CN114686763B - 550 MPa-grade wear-resistant corrosion-resistant steel - Google Patents
550 MPa-grade wear-resistant corrosion-resistant steel Download PDFInfo
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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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- 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
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- 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
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- C21D8/0226—Hot rolling
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
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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
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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
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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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- 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
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Abstract
The invention provides 550 MPa-grade wear-resistant corrosion-resistant steel, which comprises the following chemical components in percentage by weight: 0.065-0.086% of C, 0.58-0.86% of Si, 0.90-1.47% of Mn, less than or equal to 0.018% of P, less than or equal to 0.006% of S, 0.85-1.39% of Cr, 0.14-0.24% of Cu, 0.051-0.084% of Sb, 0.25-0.45% of W, 0.066-0.086% 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 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 550 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, energy can be saved, consumption can be reduced, 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 at higher grades, the manufactured parts are partially worn and corroded seriously when transporting ore or coal due to insufficient hardness, and the safety is seriously affected when the manufactured parts are continuously thinned.
The patent document CN112159934A discloses a corrosion-wear-resistant steel plate and a preparation method thereof, which is a novel steel plate with excellent corrosion-wear resistance in an acid environment, wherein martensite is used as a matrix structure through alloy component design and a heat treatment process. The patent document CN107653423B discloses a coal water corrosion resistant steel plate for railway coal vehicle and its manufacturing method, which controls the contents of C, cr and Ni to meet the requirement of 1.6% to 12C + Cr/Ni to 2.8%, and the relative Q450NQR1 wear corrosion rate 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 contents of Cr and Mo dissolved in a steel are controlled so as to satisfy 0.05 to 2.0 (%) inclusive, and the primary phase is a quenched martensite phase and the prior austenite grain diameter is 30 μm or less, thereby achieving the object of greatly improving the resistance to corrosive wear, 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 discloses a low-alloy wear-resistant corrosion-resistant steel and a manufacturing method thereof, which forms Mn-Si-Cr-Mo-Al series carbide-free bainite steel by properly adjusting the carbon content, adding Al and Nb which are elements contributing to improving the corrosion resistance of the alloy and performing modification treatment on rare earth, thereby obtaining the low-alloy wear-resistant corrosion-resistant steel suitable for a marine silt wear corrosion environment. 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 precious 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 550 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 550 MPa-grade wear-resistant corrosion-resistant steel comprises the following chemical components in percentage by weight: 0.065-0.086% of C, 0.58-0.86% of Si, 0.90-1.47% of Mn, less than or equal to 0.018% of P, less than or equal to 0.006% of S, 0.85-1.39% of Cr, 0.14-0.24% of Cu, 0.051-0.084% of Sb, 0.25-0.45% of W, 0.066-0.086% 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 is limited to 0.065-0.086 percent in the invention.
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 0.58-0.86% 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 0.90-1.47%.
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 lower P and S. 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 0.85% -1.39%.
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 Sb, cr and W are added in a compounding manner and are synergistically enriched in a rust layer, so that the formation of Sb2O5 and CuO is promoted in addition to the formation of a WO3 protective product film, and the transmission of etching ions is obviously hindered. The content range of the invention is limited to 0.051 percent to 0.084 percent.
W can form tungstate radicals or W carbide, promotes the formation of a protective product film or a passive film, is partially dissolved in iron to form a solid solution, can obviously improve the wear resistance of steel, and comprehensively considers the cost factor, and the content range of the W is limited to 0.25-0.45 percent.
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 0.066% -0.086%.
And (3) 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 to adopt Ti microalloying technology to improve the wear resistance of the steel plate, and Ti is an element with strong activity, the Ti reacts with elements in steel such as O, N, S and the like, if the content of N is too high, tiN with large size can be separated out from molten steel, the austenite crystal grain can not be prevented from growing, the precipitation strengthening effect can not be realized, and on the contrary, the refined crystal grain and the precipitation strengthening effect of Ti 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 550MPa, the tensile strength is more than 650MPa, and the elongation is more than 20%.
A manufacturing method of 550 MPa-level wear-resistant corrosion-resistant steel is characterized by comprising the following steps of water pre-desulfurization, converter top and bottom combined blowing, LF external refining, slab continuous casting, slab heating, hot continuous rolling, laminar cooling and coiling, and specifically comprises the following steps:
1) Heating the continuous casting plate blank to 1254-1282 ℃ by a heating furnace, wherein the heating steel burning atmosphere is a reducing atmosphere, the air-fuel ratio is lower than 2.0, the continuous casting plate blank is slowly heated when the temperature is lower than 1100 ℃, and the heating rate is 7.7-8.7 ℃/min; the high-temperature quick firing is carried out at the temperature of more than 1100 ℃, the heating rate is 12.3-14.3 ℃/min, the heat preservation time of the soaking section is 27-43 min, and the total furnace time is not more than 183min; 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) Two-stage rolling control is adopted, the rough rolling adopts a 3+3 mode, descaling is carried out on each pass of the 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 1079-1094 ℃, and the finish rolling temperature is 905-939 ℃.
