CN114836694B - Marine seawater corrosion fatigue resistant ultra-high strength steel and manufacturing method thereof - Google Patents

Marine seawater corrosion fatigue resistant ultra-high strength steel and manufacturing method thereof Download PDF

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CN114836694B
CN114836694B CN202210584655.2A CN202210584655A CN114836694B CN 114836694 B CN114836694 B CN 114836694B CN 202210584655 A CN202210584655 A CN 202210584655A CN 114836694 B CN114836694 B CN 114836694B
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steel
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corrosion fatigue
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CN114836694A (en
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李广龙
严玲
韩鹏
张鹏
李博雍
齐祥羽
王晓航
李黎明
肖青松
应传涛
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Angang Steel Co Ltd
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    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • B—PERFORMING OPERATIONS; TRANSPORTING
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Abstract

The marine seawater corrosion fatigue resisting ultra-high strength steel comprises the chemical components of 0.030-0.080% of C, 0.25-0.60% of Si, 0.95-1.50% of Mn, 0.030-0.050% of Nb, 0.040-0.070% of V, 0.30-0.70% of Cu, 0.0120-0.0160% of N, 0.40-0.80% of Ni, 0.010-0.030% of P, less than or equal to 0.005% of S, 0.10-0.50% of Sb, 0.30-0.45% of Sn, 0.50-1.00% of Cr, 0.15-0.40% of Mo, 0.0040-0.0060% of La, 0.015-0.035% of Als and the balance of Fe and impurities. The invention can produce the ultra-high strength steel plate with reasonable component design, high strength, good low-temperature toughness and excellent corrosion fatigue performance.

Description

Marine seawater corrosion fatigue resistant ultra-high strength steel and manufacturing method thereof
Technical Field
The invention relates to the field of metal material preparation, in particular to marine seawater corrosion fatigue resistant ultra-high strength steel and a manufacturing method thereof.
Background
Corrosion fatigue is one of the key factors in causing failure of an engineered structure, where the maximum loading stress amplitude tends to be less than the material yield limit, and there is no sign before failure. In the corrosion fatigue process, there are two basic fatigue damage modes, one is fatigue damage caused by alternating load; secondly, the corrosion damage caused by the corrosion medium is often not simply overlapped, but obvious coupling effect exists between the two, namely mutual competition is promoted. When the ship is in service in a marine environment, particularly in an ice region environment, the ship is subjected to alternating influences of low temperature, chloride ions, dry and wet circulation, wind waves, sea ice load and the like in the marine region for a long time, and the damage failure is more remarkable. In order to cope with the service environment of ice areas, the strength and low-temperature toughness of ship building materials are improved, and meanwhile, the steel has good seawater corrosion fatigue resistance.
For a long time, much attention has been paid to high strength and toughness in the design, manufacture, etc. of engineering steels, and less attention has been paid to corrosion, fatigue, and corrosion fatigue. However, as the research of iron and steel materials progresses, the performances such as corrosion, fatigue and the like are more and more concerned. The method is named as 'a high-fatigue structural steel with 345MPa yield and a manufacturing method thereof', and has the application number: 201910712227.1 discloses a high-fatigue structural steel with 345 MPa-grade yield strength, which comprises the following chemical components: 0.13 to 0.16 percent of C, 1.30 to 1.60 percent of Mn, 0.020 to 0.050 percent of Nb, 0.020 to 0.030 percent of Alt, less than or equal to 0.010 percent of Ti, less than or equal to 0.12 percent of Si, less than or equal to 0.010 percent of P, less than or equal to 0.005 percent of S, and the balance of iron and unavoidable impurities, and the obtained steel plate has good comprehensive mechanical property and better surface quality by adopting a large-pressure plus cold control process. However, the steel sheet was not evaluated for corrosion fatigue properties, and the steel sheet was evaluated for impact toughness at-20℃only, and was far from satisfactory for use. The name is "high strength hot rolled steel sheet excellent in fatigue resistance and method for producing the same", application