CN112501504B - BCA 2-grade container ship crack arrest steel plate and manufacturing method thereof - Google Patents

BCA 2-grade container ship crack arrest steel plate and manufacturing method thereof Download PDF

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CN112501504B
CN112501504B CN202011267544.6A CN202011267544A CN112501504B CN 112501504 B CN112501504 B CN 112501504B CN 202011267544 A CN202011267544 A CN 202011267544A CN 112501504 B CN112501504 B CN 112501504B
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CN112501504A (en
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邱保文
赵晋斌
车马俊
李恒坤
张晓雪
伯飞虎
张淼
邓阳
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Nanjing Iron and Steel Co Ltd
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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
    • 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
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    • C21D6/00—Heat treatment 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
    • 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
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    • 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
    • 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
    • C22C38/06—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
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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
    • C22C38/18—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
    • 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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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

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Abstract

The invention discloses a BCA 2-grade crack-arresting steel plate for container ships, which relates to the technical field of steel production and comprises the following chemical components in percentage by mass: c: 0.04-0.10%, Mn: 1.60% -2.00%, Ni: 0.30% -0.60%, Nb: 0.005-0.05%, Ti: 0.005-0.02%, Al: 0.015% -0.060%, Cr: 0.01 to 0.25%, Cu: 0.10% -0.35%, Si: 0.10 to 0.40 percent of the total weight of the alloy, less than or equal to 0.010 percent of P, less than or equal to 0.004 percent of S, and the balance of Fe and other inevitable impurities. Ferrite is induced to be separated out in the crystal boundary deformation, the generation of carbide at the crystal boundary is restrained, the crack initiation probability is reduced, and the crack initiation energy is increased; coarse carbide particles among bainite strands are refined, the number of the coarse carbides is reduced, the crack propagation path length is increased, and the brittle crack propagation resistance is effectively increased, so that the crack arrest toughness is obviously improved.

Description

BCA 2-grade container ship crack arrest steel plate and manufacturing method thereof
Technical Field
The invention relates to the technical field of steel production, in particular to a BCA 2-grade crack-stopping steel plate for container ships and a manufacturing method thereof.
Background
After the thickness of the crack-arresting steel plate for the container ship is regulated to exceed 80mm by the International Ship society of Ship-Classification, the crack-arresting toughness of the crack-arresting steel plate meets BCA2 level, namely the crack-arresting toughness Kca at-10 ℃ is more than or equal to 8000N/mm1.5And take effect 1 month and 1 day in 2021.
For steel sheets of 80mm or more, it has been difficult to improve the crack arrest performance of the steel sheet by the conventional TMCP process because the compression ratio is relatively small and the rate of controlled cooling is also small.
Research has shown that there are many factors affecting the crack arrest performance of steel plates, and the grain size, volume fraction of each phase, pearlite amount, precipitated carbide amount and position, rolling texture, etc. all show different degrees of effects. Alloy design and active control are carried out according to the factors, and the cracking resistance of the steel plate can be effectively improved.
A patent publication No. JP2017-186614 discloses a thick steel sheet having a thickness of more than 70mm and excellent crack arrest performance and a method for manufacturing the same, in which a structure within 5mm is defined as a structure extending in a rolling direction, and an average aspect ratio of the structure is 1.5 or more; the average bainite grain diameter of 1/4t part of the plate thickness is below 25.0 μm, and the average bainite grain diameter of 1/2t part of the plate thickness is less than 35.0 μm; the ferrite fraction of 1/4t part of the plate thickness is 15.0-40.0%, and the ferrite fraction of 1/2t part of the plate thickness is 10.0-40.0%. Further, the total area of the structure other than ferrite and bainite in each plate thickness position is less than 5% (including 0%), and after the accelerated cooling is completed, tempering treatment at 350 to 650 ℃ is required.
