CN112322966A - E550-W100 ultrahigh-strength ship plate steel and manufacturing method thereof - Google Patents

E550-W100 ultrahigh-strength ship plate steel and manufacturing method thereof Download PDF

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CN112322966A
CN112322966A CN202011022559.6A CN202011022559A CN112322966A CN 112322966 A CN112322966 A CN 112322966A CN 202011022559 A CN202011022559 A CN 202011022559A CN 112322966 A CN112322966 A CN 112322966A
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steel
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赵晋斌
李恒坤
陈林恒
伯飞虎
车马俊
张晓雪
邱保文
黄建华
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Nanjing Iron and 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • B21B1/22—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 plates, strips, bands or sheets of indefinite length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
    • 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
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • B21B1/22—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 plates, strips, bands or sheets of indefinite length
    • B21B2001/225—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 plates, strips, bands or sheets of indefinite length by hot-rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B2261/00—Product parameters
    • B21B2261/20—Temperature
    • 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
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention discloses an E550-W100 ultrahigh-strength ship plate steel which comprises the following chemical components in percentage by mass: c: 0.04-0.12%, Si: 0.15-0.35%, Mn: 1.50-1.70%, P is less than or equal to 0.020%, S is less than or equal to 0.0030%, V: 0.030 to 0.060%, Nb: 0.010% -0.030%, Alt: 0.030-0.080%, Ti: 0.005-0.030%, Ca: 0.0005 to 0.0040 percent, N is less than or equal to 0.0060 percent, and (alt.N)/Ti is controlled to be 0.010 to 0.030 percent. The yield strength is more than or equal to 550MPa, the tensile strength is more than or equal to 670MPa, the welding line energy is suitable for high-strength ship plate steel within the range of 100kJ/cm, and the HAZ of the steel plate is more than 55J at the temperature of minus 40 ℃.

Description

E550-W100 ultrahigh-strength ship plate steel and manufacturing method thereof
Technical Field
The invention relates to the technical field of steel production, in particular to E550-W100 ultrahigh-strength ship plate steel and a manufacturing method thereof.
Background
The steel for high heat input welding is widely used, for example, in the shipbuilding industry, the shipbuilding efficiency of the common ship plate is only one fourth of that of the ship plate for high heat input welding. When the product cannot be produced at home, the product can only be imported from foreign countries, but the price is expensive. The high heat input welding method is the most practical way to improve the welding construction efficiency and reduce the cost, and the high heat input welding steel is one of the targets of the key development of the steel industry in China, and has wide market prospect.
When the welding heat input is more than 50kJ/cm, the steel plate is subjected to high heat input welding, the mechanical property of a welding joint can be seriously reduced due to excessive coarsening of a welding heat affected zone tissue of a traditional steel plate under the condition that the welding heat input is more than 50kJ/cm, even the mechanical property is lower than the standard requirement of a base metal steel plate, and research and development of steel for meeting the high heat input welding are effective ways for solving the problem of low-temperature toughness deterioration of a high heat input welding heat affected zone.
Disclosure of Invention
In order to solve the technical problems, the invention provides an E550-W100 ultrahigh-strength ship plate steel which comprises the following chemical components in percentage by mass: c: 0.04-0.12%, Si: 0.15-0.35%, Mn: 1.50-1.70%, P is less than or equal to 0.020%, S is less than or equal to 0.0030%, V: 0.030 to 0.060%, Nb: 0.010% -0.030%, Alt: 0.030-0.080%, Ti: 0.005-0.030%, Ca: 0.0005 to 0.0040 percent of the total weight of the alloy, less than or equal to 0.0060 percent of N, and the balance of Fe and inevitable impurities, (Alt.N)/Ti is controlled to be 0.010 to 0.030 percent.
The technical effects are as follows: the invention designs the economical steel for high heat input welding with high strength, high toughness and excellent weldability according to the characteristics of elements. The basic idea of the component design of the steel is to add manganese and Ti, Al, Nb and V composite micro-alloying element content to improve the strength, control the content of impurity elements such as phosphorus, sulfur and the like, effectively refine crystal grains and improve the toughness; by adopting a composite deoxidation method and controlling the value of (Alt.N)/Ti, fine and dispersed micro inclusions are formed, the growth of austenite is inhibited and the transformation of the structure is controlled in the welding process, so that the toughness of a coarse crystal area of the steel for large heat input welding is kept at a better level. The production cycle is short, the production rhythm is fast, and the economic significance is great.
