CN116288064A - Ultrahigh-strength corrosion-resistant low Wen Haigong steel plate and manufacturing method thereof - Google Patents

Ultrahigh-strength corrosion-resistant low Wen Haigong steel plate and manufacturing method thereof Download PDF

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CN116288064A
CN116288064A CN202211610318.2A CN202211610318A CN116288064A CN 116288064 A CN116288064 A CN 116288064A CN 202211610318 A CN202211610318 A CN 202211610318A CN 116288064 A CN116288064 A CN 116288064A
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steel plate
temperature
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strength
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CN116288064B (en
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朱隆浩
王军生
韩鹏
赵坦
金耀辉
于浩男
李俊博
冯丹竹
柴铁洋
陈妍
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Angang Steel Co Ltd
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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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • 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
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/008—Martensite
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Abstract

The invention provides an ultra-high-strength corrosion-resistant low Wen Haigong steel plate and a manufacturing method thereof, wherein the steel plate comprises the following components in percentage by weight: c:0.04%-0.07%, si:0.05% -0.2%, mn:0.8% -1.1%, P is less than or equal to 0.02%, S is less than or equal to 0.01%, als:0.01% -0.05%, ni:4% -6.5%, cr:9% -15%, mo:0.9% -1.5%, cu:0.1% -0.3%, nb:0.02% -0.06%, V:0.02% -0.08%, ti:0.005% -0.01%, N:0.002% -0.005% and the balance of Fe and unavoidable impurities. The invention utilizes the key production technology of the ultra-high strength low temperature toughness marine steel plate matched with Ni, cr, mo, cu element, and can produce the ultra-high strength marine steel with large thickness and marine environment corrosion resistance. The production method of the steel plate comprises smelting, continuous casting, electroslag remelting, high-temperature heating, high-efficiency hot rolling, solid solution and low-temperature tempering. The maximum thickness of the marine steel plate can reach 50mm, the yield strength is more than or equal to 960MPa, the tensile strength is 980-1150MPa, the elongation is more than or equal to 12%, the Charpy impact energy at-80 ℃ is more than or equal to 70J, and the pitting corrosion rate is less than or equal to 0.026 g.m ‑2 ·h ‑1 After intergranular corrosion, the sample is bent 180 degrees without cracks.

Description

Ultrahigh-strength corrosion-resistant low Wen Haigong steel plate and manufacturing method thereof
Technical Field
The invention belongs to the field of steel material preparation, and particularly relates to an ultra-high-strength corrosion-resistant low Wen Haigong steel plate and a component design and a manufacturing method thereof.
Background
Besides the conventional stress, the ocean engineering platform has a severe service environment, and is influenced by various factors such as strong wind, surge, tide, ice block impact, earthquake and the like, so that the specificity of the steel for the ocean platform is determined, and the ocean engineering platform must be suitable for various sea conditions in the aspect of material selection of platform construction. Meanwhile, the steel plate is in a humid and high-salinity marine environment for a long time, and is subjected to the problems of paint film falling, corrosion and corrosion fatigue on the surface of the steel plate and the like caused by adhesion of humid air, seawater and marine organisms, so that the mechanical property of the steel plate is reduced, the service life is shortened, and the normal use of an ocean engineering platform is seriously influenced. In addition, ocean platforms are far away from the coast and cannot be regularly docked for maintenance as ships do. In order to enable the ocean engineering platform to be safely used in extremely cold complex environments such as polar regions, development of high-quality ocean engineering ultra-high strength steel with excellent comprehensive performance is urgently needed, and the ocean engineering ultra-high strength steel plate has the advantages of high strength, ultra-low temperature toughness, fatigue resistance, easiness in welding, ocean environment corrosion resistance, marine organism adhesion resistance and the like.