The patent with the application number of '201280007816.6' discloses a manufacturing method of a thick steel plate, an evaluation method and an evaluation device for the propagation stopping performance of a long brittle crack, and adopts a two-phase zone rolling control texture technology, so that the production difficulty is high, the efficiency is obviously reduced, and the method is not suitable for commercial application. Patent application No. 201580070867.7 discloses a high-strength steel material excellent in brittle crack growth resistance and a method for manufacturing the same, in which a matrix is toughened with a high content of noble metal Ni, so that the production cost is greatly increased, and a blank having a thickness of 400mm is required, and general production conditions are not available.
The' 201910149978.7 patent discloses a low alloy cost, high crack arrest super thick steel plate and method of making the same using a three stage rolling process. The second stage has accumulated rolling reduction not less than 50%, and the third stage is in two-phase region with accumulated rolling reduction not less than 28%. The total compression ratio of the steel plate is required to be more than or equal to 3.5, and universal production conditions are not available; the production process is complex, the rolling efficiency is low, and the disadvantages of increased comprehensive cost are brought.
Disclosure of Invention
In order to solve the technical problems, the invention provides a BCA 2-grade crack arrest steel plate for container ships, which comprises the following chemical components in percentage by mass: c: 0.04-0.10%, Mn: 1.60% -2.00%, Ni: 0.30% -0.60%, Nb: 0.005-0.05%, Ti: 0.005-0.02%, Al: 0.015% -0.060%, Cr: 0.01 to 0.25%, Cu: 0.10% -0.35%, Si: 0.10 to 0.40 percent of the total weight of the alloy, less than or equal to 0.010 percent of P, less than or equal to 0.004 percent of S, and the balance of Fe and other inevitable impurities.
The technical scheme of the invention is further defined as follows:
the BCA 2-grade crack arrest steel plate for the container ship comprises the following chemical components in percentage by mass: c: 0.05-0.09%, Mn: 1.70% -2.00%, Ni: 0.35% -0.58%, Nb: 0.012% -0.045%, Ti: 0.009% -0.018%, Al: 0.020-0.050%, Cr: 0.03 to 0.22 percent, Cu: 0.12% -0.30%, Si: 0.12 to 0.35 percent of the total weight of the alloy, less than or equal to 0.008 percent of P, less than or equal to 0.002 percent of S, and the balance of Fe and other inevitable impurities.
The BCA 2-grade crack arrest steel plate for the container ship comprises the following chemical components in percentage by mass: c: 0.04%, Mn: 1.70%, Ni: 0.35%, Nb: 0.012%, Ti: 0.012%, Al: 0.020%, Cr: 0.01%, Cu: 0.30%, Si: 0.40%, P: 0.009%, S: 0.003% and the balance of Fe and other inevitable impurities.
The BCA 2-grade crack arrest steel plate for the container ship comprises the following chemical components in percentage by mass: c: 0.09%, Mn: 1.85%, Ni: 0.50%, Nb: 0.030%, Ti: 0.005%, Al: 0.030%, Cr: 0.10%, Cu: 0.20%, Si: 0.10%, P: 0.004%, S: 0.002%, and the balance of Fe and other inevitable impurities.
The BCA 2-grade crack arrest steel plate for the container ship comprises the following chemical components in percentage by mass: c: 0.07%, Mn: 2.00%, Ni: 0.58%, Nb: 0.045%, Ti: 0.020%, Al: 0.050%, Cr: 0.22%, Cu: 0.10%, Si: 0.25%, P: 0.006%, S: 0.001%, and the balance of Fe and other unavoidable impurities.
The BCA 2-grade crack arrest steel plate for the container ship has the thickness of 80-100 mm.