The technical scheme of the invention is further defined as follows:
the E550-W100 ultrahigh-strength ship plate steel comprises the following chemical components in percentage by mass: c: 0.08%, Si: 0.24%, Mn: 1.60%, P: 0.007%, S: 0.0008%, V: 0.055%, Nb: 0.023%, Alt: 0.065%, Ti: 0.020%, Ca: 0.0016%, N: 0.0049 percent, and the balance of Fe and inevitable impurities, (Alt.N)/Ti is controlled to be 0.016.
The E550-W100 ultrahigh-strength ship plate steel comprises the following chemical components in percentage by mass: c: 0.10%, Si: 0.20%, Mn: 1.50%, P: 0.011%, S: 0.0013%, V: 0.035%, Nb: 0.012%, Alt: 0.050%, Ti: 0.012%, Ca: 0.0008%, N: 0.0031%, and the balance of Fe and inevitable impurities, (Alt. N)/Ti, was controlled to 0.013.
The E550-W100 ultrahigh-strength ship plate steel comprises the following chemical components in percentage by mass: c: 0.06%, Si: 0.25%, Mn: 1.70%, P: 0.012%, S: 0.0015%, V: 0.045%, Nb: 0.033%, Alt: 0.072%, Ti: 0.015%, Ca: 0.0024%, N: 0.0056%, and the balance of Fe and inevitable impurities, (Alt. N)/Ti, controlled to 0.027.
The thickness of the E550-W100 ultrahigh-strength ship plate steel is 50mm, and the E550-W100 ultrahigh-strength ship plate steel is suitable for welding high-strength ship plate steel with the linear energy within the range of 100 kJ/cm.
Another object of the present invention is to provide a method for manufacturing an E550-W100 ultrahigh-strength ship plate steel, comprising the steps of: molten iron desulfurization pretreatment → converter smelting → LF refining → RH refining → continuous casting → inspection of casting blank, judgment → acceptance of casting blank → heating of continuous casting blank → descaling → rolling → cooling → flaw detection → cutting, sampling → spray printing mark → warehousing,
wherein the sulfur content after the molten iron desulphurization pretreatment is controlled to be less than or equal to 0.005 percent, the P content during converter smelting is controlled to be less than or equal to 0.013 percent, and the inclusion control and alloy component adjustment are carried out during LF refining and are strictly added according to the sequence of Ti iron-Al blocks-Ca lines-Al lines; the RH refining vacuumizing treatment is carried out for more than or equal to 10 minutes under the condition that the high vacuum degree is less than or equal to 5.0mbar, the temperature of a continuous casting tundish is controlled to be 5-30 ℃ of a liquidus line, and the continuous casting billet is stacked and slowly cooled for more than 48 hours;
the heating temperature of the continuous casting billet is 1100-1200 ℃, the rolling adopts two-stage rolling of an austenite recrystallization region and a non-recrystallization region, the rough rolling adopts pass large reduction to break austenite grains, the pass reduction is more than or equal to 30mm, the rough rolling starting temperature is more than or equal to 1050 ℃, the rough rolling is carried out to obtain an intermediate billet with the thickness of more than or equal to 2.0 times of the finished product thickness, the rough rolling finishing temperature is controlled to be 900-1050 ℃, the finish rolling starting temperature is 780-880 ℃, and the reduction rate of each pass is 10-15%; and (4) after rolling, controlling cooling, adopting laminar cooling, and then air cooling, wherein the temperature of red return is 350-450 ℃.