At present, the steel for ocean engineering can meet most of the demands of the market in the field of marine engineering, but special steel with lower ductile-brittle transition temperature and excellent comprehensive performance is still a development target of countries around the world, and the high-strength steel plate with high service safety has the advantages of high difficulty in scientific research, strict production process, high requirement on equipment and high development difficulty. The patent with publication number of CN111455269A (very high strength marine steel plate with 960MPa grade yield strength and manufacturing method thereof) proposes a marine steel plate with 50mm maximum thickness and ultra high strength, which adopts a conventional C, mn alloy system and is matched with a small amount of Ni, cr and Cu elements, so that the strength grade of 960MPa can be achieved, but the impact toughness is not high and the marine environment corrosion resistance is poor. The patent with publication number CN110865145A, namely 960MPa grade ultra-high strength steel with excellent low temperature toughness and a manufacturing method thereof, proposes a steel plate with low temperature toughness of 960MPa, adopts the design of high Cu alloy components, improves the strength of the steel plate by utilizing Cu nano precipitation, and reduces the ductile-brittle transition temperature by utilizing Ni and Mo elements, but only produces the steel plate with thinner thickness without Cr elements so as to ensure the corrosion resistance of the steel plate. The patent with publication number CN110518008A, namely a high-strength steel plate with high tensile strength and 960MPa of high-strength yield strength and a production method thereof, proposes a high-strength steel plate with high strength, wherein the content of Ni, cu, cr, mo alloy in chemical components is too low, and the low-temperature toughness cannot be ensured. C. The Mn content is too high, and the steel billet segregation problem cannot be controlled. Patent publication No. CN104328350B, "quenched and tempered steel with 960MPa grade yield strength and manufacturing method thereof", proposes an ultrahigh strength coiled plate, which has lower chemical composition, does not require low-temperature toughness and corrosion resistance, and the production process is not suitable for the production of large-scale extra-thick plates.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to prepare the 960MPa ultrahigh-strength steel plate with good corrosion resistance suitable for the field of extremely cold ocean engineering and the manufacturing method thereof, wherein the mechanical property and the high service safety performance of the steel plate can reach the service condition of ocean engineering equipment, and the low-temperature impact toughness of-80 ℃ is more than or equal to 70J.
The invention aims at realizing the following steps:
the ultra-high-strength corrosion-resistant low Wen Haigong steel plate comprises the following components in percentage by weight: c:0.04% -0.07%, si:0.05% -0.2%, mn:0.8% -1.1%, P is less than or equal to 0.02%, S is less than or equal to 0.01%, als:0.01% -0.05%, ni:4% -6.5%, cr:9% -15%, mo:0.9% -1.5%, cu:0.1% -0.3%, nb:0.02% -0.06%, V:0.02% -0.08%, ti:0.005% -0.015%, N:0.002% -0.005% and the balance of Fe and unavoidable impurities.
Further, the yield strength of the steel plate after the quenching and tempering treatment is more than or equal to 960MPa, the tensile strength is 980-1150MPa, the elongation is more than or equal to 12%, and the Charpy impact energy at-80 ℃ is more than or equal to 70J.
Further, the thickness of the steel plate is less than or equal to 50mm.
Further, the microstructure of the steel plate is martensite and retained austenite, and the retained austenite content is less than or equal to 5%.
The reason for designing the components of the invention is as follows:
1) C is used as a basic strengthening element in steel, is a main element for ensuring strength and hardness, and the too low content of C can lead to the reduction of C solid solution content and carbide content, has lower grain refinement effect and insufficient steel plate strength. The C element has great influence on the welding performance, mechanical performance and HIC resistance of the steel plate, and the three performance indexes can be obviously reduced along with the increase of the C content, so that the C content of the steel plate is 0.04-0.07% in order to obtain good low-temperature toughness and higher strength.
2) Si can improve the strength of the steel plate, meanwhile, the Si can be used as a deoxidizer to reduce the O content, the deoxidizing effect is not obvious when the Si content is lower than 0.05 percent, the structure coarsening can be caused when the Si content is higher than 0.2 percent, and the low-temperature toughness is reduced, so that the Si content is 0.05 to 0.2 percent.
