CN115323270A - Low-temperature steel plate for VLGC ship and manufacturing method thereof - Google Patents
Low-temperature steel plate for VLGC ship and manufacturing method thereof Download PDFInfo
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- CN115323270A CN115323270A CN202210902760.6A CN202210902760A CN115323270A CN 115323270 A CN115323270 A CN 115323270A CN 202210902760 A CN202210902760 A CN 202210902760A CN 115323270 A CN115323270 A CN 115323270A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—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
- B21B1/24—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 in a continuous or semi-continuous process
- B21B1/26—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 in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- 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
- C22C38/04—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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Abstract
The invention discloses a VLGC ship low-temperature steel plate and a production method thereof. Belongs to the field of ferrous metallurgy, and comprises the following main chemical components: C. si, mn, P, S, als, ti, N, bs, and the balance of Fe and unavoidable impurities; on the basis of the components of C-Mn steel, micro alloy elements such as Nb and V and precious alloys such as Mo, ni, cr and Cu are not added, and the low-cost alloy design with low Ceq and low Pcm is adopted. The content of free N in a base metal and a welding heat affected zone is reduced by strictly controlling the content of N and the ratio of Ti to N, the toughness of a matrix is improved, and meanwhile, a small amount of B is added to optimize a coarse grain zone structure, optimize the proportion of grain boundary ferrite and improve the low-temperature impact toughness of a welding joint. The steel plate provided by the invention has excellent welding performance, can be suitable for the maximum linear energy of 80kJ/cm, has excellent impact performance of a welding joint, does not increase extra alloy cost, is simple and feasible in production process, and is suitable for the construction of a large VLGC ship.
Description
Technical Field
The invention belongs to the field of ferrous metallurgy, relates to a manufacturing method of a VLGC (very-high-temperature gas chromatography) marine low-temperature steel plate, and more particularly relates to a VLGC marine low-temperature steel plate with excellent welding performance and a production method thereof.
Background
During the construction of large ships, welding is often the most costly and time consuming, even accounting for over 50% of the total ship, and the quality of the welded joint is the weakest, with quality problems associated with welding being the most common. Therefore, how to ensure the weldability of the steel plate is the most important concern in ship construction. In recent years, new techniques for improving welding efficiency, such as a steel plate for high heat input welding, a weld-free preheated steel plate, and the like, have been attracting attention.
The method has the advantages that the welding efficiency is improved, and how to improve the toughness of a welding joint is a core problem, the existing technology has low requirements on low-temperature impact, generally has an A/D grade (0-minus 20 ℃), and individually realizes an E grade (-40 ℃), but cannot meet the requirements of a VLGC, and the VLGC is designed to have a low use temperature and requires the welding joint to meet the impact of minus 51 ℃, so special consideration is needed.
In the prior art, one or more deoxidizers or specific cored wires need to be added according to a specific sequence, and the purpose of controlling the organization of a heat affected zone is achieved by controlling inclusion particles (mainly oxide particles) in steel.
Disclosure of Invention
The invention aims to: the invention aims to provide a manufacturing method of a VLGC ship low-temperature steel plate, which strictly controls the content of manufactured N and the Ti/N ratio through reasonable component design, reduces the content of free N in a base material and a welding heat affected zone, improves the toughness of a matrix, simultaneously adds a trace amount of B to optimize a coarse grain zone structure, optimizes the proportion of grain boundary ferrite and improves the low-temperature impact toughness of a welding joint.
The technical scheme is as follows: the VLGC low-temperature steel plate with excellent welding performance for the ship comprises the following components in percentage by mass: c:0.06% -0.10%, si: 0.10-0.15%, mn: 1.30-1.60%, P is less than or equal to 0.010%, S is less than or equal to 0.002%, als:0.030 to 0.060%, ti: 0.008-0.012%, N is not more than 40ppm, bs:5 ppm-12 ppm, and the balance of Fe and inevitable impurities, and the ratio of Ti to N is ensured to be more than or equal to 3.
Further, the weight percentage of each component is as follows:
c:0.06%, si:0.15%, mn:1.60%, P:0.008%, S:0.0015%, als:0.055%, ti:0.012%, N:40ppm, bs:10ppm, the balance being Fe and unavoidable impurities, ti/N =3.0.
Further, the weight percentage of each component is as follows:
c:0.08%, si:0.13%, mn:1.450%, P:0.010%, S:0.002%, als:0.040%, ti:0.008%, N:25ppm, bs:8ppm, the balance being Fe and unavoidable impurities, ti/N =3.3.
Further, the weight percentage of each component is as follows:
c:0.10%, si:0.10%, mn:1.30%, P:0.007%, S:0.0018%, als:0.060%, ti:0.010%, N:35ppm, bs:8ppm, the balance being Fe and unavoidable impurities, ti/N =3.1.