4) After finish rolling, laminar cooling is carried out, the steel is cooled to 605 to 639 ℃ at the cooling rate of 24 to 34 ℃/s for coiling, and then the steel is air-cooled 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 ℃, the band steel is not allowed to swing, finish rolling is started at 1079-1094 ℃, the start rolling temperature of the finish rolling is higher than 1094 ℃, crystal grains of finished products are not easy to refine, and the fine grain strengthening effect is poor; the temperature of the tail part of the strip steel is quickly reduced below 1079 ℃, so that the load of a finish rolling machine frame is increased, and accidents are easily caused; when the finishing rolling temperature is lower, the grain size of ferrite is favorably refined, and the fine-grain strengthening effect is improved, but simultaneously, the lower finishing rolling temperature can induce the deformation induced precipitation of carbonitride. Although the precipitates inhibit the growth of austenite grains and perform certain functions of fine grain strengthening and precipitation strengthening, the precipitates are relatively large in size compared with ferrite-precipitated nano-scale particles, and the precipitation strengthening effect is reduced. Therefore, the finishing temperature of the invention is preferably controlled between 905 ℃ and 939 ℃. And after rolling, carrying out laminar cooling and coiling. The laminar flow is intensively cooled in the front section, 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 the cooling speed is set to be 24-34 ℃/s in order to ensure that a large amount of fine secondary phase precipitated particles are obtained after coiling. The coiling temperature is too high, the precipitation phase obtained after coiling is 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 in the present invention is preferably controlled to 605 to 639 ℃.
Smelting and continuous casting process: 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 20-30 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 | 0.065 | 0.58 | 0.90 | 0.017 | 0.006 | 0.015 | 0.85 | 0.14 | 0.25 | 0.086 | 0.084 | 0.0034 |
| Example 2 | 0.082 | 0.82 | 1.37 | 0.016 | 0.004 | 0.025 | 1.26 | 0.21 | 0.42 | 0.068 | 0.056 | 0.0032 |
| Example 3 | 0.069 | 0.77 | 0.91 | 0.018 | 0.005 | 0.035 | 1.18 | 0.19 | 0.27 | 0.083 | 0.071 | 0.0034 |
| Example 4 | 0.071 | 0.62 | 0.99 | 0.013 | 0.005 | 0.027 | 0.95 | 0.23 | 0.29 | 0.084 | 0.079 | 0.0036 |
| Example 5 | 0.073 | 0.67 | 0.94 | 0.018 | 0.004 | 0.020 | 0.99 | 0.16 | 0.31 | 0.081 | 0.075 | 0.0037 |
| Example 6 | 0.075 | 0.70 | 1.19 | 0.013 | 0.003 | 0.030 | 1.12 | 0.15 | 0.34 | 0.078 | 0.061 | 0.0039 |
| Example 7 | 0.078 | 0.75 | 1.25 | 0.015 | 0.006 | 0.041 | 0.89 | 0.17 | 0.37 | 0.074 | 0.066 | 0.0036 |
| Example 8 | 0.086 | 0.86 | 1.47 | 0.016 | 0.004 | 0.045 | 1.39 | 0.24 | 0.45 | 0.066 | 0.051 | 0.0038 |
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. And (2) conveying the continuous casting slab to a hot rolling production line, wherein the heating outlet temperature of the continuous casting slab is 1254-1282 ℃, the rolling start temperature of the fine rolling is 1079-1094 ℃, the final rolling temperature of the fine rolling is 905-939 ℃, laminar cooling is adopted after rolling, the cooling speed is 24-34 ℃/s, the coiling temperature is 605-639 ℃, and the air cooling is carried out to the room temperature after coiling.