3) Mn element and Fe atom have similar radius, and can be dissolved in Fe matrix in large quantity to improve the strength of the steel plate. The proper amount of Mn can improve the hardenability of the steel plate, the Mn content is lower, the Mn contributes to the strength of the steel plate, the Mn is an element for enlarging an austenite phase region, the austenite stability is improved, when the mass percentage of Mn element is more than 1.1%, the martensitic transformation tendency of the steel plate is weakened in the quenching process, the heat treatment is not facilitated, the low-temperature toughness of the thick plate core is poorer due to the segregation of Mn element, and the Mn content is 0.8% -1.1%.
4) The P, S element has no benefit on the mechanical property of the steel plate, particularly the elongation percentage, and the P is controlled to be less than or equal to 0.02 percent and the S is controlled to be less than or equal to 0.01 percent.
5) Al is a main deoxidizing element in steel, when the Al content is too low, the deoxidizing effect is poor, micro-alloy elements such as Ti and the like cannot be used for refining grains due to oxidization, and the ultra-high strength steel plate with larger thickness needs to properly improve the Als content in the steel; conversely, if the Al element is too high, large-sized inclusions are formed, and the Als content is 0.01% -0.05%.
6) The role of Ni is to improve the strength, toughness and hot workability of the steel sheet. The addition of a large amount of Ni can obtain lower ductile-brittle transition temperature, and meanwhile, the addition of Ni can improve the hot cracking tendency of Cu in steel, and the Ni has a certain corrosion resistance, and the Ni content is 4% -6.5%.
7) The Cr element can effectively improve the strength of the steel plate in the steel, and for the ultra-high strength heat treated steel with larger thickness, the hardenability of the steel plate can be improved, when the Cr content in the steel is higher than 9%, the Cr oxide can form a compact oxide film on the surface of the steel plate, so that the corrosion resistance of the steel plate in the marine environment is improved, and the toughness and the corrosion resistance of the steel can be further improved by being matched with Ni and Mo elements; however, the Cr content is too high, which reduces the impact toughness of the steel sheet, and the Cr content is 9% -15%.
8) The Mo element can improve the hardenability and tempering stability of the steel plate, and can form tiny carbide in the steel, so that the strength of the steel plate can be effectively improved, the Mo element can also be matched with Ni to play a certain corrosion-resistant role, particularly the spot corrosion phenomenon caused by Cl ions is inhibited, and the Mo content is 0.9% -1.5%.
9) The addition of Cu element can improve the strength and toughness of the steel plate, and the addition of Cu and Ni element can improve the corrosion resistance of the steel and the low-temperature toughness of the steel plate, but excessive addition can cause the phenomenon of Cu embrittlement of the steel plate. Cu content is 0.1% -0.3%.
10 Nb element forms a solid solution and plays a solid solution strengthening role. Nb significantly improves the hardenability of the steel when dissolved in austenite. Nb element can improve the tempering stability of steel. The addition of a small amount of Nb to the steel can improve the strength of the steel without affecting the toughness and plasticity of the steel. The impact toughness of the steel can be improved and the brittle transition temperature can be reduced due to the effect of grain refinement. The Nb content is 0.02% -0.06%.
11 V element can form V (C, N) particles in the matrix, and can play roles in refining and strengthening grains. The alloy acts together with Ti and N elements to obviously improve the toughness and the welding performance of the steel plate. The V content is 0.02% -0.08%.