Further, the production method of the VLGC low-temperature steel plate for the ship with excellent welding performance comprises the following specific operation steps:
(1) The molten iron is subjected to desulfurization pretreatment;
(2) Smelting in a converter;
(3) LF refining and RH vacuum treatment;
(4) Continuous casting and heating of casting blank;
(5) And controlling rolling and cooling after rolling.
Further, in the step (4), the temperature for heating the casting blank is: 1050-1130 ℃.
Further, in the step (5), the controlled rolling adopts two-stage controlled rolling, including recrystallization zone rolling and non-recrystallization zone rolling,
wherein the cumulative reduction rate of rolling in the recrystallization zone is more than or equal to 50 percent, and the single-pass reduction rate of rolling in the non-recrystallization zone is more than or equal to 10 percent;
further, the final rolling temperature after rolling is controlled to be 790 +/-20 ℃ by adopting two stages; after rolling, the water cooling speed is 3 ℃/s-10 ℃/s, and the temperature of red returning is 600 +/-30 ℃; and the steel plate is subjected to accelerated cooling and then air-cooled to room temperature.
Has the beneficial effects that: compared with the prior art, the method reduces the content of free N in the base metal and the welding heat affected zone by strictly controlling the content of N and the Ti/N ratio through reasonable component design, and achieves the effect of toughening the base body. Meanwhile, a trace amount of B is added to optimize the structure of a coarse crystal region, regulate and control the proportion of crystal boundary ferrite and improve the low-temperature impact toughness of the welding joint. The invention relates to a VLGC low-temperature steel plate with excellent welding performance for a ship, which is suitable for the maximum linear energy of 80kJ/cm, the impact performance of a welding heat affected zone can reach more than 100J, and meanwhile, the alloy cost, the process cost of steelmaking and steel rolling and the like are not increased. Is particularly suitable for the low-cost manufacturing requirement of a large VLGC ship.
Drawings
FIG. 1 is a flow chart of the structure of the present invention.
Detailed Description
The invention is further described with reference to the following figures and examples.
The VLGC low-temperature steel plate with excellent welding performance for the ship comprises the following components in percentage by mass: c:0.06% -0.10%, si: 0.10-0.15%, mn: 1.30-1.60%, P is less than or equal to 0.010%, S is less than or equal to 0.002%, als:0.030 to 0.060%, ti: 0.008-0.012%, N is not more than 40ppm, bs:5ppm to 12ppm, the balance of Fe and inevitable impurities, and the Ti/N ratio is ensured to be more than or equal to 3.
Further, the weight percentage of each component is as follows:
c:0.06%, si:0.15%, mn:1.60%, P:0.008%, S:0.0015%, als:0.055%, ti:0.012%, N:40ppm, bs:10ppm, the balance being Fe and unavoidable impurities, ti/N =3.0.
Further, the weight percentage of each component is as follows:
c:0.08%, si:0.13%, mn:1.450%, P:0.010%, S:0.002%, als:0.040%, ti:0.008%, N:25ppm, bs:8ppm, the balance being Fe and unavoidable impurities, ti/N =3.3.
Further, the weight percentage of each component is as follows:
c:0.10%, si:0.10%, mn:1.30%, P:0.007%, S:0.0018%, als:0.060%, ti:0.010%, N:35ppm, bs:8ppm, the balance being Fe and unavoidable impurities, ti/N =3.1.
Further, the production process of the VLGC low-temperature steel plate with excellent welding performance for the ship comprises the following steps: the method comprises the following steps of (1) molten iron desulphurization pretreatment, (2) converter smelting, (3) LF refining and RH vacuum treatment, (4) continuous casting and casting blank heating, and (5) controlled rolling and controlled cooling after rolling.
Further, in the step (4), the temperature for heating the cast slab is: 1050-1130 ℃.
Further, in the step (5), the controlled rolling adopts two-stage controlled rolling, including recrystallization zone rolling and non-recrystallization zone rolling,
wherein the cumulative reduction rate of rolling in the recrystallization zone is more than or equal to 50 percent, and the single-pass reduction rate of rolling in the non-recrystallization zone is more than or equal to 10 percent;
further, the finishing temperature after rolling is controlled at 790 +/-20 ℃ by adopting two stages; after rolling, the water cooling speed is 3 ℃/s-10 ℃/s, and the temperature of red returning is 600 +/-30 ℃; and the steel plate is subjected to accelerated cooling and then air-cooled to room temperature.