The invention has the beneficial effects that:
(1) the steel of the invention has the advantages of chemical composition design:
carbon is the most important element in steel and is one of the cheapest elements, carbon is a strong-gap solid solution element, and the addition of carbon in steel can have a remarkable gap solid solution strengthening effect on the steel, so that the strength of the low-alloy high-strength steel is improved, and the contribution to the strength of the steel is maximum; the carbon is combined with micro alloy elements (Nb, Ti, V and the like) in the steel to form carbide, particularly fine and dispersed carbide inclusions are formed in austenite, the effects of grain refinement and precipitation strengthening are achieved, and the hardness and the strength of the steel are improved; as the carbon content of the steel increases, yield and tensile strength increase, but plasticity and impact toughness decrease and weldability thereof deteriorates; the low-alloy high-strength steel is designed by low carbon, so that strength loss is inevitably caused, reasonable microalloying treatment is required to ensure that the high-strength steel for high heat input welding still has high strength on the premise of low carbon, and the strength is improved by adding microalloying elements; manganese is a weak carbide-forming element, increasing the hardness and strength of ferrite and austenite in steel, and generally increasing the manganese content makes up for part of the strength loss caused by reducing the carbon content; manganese can obviously reduce the transformation temperature, strongly reduce the starting transformation temperature of grain boundary ferrite and promote the formation of acicular ferrite;
silicon can be dissolved in ferrite and austenite so as to improve the hardness and strength of steel and make up for partial strength loss caused by reducing the carbon content; silicon has good deoxidation effect in molten steel and is a good deoxidizer; when aluminum is used for deoxidation, a certain amount of silicon is added, so that the deoxidation capability of the aluminum can be obviously improved; however, the high energy of the silicon content promotes the nucleation of the grain boundary-imitating ferrite, inhibits the formation of needle-shaped ferrite, increases the content of M-A components, reduces the plasticity and toughness of the steel and reduces the welding performance of the steel; therefore, the steel for high heat input welding should have low silicification to promote the formation of fine bainite and ferrite structures;
aluminum is used as a strong oxidant, has high stability, and can generate fine oxides to be dispersed in steel; meanwhile, aluminum is a strong nitrogen fixing agent, so that a nano-scale aluminum nitride precipitate is formed, the thermal stability of the steel is improved, and austenite grains of the steel are inhibited from coarsening in the reheating process; but the pinning effect of the aluminum nitride on the austenite grain boundary is only limited to 1100 ℃; during austenite decomposition, the aluminum composite inclusion can effectively induce acicular ferrite nucleation, refine crystal grains and improve toughness; the proper amount of aluminum is added into steel, the number of M-A islands in a heat affected zone is reduced, the average length of the M-A islands is reduced, and the number of retained austenite in the M-A islands is increased, so that the toughness of the heat affected zone is improved;
niobium is a typical precipitation strengthening element and has strong affinity with carbon and nitrogen; at normal temperature, most niobium in the steel exists in the forms of carbide, nitride and carbonitride; a proper amount of niobium element can form fine and dispersed second-phase particles, and has good fine-grain strengthening and precipitation strengthening effects in the rolling process; the fine second phase particles can also pin austenite grains in the welding process and inhibit the coarsening of the grains; part of niobium can be dissolved in an austenite matrix in a solid mode and segregated at an austenite grain boundary, the growth of grains is limited by inhibiting the movement of the austenite grain boundary through a solute dragging effect, the grains are refined, and the strength and the toughness are improved;
vanadium, carbon, nitrogen and other elements have strong affinity, mainly exist in the form of carbide and nitride in steel, and can improve the strength by precipitation strengthening; VN precipitated in austenite can inhibit austenite grain growth; VN precipitated in a ferrite area can increase nucleation cores of ferrite in the crystal, grain refinement is promoted on the two aspects, and the welding performance of the low-carbon low-alloy steel is obviously improved;
titanium, oxygen, nitrogen and carbon have strong affinity, and are good deoxidizers and effective elements for fixing nitrogen and carbon; titanium oxide is considered to be the most effective nucleation inclusion in steel, and can effectively promote acicular ferrite nucleation;
sulfur is a harmful element in steel, exists in a FeS form with a lower melting point, and is easy to cause the steel to generate hot brittleness, so that cracks are generated, S in the steel is easy to combine with Mn to form MnS-doped lamellar segregation, the strength and plasticity in the plate thickness direction are greatly reduced, lamellar tearing is generated, and the performance of the steel is damaged; meanwhile, under specific conditions, MnS in the steel, VN and TiN together pin austenite grain growth and induce intragranular ferrite nucleation, thereby effectively refining grains and improving toughness;
phosphorus is an impurity element, and the biggest harm is serious segregation, so that the plasticity and toughness of steel are obviously reduced, and the weldability is also adversely affected;
(2) according to the invention, through a smelting process based on a composite deoxidation technology, oxide particles which are thinned, dispersed and compounded are formed in steel, fine dispersed inclusion particles which are stable under high temperature and heat are utilized to pin austenite crystal boundaries of a welding heat affected zone under a high heat input condition, austenite crystal particles are thinned, and meanwhile, the oxides are utilized as nucleation points of acicular ferrite IAF in crystal, so that an IAF structure with better toughness is formed in the welding heat affected zone, and further the toughness of the large linear energy welding heat affected zone is improved;
(3) the invention adopts TMCP technology combined with high temperature, low speed and high pressure rolling to produce high strength ship plate steel without heat treatment, thereby reducing cost and having stable production process.