12 Ti element is a key factor of the chemical composition of the invention, ti can generate strong precipitation strengthening effect, prevent austenite from recrystallization growth, refine crystal grains and improve the yield strength of steel. Elements such as Ti, V, N, C and the like can form fine dispersed C, N compound second phase in the quenching process, so that the growth of original austenite grains is effectively controlled, and the toughness of the steel plate is remarkably improved. The content of Ti, V and N can be reasonably designed to reduce the content of N dissolved in the matrix, improve the comprehensive performance of the steel plate, and the content of Ti is 0.005-0.015 percent
13 N element plays a role in solid solution strengthening and improving hardenability. Since the N-type compounds are precipitated on the grain boundary, the high-temperature strength of the grain boundary can be improved, and the creep strength of the steel can be increased. N combines with Ti, nb, V and other elements in steel, and has precipitation hardening effect. A large number of cracks can be generated on the surface of the steel billet with the N content being too high, and the N content is 0.002% -0.005%.
The second technical scheme of the invention is to provide a manufacturing method of the ultra-high-strength corrosion-resistant low Wen Haigong steel plate, which comprises alloying smelting, die casting or continuous casting, electroslag remelting, high-temperature heating, high-efficiency hot rolling, high-temperature solid solution and low-temperature tempering;
smelting
Refining the molten steel by a converter, an LF furnace, an RH or VD furnace, and further reducing the content of P, S and nonmetallic inclusion.
Die casting or continuous casting
And the whole casting process is protected, and the superheat degree of the ladle molten steel is 25-30 ℃. Die casting or continuous casting, and producing electroslag blanks by using die cast ingot or continuous casting blanks, wherein the off-line slow cooling time of the electroslag blanks is more than or equal to 72h.
High temperature heating
The casting blank is put into a heating furnace at the temperature of 700-900 ℃ for heat preservation for 1-2 hours, so that the temperature of the steel blank in the thickness direction is kept consistent at the low temperature stage, and the preparation is made for the uniform structure of the high temperature section. The temperature rising rate of the casting blank in the subsequent temperature rising process is controlled to be 2-7 ℃/min, so that uneven heating of the inside of the steel blank caused by over-fast heating of the steel blank is avoided. The heating temperature is 1300-1400 ℃ for 1-6 hours, and the alloy composition is higher, so that the steel is fully austenitized and homogenized at a higher heating temperature, and the abnormal growth of the microstructure in the electroslag blank is avoided.
High-efficiency hot rolling
The initial rolling temperature is 1200-1360 ℃, the average pass reduction is 10-20%, and the final rolling temperature is 1000-1250 ℃. The purpose of high-temperature hot rolling is to increase the rolling reduction rate of single pass as much as possible at the stage of low deformation resistance and improve the as-cast structure of the slab. The deformation of the core of the steel plate is increased, the grain size of the core of the steel plate is improved, and the flattening and the miniaturization of austenite grains are promoted. As ferrite is nucleated on the austenite grain boundary, the effect of grain refinement can be achieved by increasing the area of the austenite grain boundary.
Heat treatment process
The heat treatment process is the key for influencing the low-temperature toughness and corrosion resistance of the steel plate, a high-temperature solid solution and tempering process is adopted, the solid solution temperature is 900-1150 ℃ and the heat preservation time is 0.8-3.0min/mm, and the steel plate is cooled to the room temperature after solid solution. The tempering temperature is 250-470 ℃ and the temperature is kept for 2.5-4min/mm. The purpose of the solution treatment is to fully austenitize the steel plate, ensure that the austenite of the steel plate is not overheated or underheated, lead the steel plate to form a large amount of martensite and residual austenite with the volume content of less than 5 percent, fully homogenize alloy elements in the steel plate, avoid element aggregation and reduce the corrosion resistance of the steel plate. The tempering can adjust the quality of the precipitated second phase while adjusting the matrix structure, and the tempering with sufficient temperature and time can ensure that a tempering transformation product is transformed as much as possible, thereby avoiding precipitation of the brittle second phase, reducing the strength and hardness of the steel plate and improving the impact toughness and corrosion resistance.