number: 201180044623.3 discloses a high-strength hot-rolled steel sheet excellent in fatigue resistance, which comprises the following chemical components: the steel plate obtained by adopting the controlled rolling and cooling process has the strength of 780MPa or more, the fatigue strength of 580MPa or more under 200 ten thousand cycles, the corrosion fatigue performance of the steel plate is not evaluated, and the low-temperature toughness of the steel plate is not evaluated. The name is 'a thick steel plate with high crack resistance and fatigue strength and a preparation method thereof', and the application number is: 201810007814.6 discloses a high crack arrest and fatigue strength thick steel plate, which comprises the following chemical components: 0.05-0.07% of C, 0.10-0.20% of Si, 1.40-1.60% of Mn, 0.04-0.06% of Nb, 0.01-0.02% of Ti, 0.30-0.35% of Cu, 0.27-0.31% of Cr, 0.4-0.5% of Ni, 0.01-0.04% of Al, 0.06-0.11% of Mo, less than or equal to 0.020% of P, less than or equal to 0.010% of S, and the balance of iron and impurities, wherein the yield strength of the steel is not lower than 500MPa, the impact absorption energy at minus 60 ℃ is greater than 250J, the fatigue strength of 200 ten thousand times is greater than 160J, the fatigue strength is lower, the service performance of the steel plate is affected, and the corrosion fatigue performance is not evaluated. The name is TMCP type high-strength high-toughness high-fatigue-performance weather-resistant bridge steel plate and a preparation method thereof, and the application number is: 201810783890.6 discloses a high-fatigue bridge steel plate, which comprises the following chemical components: 0.05 to 0.08 percent of C, 0.12 to 0.18 percent of Si, 1.4 to 1.6 percent of Mn, 0.045 to 0.058 percent of Nb, 0.01 to 0.02 percent of Ti, 0.30 to 0.35 percent of Cu, 0.22 to 0.30 percent of Cr, 0.45 to 0.55 percent of Ni, 0.02 to 0.04 percent of Al, 0.05 to 0.12 percent of Mo, less than or equal to 0.009 percent of P, less than or equal to 0.005 percent of S, and the balance of Fe and other unavoidable impurities; the fatigue strength of the steel is not lower than 170MPa under 1000 ten thousand times, and is lower, so that the service performance of the steel plate is not facilitated. The method is named as 'corrosion fatigue resistant steel for engineering and a preparation method thereof', and has the application number: 202110068169.0 discloses an engineering corrosion fatigue resistant steel, which is prepared by carrying out element regulation and characteristic element addition, cu 0.28-0.66%, ni 0.76-1.55%, sb 0.03-0.12% and the balance of Fe and unavoidable impurities on the basis of main elements (C0.04-0.07%, si 0.20-0.26%, mn 1.45-1.60%, P less than or equal to 0.01%, S less than or equal to 0.015% and Cr 0.44-0.50%) of E690 steel, wherein the corrosion fatigue strength is improved by 52% but the low-temperature toughness of the steel is not evaluated.
In summary, the following problems are mainly involved in the production of the high-strength steel sheet for a ship at present.
1) The low-temperature toughness of the steel plate is insufficient, and the use requirement cannot be met.
2) The fatigue performance of the steel plate is low, and the service performance of the steel plate is affected.
3) The seawater corrosion fatigue resistance of the steel plate is insufficient, and the long-term service requirement of the ship cannot be met.
Disclosure of Invention
The invention provides marine ultra-high strength steel with seawater corrosion fatigue resistance and a manufacturing method thereof, and aims to produce the marine ultra-high strength steel plate with reasonable component design, high strength, good low-temperature toughness and excellent corrosion fatigue performance.
In order to achieve the above purpose, the invention is realized by adopting the following technical scheme:
the marine seawater corrosion fatigue resistant ultra-high strength steel comprises the following chemical components in percentage by weight: 0.030 to 0.080 percent of C, 0.25 to 0.60 percent of Si, 0.95 to 1.50 percent of Mn, 0.030 to 0.050 percent of Nb, 0.040 to 0.070 percent of V, 0.30 to 0.70 percent of Cu, 0.0120 to 0.0160 percent of N, 0.40 to 0.80 percent of Ni, 0.010 to 0.030 percent of P, less than or equal to 0.005 percent of S, 0.10 to 0.50 percent of Sb, 0.30 to 0.45 percent of Sn, 0.50 to 1.00 percent of Cr, 0.15 to 0.40 percent of Mo, 0.0040 to 0.0060 percent of La, 0.015 to 0.035 percent of Als, and the balance of Fe and unavoidable impurities.