The reasons for limiting the chemical elements of the present invention are described below:
c: the most common alloy elements in steel are the most effective solid solution strengthening and precipitation strengthening elements which are most economical, but the toughness and plasticity are damaged due to the excessively high content of C, and the content of C is strictly controlled in order to improve the welding performance of the steel;
si: the alloy is mainly used for deoxidation, is added together with Al, better eliminates oxygen in steel, simultaneously Si is a non-carbide forming element, can delay the precipitation of carbide in super-cooled austenite, has a stabilizing effect on the super-cooled austenite, and controls the content of Si when the energy of a welding line is large in order to avoid forming MA in a welding coarse crystal area;
mn: the most important solid solution strengthening elements in the steel can effectively improve the strength of the steel plate, mn can expand a gamma phase region, reduce the phase transition temperature, be conductive to refining the phase transition structure, improve the toughness, reduce the ductile-brittle transition temperature and the like;
al: deoxidizing elements in the steel are also the most important grain refining elements, and strong nitride forming elements effectively fix N in the steel to improve the low-temperature toughness of a matrix and a welding joint;
ti: the most important grain refining element in the steel, titanium has strong nitrogen fixation capacity, can inhibit the growth of grains, and improves the low-temperature toughness of parent metal and weld metal.
B: the most important trace alloy element in steel, B, is segregated in austenite grain boundary to delay ferrite phase change.
Tables 1 and 2 show the base material and weld joint properties of the VLGC marine low temperature steel sheet excellent in welding properties as described in example 1.
TABLE 1 Low temperature Steel sheet Performance for VLGC Ship with Excellent weldability
| Example 1 | Specification/mm | ReH/MPa | Rm/MPa | A/％ | Impact work at-60 ℃ J |
| Base material | 20 | 369 | 489 | 29 | 315/327/308 |
TABLE 2 welding Properties of VLGC Low temperature Steel plate for Ship with Excellent welding Properties
Example 1:
the embodiment is a VLGC low-temperature steel plate for ships with excellent welding performance, which comprises the following components in percentage by mass: c:0.06%, si:0.15%, mn:1.60%, P:0.008%, S:0.0015%, als:0.055%, ti:0.012%, N:40ppm, bs:10ppm, the balance being Fe and unavoidable impurities, ti/N =3.0.
Heating a 150mm casting blank to 1080 ℃, preserving heat for 130min, and performing two-stage controlled rolling, wherein the rolling temperature of a recrystallization zone is 1000 ℃; the pass deformation is 32mm, the thickness of the intermediate blank is 65mm, the initial rolling temperature of rolling in a non-recrystallization region is 830 ℃, the final rolling temperature is 790 ℃, the rolled steel plate is 20mm, weak cooling is adopted after rolling, the cooling speed is 8 ℃/s, the temperature of red returning is 610 ℃, and then air cooling is carried out to the room temperature.
Example 2:
the embodiment is a VLGC low-temperature steel plate with excellent welding performance for ships, which comprises the following components in percentage by mass: c:0.08%, si:0.13%, mn:1.45%, P:0.010%, S:0.002%, als:0.040%, ti:0.008%, N:25ppm, bs:8ppm, the balance being Fe and unavoidable impurities, ti/N =3.3.
Heating a 150mm casting blank to 1120 ℃, preserving heat for 120min, and performing two-stage controlled rolling, wherein the rolling temperature of a recrystallization zone is 1050 ℃; the pass deformation is 30mm, the thickness of the intermediate blank is 70mm, the initial rolling temperature of rolling in a non-recrystallization region is 864 ℃, the final rolling temperature is 800 ℃, the rolled steel plate is 16mm, weak cooling is adopted after rolling, the cooling speed is 6 ℃/s, the temperature of red returning is 620 ℃, and then air cooling is carried out to the room temperature.
Example 3:
the embodiment is a VLGC low-temperature steel plate for ships with excellent welding performance, which comprises the following components in percentage by mass: c:0.10%, si:0.10%, mn:1.30%, P:0.007%, S:0.0018%, als:0.060%, ti:0.010%, N:35ppm, bs:8ppm, the balance being Fe and unavoidable impurities, ti/N =3.1.
Heating a 150mm casting blank to 1130 ℃, preserving heat for 120min, and performing two-stage controlled rolling, wherein the rolling temperature of a recrystallization zone is 1100 ℃; the pass deformation is 35mm, the thickness of an intermediate blank is 65mm, the initial rolling temperature of rolling in a non-recrystallization region is 890 ℃, the final rolling temperature is 770 ℃, the rolled steel plate is 15mm, weak cooling is adopted after rolling, the cooling speed is 3 ℃/s, the temperature of red returning is 630 ℃, and then air cooling is carried out to the room temperature.
The above is only a preferred embodiment of the present invention, and the protection scope of the present invention is not limited to the above-mentioned embodiments, and all technical solutions belonging to the idea of the present invention belong to the protection scope of the present invention. It should be noted that modifications and embellishments within the scope of the invention may be made by those skilled in the art without departing from the principle of the invention.