The invention has the beneficial effects that:
1. combining Ni, cr, mo, cu, V, nb, ti, N elements with the key production technology of the ultra-high strength low-temperature toughness marine steel plate, the 960 MPa-grade ultra-high strength steel plate with the thickness less than or equal to 50mm can be produced through alloying smelting, die casting or continuous casting, electroslag remelting, high-temperature heating, high-efficiency hot rolling, high-temperature solid solution and low-temperature tempering.
2. The innovative alloy component system can ensure that the yield strength of the steel plate after the quenching and tempering treatment is more than or equal to 960MPa, the tensile strength is 980-1150MPa, the elongation is more than or equal to 12 percent, and the Charpy impact energy at minus 80 ℃ is more than or equal to 70J.
3. The key production technology of the ultra-high strength low-temperature toughness marine steel plate matched with Ni, cr, mo, cu element can be utilized to produce the ultra-high strength marine steel with large thickness and marine environment corrosion resistance, the pitting corrosion performance is measured according to an ASTM G48 method A ferric trichloride test method, and the pitting corrosion rate of the steel plate is less than or equal to 0.026 g.m -2 ·h -1 The method comprises the steps of carrying out a first treatment on the surface of the The sample was kept for 24 hours, and after the sample was bent 180 °, no crack was generated when the sample was bent 180 ° after observing the intergranular corrosion.
Drawings
FIG. 1 is a golden phase diagram of the microstructure of example 1 of the present invention.
Detailed Description
Based on the component performance requirements of the extremely-cold ocean environment on the ultra-high strength marine steel, the invention is further described by the following examples by utilizing the component design matched with Ni, cr, mo, C and microalloy elements and the key production technology of the ultra-high strength low-temperature toughness marine steel plate.
According to the component proportion of the technical scheme, the embodiment of the invention carries out alloying smelting, die casting or continuous casting, electroslag remelting, high-temperature heating, high-efficiency hot rolling, high-temperature solid solution and low-temperature tempering.
And (3) high-temperature heating: the casting blank is put into a heating furnace at the furnace temperature of 700-900 ℃ for heat preservation for 1-2 hours, the temperature rising rate of the casting blank in the subsequent temperature rising process is controlled to be 2-7 ℃/min, the heating temperature is 1300-1400 ℃, and the heat preservation is carried out for 1-6 hours.
High-efficiency hot rolling: the initial rolling temperature is 1200-1360 ℃, the average pass reduction is 10-20%, and the final rolling temperature is 1000-1250 ℃.
The heat treatment process comprises the following steps: adopting high-temperature solid solution and low-temperature tempering, wherein the solid solution temperature is 900-1150 ℃ and the heat preservation time is 0.8-3.0min/mm, and cooling the steel plate to room temperature after solid solution; the tempering temperature is 250-470 ℃ and the temperature is kept for 2.5-4min/mm.
Further, the whole-process protection casting is adopted in the die casting or continuous casting process, and the superheat degree of the ladle molten steel is 25-30 ℃.
Further, the electroslag electrode in the electroslag remelting is a die casting blank or a continuous casting blank.
Further, the off-line slow cooling time of the electroslag blank in the electroslag remelting process is more than or equal to 72 hours.
The chemical composition of the steel of the invention is shown in Table 1, the production method is shown in Table 2, the tensile and impact properties are shown in Table 3, the pitting corrosion properties are shown in Table 4, and the intergranular corrosion properties are shown in Table 5.