The function of each chemical component in the present invention will be described in detail.
C: the basic strengthening elements in the steel are main elements for ensuring the strength and the hardness in the technical scheme of the invention; when the content is too low, the amount of carbide and the like produced is reduced, and the effect of refining grains during rolling is impaired. When the content is higher, the cementite content in the steel increases, which is detrimental to the low temperature toughness, weldability and corrosion properties of the steel sheet. Therefore, the invention comprehensively considers the factors such as cost, performance and the like, and the control C range is 0.030-0.080 percent.
Si: the essential elements for steelmaking deoxidization have strong solid solution capacity in steel, can improve the elastic limit, yield strength and fatigue strength of the steel, but have adverse effects on the low-temperature toughness and surface quality of the steel when the content is too high. The invention controls the Si range to be 0.25% -0.60%.
Mn: a substitutional solid solution is formed in the steel, and can be dissolved in a large amount in the Fe matrix. Can delay the transformation of ferrite and pearlite in steel, greatly increase the hardenability of steel, reduce the brittle transition temperature of steel and improve impact toughness, but the Mn content is too high, so that segregation is easy to form in steel, and the plasticity, toughness, fatigue and corrosion performance of steel are all adversely affected. Comprehensively considering, the invention controls the Mn range to be 0.95% -1.50%.
Nb: grain refinement elements, carbon and nitride particles of undissolved Nb are distributed on an austenite grain boundary during heating, so that the growth of austenite grains of the steel during heating can be prevented; can effectively delay the recrystallization of deformed austenite, prevent austenite grains from growing, refine ferrite grains, improve the impact toughness of steel and reduce the brittle transition temperature of steel. The invention controls the range of Nb to be 0.030% -0.050%.
V: the strong carbide forming element has small influence on austenite recrystallization, a large amount of carbon and nitride of V are precipitated at low temperature, and the precipitate and ferrite have a specific position relation, so that the strong carbide forming element has obvious precipitation strengthening and tissue refining effects, and the fatigue crack initiation and propagation resistance of the steel is improved. The V is controlled to be in the range of 0.040-0.070%.
Cu: when added in a proper amount, the steel has improved strength, low-temperature toughness and corrosion resistance, and has no adverse effect on the hardening property and toughness of a weld heat affected zone, but when the content is too high, the hot brittleness of the steel is deteriorated, and hot cracks are easily generated. The invention controls the Cu range to be 0.30% -0.70%.
N: the important strengthening and toughening elements of the invention mainly exist in two states of free state and compound state in steel, the existence of the former is unfavorable for the toughness of the steel plate, and the existence of the latter has positive effect on the comprehensive performance of the steel plate. In the case of nitrogen deficiency in steel, most of V in V-containing steel does not sufficiently exert its precipitation strengthening effect. The nitrogen-containing steel not only eliminates the cost increase caused by degassing and refining nitrogen removal in the steelmaking process, but also can fully play the role of micro-alloying elements by nitrogen increase in the steel, and saves the consumption of alloying elements, thereby greatly reducing the production cost. Meanwhile, V (C, N) is precipitated in the steel and has a specific position relation with ferrite, so that the steel has a beneficial effect on improving the fatigue performance of the steel. The invention controls the range of N to be 0.0120% -0.0160%.
Ni: the method has no adverse effect on the hardening property and toughness of a welding heat affected zone of steel, can improve the toughness of the steel, has beneficial effects on improving the fatigue strength and corrosion resistance of the steel, can reduce the hot cracking tendency when the Cu content is high by adding Ni, and comprehensively considers the factors such as cost, performance and the like, and the range of Ni is controlled to be 0.40-0.80%.