Claims (8)
1. The low-temperature steel plate for the VLGC ship is characterized by comprising the following chemical components in percentage by weight: c:0.06% -0.10%, si: 0.10-0.15%, mn: 1.30-1.60%, P is less than or equal to 0.010%, S is less than or equal to 0.002%, als:0.030 to 0.060%, ti: 0.008-0.012%, N is not more than 40ppm, bs:8ppm to 12ppm, and the balance of Fe and inevitable impurities; wherein: the ratio of Ti to N is more than or equal to 3.
2. The VLGC marine low temperature steel plate as claimed in claim 1, wherein,
the chemical components of the material by weight percentage are as follows: c:0.06%, si:0.15%, mn:1.60%, P:0.008%, S:0.0015%, als:0.055%, ti:0.012%, N:40ppm, bs:10ppm, the balance being Fe and unavoidable impurities, wherein Ti/N =3.0.
3. The VLGC marine low temperature steel plate as claimed in claim 1, wherein,
the chemical components of the material by weight percentage are as follows: c:0.08%, si:0.13%, mn:1.450%, P:0.010%, S:0.002%, als:0.040%, ti:0.008%, N:25ppm, bs:8ppm, the balance being Fe and unavoidable impurities, wherein: ti/N =3.3.
4. The VLGC marine low temperature steel plate as claimed in claim 1, wherein,
the chemical components of the material by weight percentage are as follows: c:0.10%, si:0.10%, mn:1.30%, P:0.007%, S:0.0018%, als:0.060%, ti:0.010%, N:35ppm, bs:8ppm, the balance being Fe and unavoidable impurities, wherein: ti/N =3.1.
5. The manufacturing method of a VLGC marine cryogenic steel plate as set forth in claims 1-4, characterized in that it comprises the following specific operating steps:
(1) The molten iron is subjected to desulfurization pretreatment;
(2) Smelting in a converter;
(3) LF refining and RH vacuum treatment;
(4) Continuous casting and heating of casting blank;
(5) And controlling rolling and cooling after rolling.
6. The manufacturing method of a VLGC ship low temperature steel plate as set forth in claim 5, wherein in the step (4), the temperature of heating the cast slab is: 1050-1130 ℃.
7. The method for manufacturing a low-temperature steel plate for a VLGC ship as claimed in claim 5, wherein in step (5), the controlled rolling is performed in two stages including recrystallization zone rolling and non-recrystallization zone rolling, wherein the cumulative reduction rate of the recrystallization zone rolling is 50% or more, and the single-pass reduction rate of the non-recrystallization zone rolling is 10% or more.
8. The manufacturing method of a VLGC ship low temperature steel plate as claimed in claim 7, wherein the finishing rolling temperature after rolling is controlled at 790 ± 20 ℃ by adopting two stages; after rolling, the water cooling speed is 3 ℃/s-10 ℃/s, and the temperature of red returning is 600 +/-30 ℃; and the steel plate is subjected to accelerated cooling and then air-cooled to room temperature.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4880480A (en) * | 1985-01-24 | 1989-11-14 | Kabushiki Kaisha Kobe Seiko Sho | High strength hot rolled steel sheet for wheel rims |
| JP2007277681A (en) * | 2006-04-11 | 2007-10-25 | Nippon Steel Corp | Method for manufacturing high-strength steel sheet with superior toughness in welding heat-affected zone |
| CN104105810A (en) * | 2011-02-15 | 2014-10-15 | 杰富意钢铁株式会社 | High tensile steel plate having excellent low-temperature toughness in weld heat-affected zones, and method for producing same |
| CN110629111A (en) * | 2019-09-12 | 2019-12-31 | 南京钢铁股份有限公司 | Marine low-temperature steel plate with excellent fire performance and manufacturing method thereof |
-
2022
- 2022-07-29 CN CN202210902760.6A patent/CN115323270A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4880480A (en) * | 1985-01-24 | 1989-11-14 | Kabushiki Kaisha Kobe Seiko Sho | High strength hot rolled steel sheet for wheel rims |
| JP2007277681A (en) * | 2006-04-11 | 2007-10-25 | Nippon Steel Corp | Method for manufacturing high-strength steel sheet with superior toughness in welding heat-affected zone |
| CN104105810A (en) * | 2011-02-15 | 2014-10-15 | 杰富意钢铁株式会社 | High tensile steel plate having excellent low-temperature toughness in weld heat-affected zones, and method for producing same |
| CN110629111A (en) * | 2019-09-12 | 2019-12-31 | 南京钢铁股份有限公司 | Marine low-temperature steel plate with excellent fire performance and manufacturing method thereof |
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