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 550MPa, the tensile strengths are all more than 650MPa, the elongations are all more than 20%, the cold bending properties are all qualified, and the wear resistance rate reaches about 20% -30% 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 steels 2 .h)
| Serial number | 72h | 10H 2 SO 4 +3.5NaCl，24h |
| Example 1 | 1.0628 | 0.7524 |
| Example 2 | 1.1472 | 0.8087 |
| Example 3 | 1.2351 | 0.8599 |
| Example 4 | 1.3084 | 0.8529 |
| Example 5 | 1.1934 | 0.8912 |
| Example 6 | 1.0875 | 0.8101 |
| Example 7 | 1.0954 | 0.8487 |
| Example 8 | 1.2835 | 0.8758 |
| SPA-H | 1.6421 | 2.1391 |
| Q345B | 3.1957 | 5.9052 |
A72 hour periodic infiltration corrosion test was performed according to TB/T2375-1993. A soak test of 10H2SO4+3.5NaCl was performed for 24h with reference to JB/T7901-1999. Table 4 shows the results of the atmospheric corrosion resistance of the steels of the examples of 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 (4)
1. The 550 MPa-grade wear-resistant corrosion-resistant steel is characterized by comprising the following chemical components in percentage by weight: 0.065-0.086% of C, 0.58-0.86% of Si, 0.90-1.47% of Mn, less than or equal to 0.018% of P, less than or equal to 0.006% of S, 0.99-1.39% of Cr, 0.14-0.24% of Cu, 0.051-0.084% of Sb, 0.25-0.45% of W, 0.066-0.086% 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 manufacturing method of the 550 MPa-grade wear-resistant corrosion-resistant steel specifically comprises the following steps:
1) Heating the continuous casting plate blank to 1254-1282 ℃ by a heating furnace, wherein the heating steel burning atmosphere is a reducing atmosphere, the air-fuel ratio is lower than 2.0, the continuous casting plate blank is slowly heated when the temperature is lower than 1100 ℃, and the heating rate is 7.7-8.7 ℃/min; the high-temperature quick firing is carried out at the temperature of more than 1100 ℃, the heating rate is 12.3-14.3 ℃/min, the heat preservation time of the soaking section is 27-43 min, and the total furnace time is not more than 183min;
2) The two-stage rolling is controlled, the mode of 3+3 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 1079-1094 ℃, and the finish rolling temperature of the finish rolling is 905-939 ℃;
4) After finish rolling, laminar cooling is carried out, the steel is cooled to 605-639 ℃ at the cooling rate of 24-34 ℃/s for coiling, and then the steel is air-cooled to room temperature.
2. The 550MPa grade abrasion and corrosion resistant steel according to claim 1, wherein the yield strength of the abrasion and corrosion resistant steel is more than 550MPa, the tensile strength is more than 650MPa, and the elongation is more than 20%.
3. The 550 MPa-grade wear-resistant corrosion-resistant steel according to claim 1, wherein molten iron is pretreated by converter smelting and subjected to top-blowing or top-bottom combined blowing, an LF furnace is subjected to desulfurization treatment, continuous casting is performed by electromagnetic stirring and dynamic soft reduction, and a converter procedure adopts a mode of adding antimony ingots after tapping and stirring by argon.
4. The 550MPa grade abrasion and corrosion resistant steel according to claim 1, wherein the thickness of the continuous cast slab is 200-230 mm.
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1662668A (en) * | 2002-06-19 | 2005-08-31 | 新日本制铁株式会社 | Steel for crude oil tank and method for manufacture thereof, crude oil tank and method for protecting corrosion thereof |
| JP2005290479A (en) * | 2004-03-31 | 2005-10-20 | Jfe Steel Kk | Steel material for bottom plate of crude oil tank |
| JP2007262441A (en) * | 2006-03-27 | 2007-10-11 | Jfe Steel Kk | Steel for crude oil tank and its production method |
| JP2009120957A (en) * | 2002-06-19 | 2009-06-04 | Nippon Steel Corp | Steel for crude oil tank, production method thereof, crude oil tank and method for preventing corrosion thereof |
| 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) |
| CN111386357A (en) * | 2017-11-24 | 2020-07-07 | 杰富意钢铁株式会社 | Corrosion-resistant steel for deck and bottom plate of crude oil tanker and crude oil tanker |
| CN112941424A (en) * | 2021-02-10 | 2021-06-11 | 中国铁道科学研究院集团有限公司金属及化学研究所 | Novel corrosion-resistant steel for railway vehicle and manufacturing method thereof |
| CN113195761A (en) * | 2018-12-11 | 2021-07-30 | 日本制铁株式会社 | High-strength steel sheet having excellent formability and impact resistance, and method for producing high-strength steel sheet having excellent formability and impact resistance |
-
2022
- 2022-03-30 CN CN202210325703.6A patent/CN114686763B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1662668A (en) * | 2002-06-19 | 2005-08-31 | 新日本制铁株式会社 | Steel for crude oil tank and method for manufacture thereof, crude oil tank and method for protecting corrosion thereof |
| JP2009120957A (en) * | 2002-06-19 | 2009-06-04 | Nippon Steel Corp | Steel for crude oil tank, production method thereof, crude oil tank and method for preventing corrosion thereof |
| JP2005290479A (en) * | 2004-03-31 | 2005-10-20 | Jfe Steel Kk | Steel material for bottom plate of crude oil tank |
| JP2007262441A (en) * | 2006-03-27 | 2007-10-11 | Jfe Steel Kk | Steel for crude oil tank and its production method |
| 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) |
| CN111386357A (en) * | 2017-11-24 | 2020-07-07 | 杰富意钢铁株式会社 | Corrosion-resistant steel for deck and bottom plate of crude oil tanker and crude oil tanker |
| CN113195761A (en) * | 2018-12-11 | 2021-07-30 | 日本制铁株式会社 | High-strength steel sheet having excellent formability and impact resistance, and method for producing high-strength steel sheet having excellent formability and impact resistance |
| CN112941424A (en) * | 2021-02-10 | 2021-06-11 | 中国铁道科学研究院集团有限公司金属及化学研究所 | Novel corrosion-resistant steel for railway vehicle and manufacturing method thereof |
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