The invention also aims to provide a manufacturing method of the BCA 2-grade container ship crack arrest steel plate, which comprises the following steps:
s1, heating a plate blank with the thickness of 320mm at 1080-1180 ℃, descaling, and then carrying out first-stage rough rolling at 1000-1150 ℃, so as to refine the grain size d to 25-40 μm;
d＝343ε1 -0.5d0 0.4exp (-55000/RT), where d0＝100μm，ε1R is a gas constant and T is a kelvin temperature;
s2, the temperature of the blank to be heated is 1/4 DEG Ar3～Ar3+30[Ni]In the interval, the second stage finish rolling is carried out, and the total accumulated strain epsilon2Greater than 0.50, and the condition d/epsilon of deformation induced ferrite is required to be satisfied2＜60μm；
[ Ni ] is the Ni content in%;
and S3, immediately controlling cooling after finishing the second-stage finish rolling, wherein the cooling speed is more than 2 ℃/S, cooling to below 450 ℃, and performing stack cooling for more than 60 hours to obtain the steel plate.
The invention has the beneficial effects that:
(1) the invention induces ferrite precipitation in crystal boundary deformation, inhibits the generation of carbide at the crystal boundary, reduces the crack initiation probability and increases the crack initiation energy; coarse carbide particles among bainite strands are refined, the number of the coarse carbides is reduced, the length of a crack propagation path is increased, and the brittle crack propagation resistance is effectively increased, so that the crack arrest toughness is obviously improved;
(2) the component design of the invention has the following advantages:
c is the most effective strengthening alloy element, improves the hardenability and the ductile-brittle transition temperature, reduces the content of C as much as possible under the condition of ensuring the strength, and is beneficial to reducing the ductile-brittle transition temperature;
mn is the most effective element for improving the strength under the condition of low carbon, the stable supercooled austenite has strong action when the content exceeds a certain content, the transformation temperature of bainite is shifted to a low-temperature region, the bainite strand is effectively refined, and the effective grain size is reduced; the content is further improved, Mn segregation in the casting blank is aggravated, so that abnormal low-toughness tissues appear after local material phase transformation, and the fracture-stopping toughness is damaged; by utilizing the fluctuation of the components of Mn element and matching with a proper non-recrystallization temperature zone and deformation, fine ferrite is induced in a relatively Mn-poor zone, C element is transferred into the residual austenite, favorable dynamic conditions are created for refining bainite transformation, the number of coarse carbides among bainite bundles is reduced, and the carbide morphology is improved;
cr, Cu and Ni are stable undercooled austenite elements, so that the hardenability is improved, the toughening effect on a matrix is exerted, and the ductile-brittle transition temperature is effectively reduced;
p, S element as a harmful element, the lower the content, the better the content, and the more economical the content, the P content is less than 0.008% and the S content is less than 0.002%;
(3) fine deformation induced ferrite is generated at the original austenite grain boundary at the 1/6-2/5 thickness of the steel plate, so that the formation of coarse carbide at the grain boundary is effectively inhibited; deformation induced ferrite is also generated on a deformation zone formed in austenite grains, coarse grains of the prior austenite are effectively separated, and after controlled cooling, bainite surrounds the deformation induced ferrite to nucleate and grow, and carbide is difficult to generate among bainite strip bundles;
(4) compared with the conventional process, the steel plate with the thickness of 80-100 mm has the advantages that the size and the number of carbides are reduced, and the expansion resistance of brittle cracks is greatly improved;
(5) the steel plate has high strength and excellent low-temperature toughness, and realizes economic and efficient production of the container ship high crack arrest toughness and extra thick crack arrest steel plate; and casting blanks with small compression ratio can be used, and the production condition limitation is less.
Drawings
FIG. 1 is a photograph showing the microstructure of a steel sheet of the present invention at a thickness 1/4.
Detailed Description
The components of the BCA 2-grade crack-arresting steel plate for container ships provided by the embodiment are shown in Table 1, tables 2 to 4 show the manufacturing process of the steel plate of the embodiment, and Table 5 shows the performance parameters of the steel plate of the embodiment.