P: the Cu element and the Cu element coexist to form various compound salts, so that the grains of the inner rust layer are fine and compact, the damage of Cl < - > can be resisted, the corrosion rate of steel is reduced, but serious segregation is easy to form when the content is too high, and the low-temperature toughness and the welding performance of the steel are not good. The range of P is controlled to be 0.010-0.030 percent.
Sb: in general, the mechanical properties of the steel are adversely affected, so that the strength of the steel is reduced and the brittleness is increased, as inWhen a certain amount of antimony is added into the steel, the corrosion resistance and wear resistance of the steel can be improved to different degrees, and when the antimony is added in a compounding way with Sn, the enrichment of Sn and the uniform distribution of Sb occur in a rust layer of the steel, and SnO is formed on the surface of the steel 2 -Sb 2 O 5 The corrosion-resistant oxide film can improve the Cl-permeation resistance, thereby further improving the corrosion resistance of the steel. The invention controls the range of Sb to be 0.10-0.50%.
Sn: similar to the action of Sb, the proper addition of Sb can improve the corrosion resistance of steel, and when Sb is added in a compounding way, the corrosion resistance of steel can be further improved. The invention controls the Sn range to be 0.30% -0.45%.
Cr: the hardenability of the steel is improved, and the toughness of the steel is improved. The addition of a small amount of Cr can effectively delay the initial corrosion of the steel plate, but when the Cr content is too high, the corrosion resistance of the steel can be reduced along with the extension of the corrosion time of the acid environment. The invention controls the range of Cr to be 0.50-1.00%.
Mo: the hardenability of the steel is improved, tiny carbide is formed in the steel, the strength and fatigue strength of the steel can be effectively improved, and the corrosion resistance of the steel plate can be improved by being matched with elements such as Ni, cu and the like. The invention controls the Mo range to be 0.15% -0.40%.
La: the rare earth element is added in a small amount to improve the fluidity of the steel, has good desulfurization effect, reduces nonmetallic inclusions in the steel, ensures compact and pure steel structure, and has positive effects on improving the fatigue strength and low-temperature toughness of the steel. Meanwhile, the corrosion potential of the steel in seawater can be improved, so that the corrosion resistance of the steel is improved. The invention controls the La to be in the range of 0.0040-0.0060%.
Al: the strong deoxidizer can produce highly finely divided and ultra-microscopic oxide in steel, has the function of refining grains, and can improve the strength and fatigue strength of the steel. The invention controls the Als to be in the range of 0.015% -0.035%.
The yield strength of the steel plate is 550-620MPa, the tensile strength is more than 630MPa, the elongation after fracture is more than 20.0 percent, and the low-temperature impact absorption energy at minus 60 ℃ is more than 150J.
And (3) performing corrosion fatigue performance test on the steel plate by referring to ISO 11782-I-2017 corrosion-corrosion fatigue test part 1 cycle failure test of metals and alloys, and simulating that the corrosion fatigue strength in a seawater environment is more than or equal to 306MPa under the test condition that the stress ratio is-1 and the loading frequency is 1HZ.
The manufacturing method of the marine seawater corrosion fatigue resistant ultra-high strength steel comprises the following steps of smelting, continuous casting, heating by a heating furnace and rolling:
1) Smelting steel according to the components:
a) The content of C, si, mn, P, S and other elements is regulated to be within the range of the invention during converter smelting, and other alloy components are added according to the requirement for smelting.
b) Refining the molten steel, and adjusting the content of other alloy elements to be within the scope of the invention.
c) RH treatment is carried out on refined molten steel, the RH treatment time is more than or equal to 30min, nitrogen is blown in the whole process during RH treatment, the final N content of the steel is ensured to be 0.0120% -0.0160%, and the content of [ H ] in the steel is controlled to be less than or equal to 2.0ppm and the content of [ O ] in the steel is controlled to be less than or equal to 18ppm;
2) Continuously casting the molten steel obtained in the step 1) to obtain a required casting blank, and controlling the superheat degree of a tundish to be less than or equal to 30 ℃ in order to improve the center segregation of the casting blank; the whole process of protection pouring, and the electromagnetic stirring and the light pressing are put into the process of electromagnetic stirring: i is more than or equal to 450A.