TABLE 1 chemical composition (wt%) in the examples of the invention
Composition of the components C Si Mn P S Als Ni Cr Mo Cu Nb V Ti N
1 0.048 0.131 1.01 0.01 0.003 0.016 4.12 9.31 0.93 0.16 0.029 0.049 0.006 0.0042
2 0.052 0.18 0.82 0.02 0.002 0.029 4.23 10.61 1.12 0.11 0.037 0.031 0.013 0.0033
3 0.049 0.2 0.88 0.017 0.006 0.012 6.43 11.92 1.31 0.28 0.052 0.038 0.014 0.0029
4 0.063 0.115 1.07 0.013 0.005 0.031 5.69 12.98 1.38 0.22 0.026 0.027 0.011 0.0042
5 0.069 0.142 1.03 0.013 0.006 0.027 4.76 10.31 1.29 0.23 0.043 0.021 0.007 0.0031
6 0.041 0.193 1.02 0.02 0.006 0.015 6.49 9.01 0.91 0.21 0.021 0.049 0.009 0.005
7 0.045 0.061 0.99 0.016 0.008 0.021 4.69 14.31 0.97 0.13 0.046 0.035 0.008 0.0044
8 0.057 0.09 0.93 0.015 0.007 0.048 5.48 9.99 1.48 0.27 0.049 0.023 0.012 0.005
9 0.066 0.08 0.84 0.016 0.01 0.029 5.19 14.49 1.07 0.29 0.059 0.051 0.015 0.0026
10 0.042 0.16 0.81 0.011 0.01 0.024 4.99 12.94 1.36 0.24 0.051 0.069 0.009 0.0041
11 0.059 0.13 0.94 0.007 0.007 0.037 6.06 9.73 1.41 0.1 0.044 0.073 0.007 0.0039
12 0.048 0.19 1.05 0.012 0.004 0.043 4.94 14.98 1.15 0.14 0.041 0.079 0.005 0.0024
13 0.051 0.102 1.09 0.017 0.003 0.041 5.23 13.47 0.93 0.19 0.023 0.045 0.011 0.0021
14 0.044 0.053 0.97 0.016 0.006 0.033 5.96 9.12 0.99 0.18 0.026 0.062 0.009 0.0046
15 0.068 0.051 0.83 0.012 0.007 0.019 4.41 10.98 1.33 0.25 0.029 0.027 0.013 0.0047
16 0.063 0.171 0.89 0.011 0.005 0.037 4.01 11.22 1.04 0.26 0.036 0.064 0.015 0.0036
17 0.046 0.198 0.91 0.019 0.008 0.049 5.81 9.54 1.09 0.12 0.032 0.058 0.014 0.0033
18 0.055 0.167 1.04 0.017 0.006 0.015 6.12 9.29 1.19 0.15 0.047 0.025 0.008 0.0046
19 0.053 0.079 1.1 0.012 0.007 0.011 6.33 13.69 1.44 0.21 0.058 0.076 0.007 0.0022
20 0.064 0.133 1.06 0.008 0.004 0.014 5.52 14.13 1.49 0.29 0.052 0.044 0.006 0.0035
Figure SMS_1
TABLE 3 mechanical properties of the steel sheet of the example of the invention
Figure SMS_2
TABLE 4 pitting corrosion Properties of the inventive example steel
Examples Area/mm 2 Weight loss/g Corrosion rate/(g.m) -2 ·h -1 )
1 1611.06 0.0005 0.01293
2 1608.34 0.0005 0.01295
3 1609.14 0.0005 0.01295
4 1607.1 0.0006 0.01556
5 1621.46 0.001 0.0257
6 1609.79 0.0006 0.01557
7 1607.18 0.0002 0.00519
8 1604.72 0.0004 0.01039
9 1598.93 0.0003 0.00782
10 1604.16 0.0005 0.01299
11 1630.03 0.0008 0.02045
12 1617.44 0.0004 0.01030
13 1623.09 0.0006 0.01540
14 1615.24 0.0006 0.01548
15 1613.3 0.0008 0.02066
16 1608.76 0.001 0.0259
17 1608.83 0.0009 0.0233
18 1614.33 0.0006 0.01549
19 1609.31 0.0007 0.01812
20 1610.47 0.0006 0.01552
Note that: pitting corrosion performance was measured according to ASTM G48 method a, method of testing for iron trichloride.