Table 1 chemical composition units: w.t. -%)
Serial number Thickness of plate/mm C Si Mn P S Cr Ni Cu Nb Ti Alt
Example 1 80 0.04 0.40 1.70 0.009 0.003 0.01 0.35 0.30 0.012 0.012 0.020
Example 2 90 0.09 0.10 1.85 0.004 0.002 0.10 0.50 0.20 0.030 0.005 0.030
Example 3 100 0.07 0.25 2.00 0.006 0.001 0.22 0.58 0.10 0.045 0.020 0.050
TABLE 2
Serial number Thickness of plate/mm Heating temperature/. degree.C Accumulated strain epsilon1 Grain size d/mum
Example 1 80 1180 0.74 26.52
Example 2 90 1100 0.27 33.67
Example 3 100 1080 0.41 25.45
TABLE 3
Figure BDA0002776546000000041
*Ar3＝910-273C-74Mn-56Ni-16Cr-9Mo-5Cu
TABLE 4
Serial number Cooling rate/. degree.C Temperature of re-reddening/. degree.C Cooling time per hour
Example 1 4.1 430 61
Example 2 3.5 380 72
Example 3 2.5 351 65
TABLE 5
Figure BDA0002776546000000042
Through observation and analysis of the brittle crack initiation and propagation processes of the crack arrest steel plate, the coarse carbide particles at the grain boundary are found to be main initiation points of the brittle crack initiation, and the coarse carbide particles in the bainite bundles are separated from a matrix in the propagation process to form a sharp crack and the crack initiated by the grain boundary carbide is connected to form a macrocrack. As shown in figure 1, the invention inhibits coarse carbide precipitation at grain boundaries by generating deformation induced ferrite, changes bainite nucleation positions in austenite, improves the quantity and the form of carbides among bainite strands, improves the brittle crack propagation resistance of the steel plate, and obtains the crack-stopping steel plate for the container ship of 460MPa grade meeting the BCA2 grade, wherein the maximum thickness is 100 mm. The yield strength of the steel plate is more than or equal to 460MPa, the tensile strength is 570-720 MPa, the single value of the Charpy impact energy at the central part of the plate thickness at minus 60 ℃ is more than or equal to 200J, and the Kca (-10 ℃) is more than or equal to 8000N/mm3/2。
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 utility model provides a BCA2 level container ship crack arrest steel sheet which characterized in that: the chemical components and the mass percentage are as follows: c: 0.04-0.10%, Mn: 1.60% -2.00%, Ni: 0.30% -0.60%, Nb: 0.005-0.05%, Ti: 0.005-0.02%, Al: 0.015% -0.060%, Cr: 0.01 to 0.25%, Cu: 0.10% -0.35%, Si: 0.10 to 0.40 percent of the total weight of the alloy, less than or equal to 0.010 percent of P, less than or equal to 0.004 percent of S, and the balance of Fe and other inevitable impurities;
the manufacturing method comprises the following steps:
s1, heating a plate blank with the thickness of 320mm at 1080-1180 ℃, descaling, and then carrying out first-stage rough rolling at 1000-1150 ℃, so as to refine the grain size d to 25-40 μm;
d=343ε1 -0.5d0 0.4exp (-55000/RT), where d0=100μm，ε1R is a gas constant and T is a kelvin temperature;
s2, the temperature of the blank to be heated is 1/4 DEG Ar3～Ar3+30[Ni]In the interval, the second stage finish rolling is carried out, and the total accumulated strain epsilon2Greater than 0.50, and the condition d/epsilon of deformation induced ferrite is required to be satisfied2＜60μm；
[ Ni ] is the Ni content in%;
and S3, immediately controlling cooling after finishing the second-stage finish rolling, wherein the cooling speed is more than 2 ℃/S, cooling to below 450 ℃, and performing stack cooling for more than 60 hours to obtain the steel plate.