3) In order to regulate the internal stress of the continuous casting billet, promote the precipitation of C/N compounds and prevent abnormal growth of crystal grains of the continuous casting billet, the casting billet obtained in the step 2) is stacked and slowly cooled, and the stacking time is more than or equal to 36h.
4) The casting blank is heated to 1150-1250 ℃, the steel alloy of the invention has high content and poor heat conduction performance, a sectional heating process is adopted for heating to control the heating quality of the continuous casting blank, a slow heating is adopted for heating below 700 ℃ to relieve the overlarge thermal stress caused by the poor heat conduction performance, the heating speed is 8-12 ℃/min and is higher than 700 ℃, a rapid heating process is adopted to prevent the abnormal growth of austenite grains, the heating speed is 15-20 ℃/min and the heat preservation time is 0.5-3.5 h;
5) Rolling a casting blank into a hot rolled steel plate through three stages, wherein in order to fully break austenite grains of the casting blank, a rolling process of low speed and high reduction is adopted in the first stage, the initial rolling temperature is 1050-1150 ℃, the rolling speed is 8.0-12.0r/min, the first pass reduction is more than or equal to 50mm, the casting blank is rolled to be 3.0-4.0 times the thickness of a finished product and then heated, a rolling process of recrystalization area rolling and high reduction is adopted in the second stage, the initial rolling temperature is 950-1000 ℃, the rolling speed is 14.0-16.0r/min, the pass reduction is 15-35%, the casting blank is rolled to be 1.5-2.0 times the thickness of the finished product and then heated, a high speed and low temperature high reduction process is adopted in the third stage, the grain size of the steel plate is further refined, the initial rolling temperature is 800-850 ℃, the rolling speed is 18.0-25.0r/min, and the final rolling temperature is 780-830 ℃;
6) The rolled steel plate is accelerated and cooled to prevent the grain size from growing, further maintain the refined grain, and cool at 700-730 ℃ at a cooling speed of 6-15 ℃/s and a reddening temperature of 500-550 ℃;
7) In order to release the internal stress formed in the rolling and cooling processes and further form fine precipitated phases, the steel plates are stacked and slowly cooled, the stacking temperature is 400-480 ℃, and the stacking time is more than or equal to 20 hours.
Compared with the prior art, the invention has the beneficial effects that:
1) The invention adopts low carbon and adding Cu, P, ni, cr, mo, sb, sn and other alloy elements to improve the corrosion resistance of steel, adds Si, nb, V-N and other elements to improve the fatigue performance of steel, cancels Ti and other elements which are easy to form polyhedral precipitated phases, adds rare earth elements to improve the purity of steel, and inhibits the initiation and the expansion of steel corrosion fatigue cracks through the interaction among the elements. The rolling adopts a three-stage rolling process of first-stage low-speed large-pressure, second-stage recrystallization zone rolling, large-pressure, three-stage high-speed and low-temperature large-pressure, and is matched with a subsequent rapid cooling process and stacking slow cooling, the finally obtained steel plate tissue is an ultrafine ferrite and bainite tissue, the ferrite content is 20.0-40.0%, the grain size is less than or equal to 10.0 mu m, spherical Nb and V precipitated phases are dispersed and distributed on a ferrite matrix, the size is 10-25nm, and the bainite content is 60.0-80.0%. The steel plate has good seawater corrosion fatigue resistance, the corrosion fatigue strength reaches more than 306MPa, and is 1.6 times of that of the conventional steel plate, and the corrosion fatigue ratio is more than 0.48.
2) The steel plate has excellent comprehensive mechanical performance, yield strength of 550-620MPa, tensile strength of more than 630MPa, elongation after fracture of more than 20.0 percent and low-temperature impact absorption energy of more than 150J at minus 60 ℃.
Drawings
FIG. 1 is a photograph of a typical metallographic structure of example 4.