Detailed Description
The thickness of each of the E550-W100 ultrahigh-strength ship plate steel and the manufacturing method thereof are 50mm, the chemical components are shown in Table 1, the rolling cooling process parameters are shown in Table 2, and the product performance is shown in Table 3:
TABLE 1 main chemical composition (wt%) of the examples
Figure BDA0002701127520000041
TABLE 2 Rolling Cooling Process parameters for the examples
Examples Thickness mm The temperature of the rough rolling and the final rolling is lower The start rolling temperature of finish rolling is DEG C Temperature of red return
1 50 1070 826 400
2 50 1053 818 350
3 50 1078 837 450
TABLE 3 Properties of the examples
Figure BDA0002701127520000042
Therefore, the steel plate obtained by the invention has good comprehensive mechanical properties, the yield strength is more than or equal to 550MPa, the tensile strength is more than or equal to 670MPa, the steel plate is suitable for high-strength ship plate steel with the welding line energy within the range of 100kJ/cm, and the HAZ of the steel plate has the average impact energy of more than 55J at the temperature of minus 40 ℃.
In addition to the above embodiments, the present invention may have other embodiments. All technical solutions formed by adopting equivalent substitutions or equivalent transformations fall within the protection scope of the claims of the present invention.

Claims (6)

1. The E550-W100 ultrahigh-strength ship plate steel is characterized in that: the chemical components and the mass percentage are as follows: c: 0.04-0.12%, Si: 0.15-0.35%, Mn: 1.50-1.70%, P is less than or equal to 0.020%, S is less than or equal to 0.0030%, V: 0.030 to 0.060%, Nb: 0.010% -0.030%, Alt: 0.030-0.080%, Ti: 0.005-0.030%, Ca: 0.0005 to 0.0040 percent of the total weight of the alloy, less than or equal to 0.0060 percent of N, and the balance of Fe and inevitable impurities, (Alt.N)/Ti is controlled to be 0.010 to 0.030 percent.
2. The E550-W100 ultrahigh-strength ship plate steel as claimed in claim 1, wherein: the chemical components and the mass percentage are as follows: c: 0.08%, Si: 0.24%, Mn: 1.60%, P: 0.007%, S: 0.0008%, V: 0.055%, Nb: 0.023%, Alt: 0.065%, Ti: 0.020%, Ca: 0.0016%, N: 0.0049 percent, and the balance of Fe and inevitable impurities, (Alt.N)/Ti is controlled to be 0.016.
3. The E550-W100 ultrahigh-strength ship plate steel as claimed in claim 1, wherein: the chemical components and the mass percentage are as follows: c: 0.10%, Si: 0.20%, Mn: 1.50%, P: 0.011%, S: 0.0013%, V: 0.035%, Nb: 0.012%, Alt: 0.050%, Ti: 0.012%, Ca: 0.0008%, N: 0.0031%, and the balance of Fe and inevitable impurities, (Alt. N)/Ti, was controlled to 0.013.