2. The BCA 2-grade crack arrest steel plate for container ships according to claim 1, wherein: the chemical components and the mass percentage are as follows: c: 0.05-0.09%, Mn: 1.70% -2.00%, Ni: 0.35% -0.58%, Nb: 0.012% -0.045%, Ti: 0.009% -0.018%, Al: 0.020-0.050%, Cr: 0.03 to 0.22 percent, Cu: 0.12% -0.30%, Si: 0.12 to 0.35 percent of the total weight of the alloy, less than or equal to 0.008 percent of P, less than or equal to 0.002 percent of S, and the balance of Fe and other inevitable impurities.
3. The BCA 2-grade crack arrest steel plate for container ships according to claim 1, wherein: the chemical components and the mass percentage are as follows: c: 0.04%, Mn: 1.70%, Ni: 0.35%, Nb: 0.012%, Ti: 0.012%, Al: 0.020%, Cr: 0.01%, Cu: 0.30%, Si: 0.40%, P: 0.009%, S: 0.003% and the balance of Fe and other inevitable impurities.
4. The BCA 2-grade crack arrest steel plate for container ships according to claim 1, wherein: the chemical components and the mass percentage are as follows: c: 0.09%, Mn: 1.85%, Ni: 0.50%, Nb: 0.030%, Ti: 0.005%, Al: 0.030%, Cr: 0.10%, Cu: 0.20%, Si: 0.10%, P: 0.004%, S: 0.002%, and the balance of Fe and other inevitable impurities.
5. The BCA 2-grade crack arrest steel plate for container ships according to claim 1, wherein: the chemical components and the mass percentage are as follows: c: 0.07%, Mn: 2.00%, Ni: 0.58%, Nb: 0.045%, Ti: 0.020%, Al: 0.050%, Cr: 0.22%, Cu: 0.10%, Si: 0.25%, P: 0.006%, S: 0.001%, and the balance of Fe and other unavoidable impurities.
6. The BCA 2-grade crack arrest steel plate for container ships according to claim 1, wherein: the thickness of the steel plate is 80-100 mm.
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KR1020237018392A KR20230126706A (en) 2020-11-13 2021-05-25 Crack-preventing steel sheet for BCA2-class container ships and its manufacturing method
PCT/CN2021/095658 WO2022100056A1 (en) 2020-11-13 2021-05-25 Crack arrest steel plate for bca2-grade container ship and manufacturing method for crack arrest steel plate

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JP5061649B2 (en) * 2007-02-28 2012-10-31 Ｊｆｅスチール株式会社 Thick steel plate with a thickness of 50 mm or more with excellent brittle crack propagation stopping characteristics
JP5434145B2 (en) * 2009-03-04 2014-03-05 Ｊｆｅスチール株式会社 Structural high-strength thick steel plate with excellent brittle crack propagation stopping characteristics and method for producing the same
KR101908819B1 (en) * 2016-12-23 2018-10-16 주식회사 포스코 High strength steel having excellent fracture initiation resistance and fracture arrestability in low temperature, and method for manufacturing the same
CN108660389B (en) * 2017-03-29 2020-04-24 鞍钢股份有限公司 High-strength thick steel plate with excellent crack resistance and manufacturing method thereof
CN109055856A (en) * 2018-08-14 2018-12-21 南京钢铁股份有限公司 Arrest toughness steel plate and preparation method thereof
CN109576585B (en) * 2018-12-25 2021-04-09 江阴兴澄特种钢铁有限公司 EH47 crack arrest steel for large container ship and manufacturing method thereof
CN111621694B (en) * 2019-02-28 2021-05-14 宝山钢铁股份有限公司 Low-cost high-crack-resistance super-thick steel plate and manufacturing method thereof
CN111286676A (en) * 2020-03-31 2020-06-16 湖南华菱湘潭钢铁有限公司 Production method of high crack-arresting marine steel plate
CN112501504B (en) * 2020-11-13 2022-03-01 南京钢铁股份有限公司 BCA 2-grade container ship crack arrest steel plate and manufacturing method thereof

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