength not less than 450 MPa) |
| CN109628843A (en) * | 2019-02-12 | 2019-04-16 | 鞍钢股份有限公司 | 450MPa grades of transporting coal open-top car corrosion-resisting steels of yield strength and its manufacturing method |
| CN111534746A (en) * | 2020-04-30 | 2020-08-14 | 鞍钢股份有限公司 | Weather-resistant steel for wide 450 MPa-grade hot-rolled container and manufacturing method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101705425A (en) * | 2009-11-06 | 2010-05-12 | 武汉钢铁(集团)公司 | Ti-contained sulphuric acid dew-point corrosion resisting steel with tensile strength not less than 450 MPa) |
| CN109628843A (en) * | 2019-02-12 | 2019-04-16 | 鞍钢股份有限公司 | 450MPa grades of transporting coal open-top car corrosion-resisting steels of yield strength and its manufacturing method |
| CN111534746A (en) * | 2020-04-30 | 2020-08-14 | 鞍钢股份有限公司 | Weather-resistant steel for wide 450 MPa-grade hot-rolled container and manufacturing method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN115747637A (en) * | 2022-10-18 | 2023-03-07 | 武汉钢铁有限公司 | Economical marine atmospheric corrosion resistant steel and production method thereof |
| CN115747637B (en) * | 2022-10-18 | 2024-02-13 | 武汉钢铁有限公司 | Economical ocean atmospheric corrosion resistant steel and production method thereof |
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