Detailed Description
The present invention will be described in more detail by the following examples, which are merely illustrative of the best mode of the invention and do not limit the scope of the invention in any way.
Smelting is carried out according to the chemical composition range designed by the invention, the chemical composition is shown in table 1, the obtained molten steel is subjected to continuous casting, heating, rolling and cooling to obtain the steel plate, the smelting process and the heating process are shown in table 2, the rolling process is shown in table 3, and the cooling process is shown in table 4.
TABLE 1 smelting process and chemical composition (wt%) of the inventive example steel
Numbering device C Si Mn Nb V Cu N Ni P S Sb Sn Cr Mo La Als
1 0.033 0.48 1.47 0.048 0.043 0.33 0.0132 0.42 0.023 0.003 0.13 0.32 0.52 0.37 0.0042 0.018
2 0.037 0.52 1.34 0.042 0.047 0.38 0.0138 0.49 0.029 0.002 0.18 0.38 0.96 0.17 0.0059 0.033
3 0.058 0.33 1.08 0.039 0.056 0.49 0.0151 0.61 0.012 0.004 0.29 0.36 0.93 0.21 0.0048 0.029
4 0.046 0.39 1.42 0.031 0.068 0.44 0.0158 0.53 0.018 0.001 0.31 0.37 0.88 0.29 0.0054 0.021
5 0.069 0.27 1.19 0.033 0.064 0.68 0.0144 0.79 0.027 0.002 0.47 0.39 0.82 0.32 0.0056 0.022
6 0.062 0.36 1.11 0.036 0.061 0.62 0.0146 0.73 0.026 0.003 0.38 0.44 0.64 0.36 0.0053 0.026
7 0.044 0.43 1.36 0.049 0.054 0.54 0.0129 0.63 0.016 0.002 0.43 0.34 0.69 0.33 0.0047 0.016
8 0.052 0.59 1.24 0.047 0.058 0.59 0.0153 0.69 0.014 0.001 0.49 0.41 0.58 0.34 0.0046 0.019
9 0.071 0.41 0.96 0.046 0.053 0.52 0.0155 0.64 0.028 0.004 0.18 0.43 0.74 0.39 0.0052 0.032
10 0.079 0.34 1.02 0.044 0.049 0.49 0.0147 0.58 0.013 0.003 0.22 0.42 0.77 0.36 0.0051 0.028
TABLE 2 smelting and heating process for example steel of the present invention
Figure BDA0003665434740000061
Figure BDA0003665434740000071
TABLE 3 Rolling Process of example Steel according to the invention
Figure BDA0003665434740000072
TABLE 4 Cooling Process for example Steel according to the invention
Numbering device Cooling temperature/°c Cooling rate/°c/s Temperature of redback/. Degree.C Stacking temperature/°c Stacking time/h
1 719 12 536 419 27
2 714 10 521 442 32
3 712 9 546 436 29
4 726 13 512 464 36
5 703 11 509 476 28
6 712 10 526 473 35
7 724 8 518 432 24
8 728 7 531 469 22
9 716 14 522 456 33
10 711 12 533 452 34
Conventional mechanical property tests were performed on the steels of the examples of the present invention, and the results are shown in Table 5.
TABLE 5 mechanical Properties of the inventive example steels
Figure BDA0003665434740000073
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Figure BDA0003665434740000081
The corrosion fatigue performance of the steel of the embodiment and the comparative steel of the invention is tested, and the corrosion fatigue life curve is measured by adopting an axial stress control method by referring to ISO 11782-I-2017, corrosion-corrosion fatigue test of metals and alloys, part 1 cycle failure test. Stress ratio-1, loading frequency 1HZ. The corrosion solution for corrosion fatigue was prepared to simulate seawater according to ASTM D1141-98, and the pH was adjusted to 8.2 with a dilute NaOH solution. The test results are shown in Table 6.