TABLE 5 intergranular corrosion Properties of the inventive example Steel
Figure SMS_3
As can be seen from the above, the yield strength of the steel plate is more than or equal to 960MPa, the tensile strength is 980-1150MPa, the elongation is more than or equal to 12%, the Charpy impact energy at-80 ℃ is more than or equal to 70J, and the maximum thickness of the produced steel plate is 50mm. The pitting corrosion performance is measured according to an ASTM G48 method A ferric trichloride test method, and the pitting corrosion rate of the steel plate is less than or equal to 0.026 g.m -2 ·h -1 The sample was kept for 24 hours; the sample is bent 180 degrees, and no crack is generated when the sample is bent 180 degrees after being observed to be corroded among crystals.
The present invention has been properly and fully described in the foregoing embodiments by way of example only, and not by way of limitation, and various changes and modifications may be made by one skilled in the art without departing from the spirit and scope of the invention, any modification, equivalent substitution, improvement, etc. should be included in the scope of the invention, and the scope of the invention is defined by the claims.

Claims (8)

1. The ultra-high-strength corrosion-resistant low Wen Haigong steel plate is characterized by comprising the following components in percentage by weight: c:0.04% -0.07%, si:0.05% -0.2%, mn:0.8% -1.1%, P is less than or equal to 0.02%, S is less than or equal to 0.01%, als:0.01% -0.05%, ni:4% -6.5%, cr:9% -15%, mo:0.9% -1.5%, cu:0.1% -0.3%, nb:0.02% -0.06%, V:0.02% -0.08%, ti:0.005% -0.015%, N:0.002% -0.005% and the balance of Fe and unavoidable impurities.
2. The ultra-high-strength corrosion-resistant low Wen Haigong steel plate according to claim 1, wherein the yield strength of the steel plate after quenching and tempering is more than or equal to 960MPa, the tensile strength is 980-1150MPa, the elongation is more than or equal to 12%, and the Charpy impact energy at-80 ℃ is more than or equal to 70J.
3. The ultra-high strength corrosion resistant low Wen Haigong steel sheet according to claim 1, wherein said steel sheet has a thickness of 50mm or less.
4. The ultra-high strength corrosion resistant low Wen Haigong steel sheet according to claim 2, wherein said steel sheet microstructure is martensite and retained austenite, said retained austenite content being 5% or less.
5. A method for manufacturing an ultra-high-strength corrosion-resistant low Wen Haigong steel sheet according to claim 1, comprising alloying smelting, die casting or continuous casting, electroslag remelting, high-temperature heating, high-efficiency hot rolling, high-temperature solid solution, low-temperature tempering, characterized in that,
high temperature heating
Placing the casting blank into a heating furnace at the furnace temperature of 700-900 ℃ for heat preservation for 1-2 hours, controlling the heating rate of the casting blank to be 2-7 ℃/min in the subsequent heating process, and keeping the heating temperature of 1300-1400 ℃ for 1-6 hours;
high-efficiency hot rolling
The initial rolling temperature is 1200-1360 ℃, the average pass reduction is 10-20%, and the final rolling temperature is 1000-1250 ℃;
heat treatment process
Adopting high-temperature solid solution and low-temperature tempering, wherein the solid solution temperature is 900-1150 ℃ and the heat preservation time is 0.8-3.0min/mm, and cooling the steel plate to room temperature after solid solution; the tempering temperature is 250-470 ℃ and the temperature is kept for 2.5-4min/mm.
6. The method for manufacturing the ultra-high-strength corrosion-resistant low Wen Haigong steel plate according to claim 5, wherein the die casting or continuous casting process is whole-process protection casting, and the superheat degree of the ladle molten steel is 25-30 ℃.
7. The method for manufacturing an ultra-high-strength corrosion-resistant low Wen Haigong steel sheet according to claim 5, wherein the electroslag electrode in the electroslag remelting is a die cast blank or a continuous cast blank.
8. The method for manufacturing the ultra-high-strength corrosion-resistant low Wen Haigong steel plate according to claim 7, wherein the off-line slow cooling time of the electroslag blank in the electroslag remelting process is more than or equal to 72 hours.
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