4. The E550-W100 ultrahigh-strength ship plate steel as claimed in claim 1, wherein: the chemical components and the mass percentage are as follows: c: 0.06%, Si: 0.25%, Mn: 1.70%, P: 0.012%, S: 0.0015%, V: 0.045%, Nb: 0.033%, Alt: 0.072%, Ti: 0.015%, Ca: 0.0024%, N: 0.0056%, and the balance of Fe and inevitable impurities, (Alt. N)/Ti, controlled to 0.027.
5. The E550-W100 ultrahigh-strength ship plate steel as claimed in claim 1, wherein: the thickness of the steel plate is 50mm, and the high-strength ship plate steel with the welding line energy in the range of 100kJ/cm is suitable.
6. A manufacturing method of E550-W100 ultrahigh-strength ship plate steel is characterized by comprising the following steps: the method according to any one of claims 1 to 5, comprising the following steps: molten iron desulfurization pretreatment → converter smelting → LF refining → RH refining → continuous casting → inspection of casting blank, judgment → acceptance of casting blank → heating of continuous casting blank → descaling → rolling → cooling → flaw detection → cutting, sampling → spray printing mark → warehousing,
wherein the sulfur content after the molten iron desulphurization pretreatment is controlled to be less than or equal to 0.005 percent, the P content during converter smelting is controlled to be less than or equal to 0.013 percent, and the inclusion control and alloy component adjustment are carried out during LF refining and are strictly added according to the sequence of Ti iron-Al blocks-Ca lines-Al lines; the RH refining vacuumizing treatment is carried out for more than or equal to 10 minutes under the condition that the high vacuum degree is less than or equal to 5.0mbar, the temperature of a continuous casting tundish is controlled to be 5-30 ℃ of a liquidus line, and the continuous casting billet is stacked and slowly cooled for more than 48 hours;
the heating temperature of the continuous casting billet is 1100-1200 ℃, the rolling adopts two-stage rolling of an austenite recrystallization region and a non-recrystallization region, the rough rolling adopts pass large reduction to break austenite grains, the pass reduction is more than or equal to 30mm, the rough rolling starting temperature is more than or equal to 1050 ℃, the rough rolling is carried out to obtain an intermediate billet with the thickness of more than or equal to 2.0 times of the finished product thickness, the rough rolling finishing temperature is controlled to be 900-1050 ℃, the finish rolling starting temperature is 780-880 ℃, and the reduction rate of each pass is 10-15%; and (4) after rolling, controlling cooling, adopting laminar cooling, and then air cooling, wherein the temperature of red return is 350-450 ℃.
CN202011022559.6A 2020-09-25 2020-09-25 E550-W100 ultrahigh-strength ship plate steel and manufacturing method thereof Pending CN112322966A (en)

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JP2010095781A (en) * 2008-10-20 2010-04-30 Kobe Steel Ltd Thick steel plate excellent in toughness at basic material and weld heat-affected zone
CN102021477A (en) * 2009-09-23 2011-04-20 鞍钢股份有限公司 Hull structural steel adapting to high heat input welding and smelting method thereof
CN102102162A (en) * 2009-12-22 2011-06-22 鞍钢股份有限公司 Steel plate with low M-A content in high heat input welding heat affected zone
CN106756543A (en) * 2016-12-12 2017-05-31 南京钢铁股份有限公司 A kind of TMCP states low cost Large Heat Input Welding strength ship plate steel high and its manufacture method
JP2020033585A (en) * 2018-08-28 2020-03-05 日本製鉄株式会社 steel sheet

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* Cited by examiner, † Cited by third party
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JP2009114529A (en) * 2007-11-08 2009-05-28 Kobe Steel Ltd METHOD FOR MANUFACTURING 550 MPa CLASS LOW YIELD RATIO STEEL SHEET HAVING SMALL DISPERSION OF QUALITY IN STEEL SHEET
JP2010095781A (en) * 2008-10-20 2010-04-30 Kobe Steel Ltd Thick steel plate excellent in toughness at basic material and weld heat-affected zone
CN102021477A (en) * 2009-09-23 2011-04-20 鞍钢股份有限公司 Hull structural steel adapting to high heat input welding and smelting method thereof
CN102102162A (en) * 2009-12-22 2011-06-22 鞍钢股份有限公司 Steel plate with low M-A content in high heat input welding heat affected zone
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