TABLE 6 Corrosion fatigue Properties of the inventive example steels
Figure BDA0003665434740000082
Figure BDA0003665434740000091
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Claims (5)

1. The marine seawater corrosion fatigue resistant ultra-high strength steel is characterized by comprising the following chemical components in percentage by weight: 0.030 to 0.080 percent of C, 0.25 to 0.60 percent of Si, 0.95 to 1.50 percent of Mn, 0.030 to 0.050 percent of Nb, 0.040 to 0.070 percent of V, 0.30 to 0.70 percent of Cu, 0.0120 to 0.0160 percent of N, 0.40 to 0.80 percent of Ni, 0.010 to 0.030 percent of P, less than or equal to 0.005 percent of S, 0.31 to 0.50 percent of Sb, 0.32 to 0.45 percent of Sn, 0.64 to 1.00 percent of Cr, 0.32 to 0.40 percent of Mo, 0.0040 to 0.0048 percent of La, 0.015 to 0.035 percent of Als, and the balance of Fe and unavoidable impurities.
The manufacturing method of the marine seawater corrosion fatigue resistant super-high strength steel comprises the following steps:
1) RH treatment is carried out on refined molten steel, the RH treatment time is more than or equal to 30min, nitrogen is blown in the whole process during RH treatment, the final N content of the steel is ensured to be 0.0120% -0.0160%, and the content of [ H ] in the steel is controlled to be less than or equal to 2.0ppm and the content of [ O ] in the steel is controlled to be less than or equal to 18ppm;
2) Continuously casting the molten steel obtained in the step 1) to obtain a required casting blank, and controlling the superheat degree of a tundish to be less than or equal to 30 ℃;
3) Heating the casting blank to 1150-1250 ℃, wherein the heating adopts a sectional heating process, the temperature rising speed is 8-12 ℃/min below 700 ℃, the temperature rising speed is more than 700 ℃, the temperature rising speed is 15-20 ℃/min, and the heat preservation time is 0.5-3.5 h;
4) Rolling the casting blank into a hot rolled steel plate through three stages, wherein the initial rolling temperature of one stage is 1050-1150 ℃, the rolling speed of the one stage is 8.0-12.0r/min, the first pass rolling reduction is more than or equal to 50mm, the casting blank is rolled to 3.0-4.0 times of the thickness of a finished product and then is heated, the initial rolling temperature of the two stage is 950-1000 ℃, the rolling speed of the two stages is 14.0-16.0r/min, the rolling reduction rate of the pass is 15-35%, the casting blank is rolled to 1.5-2.0 times of the thickness of the finished product and then is heated, the initial rolling temperature of the three stages is 800-850 ℃, the rolling speed of the three stages is 18.0-25.0r/min, and the final rolling temperature is 780-830 ℃;
5) The rolled steel plate is cooled in an accelerated way, the cooling temperature is 700-730 ℃, the cooling speed is 6-15 ℃/s, and the reddening temperature is 500-550 ℃;
6) And (3) stacking and slowly cooling the steel plates, wherein the stacking temperature is 400-480 ℃, and the stacking time is more than or equal to 20h.
2. The marine seawater corrosion fatigue resistant ultra-high strength steel according to claim 1, wherein the yield strength of the steel plate is 550-620MPa, the tensile strength is more than 630MPa, the elongation after break is more than 20.0%, and the low-temperature impact absorption energy at-60 ℃ is more than 150J.
3. The marine seawater corrosion fatigue resistant ultra-high strength steel according to claim 1, wherein the corrosion fatigue performance test of the steel plate is carried out by referring to ISO 11782-I-2017 corrosion-corrosion fatigue test 1 st part cycle failure test of metals and alloys, and the corrosion fatigue strength in the seawater environment is simulated to be more than or equal to 306MPa under the test condition that the stress ratio is-1 and the loading frequency is 1HZ.
4. The marine seawater corrosion fatigue resistant ultra-high strength steel according to claim 1, wherein said step 2) is a full-process protective casting, and is subjected to electromagnetic stirring and light pressure, electromagnetic stirring: i is more than or equal to 450A.
5. The marine seawater corrosion fatigue resistant ultra-high strength steel according to claim 1, wherein the casting blanks obtained in the step 2) are stacked and slowly cooled, and the stacking time is more than or equal to 36h.
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