EP4474491A1 - Stahlblech und verfahren zur herstellung davon - Google Patents

Stahlblech und verfahren zur herstellung davon Download PDF

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Publication number
EP4474491A1
EP4474491A1 EP23807309.2A EP23807309A EP4474491A1 EP 4474491 A1 EP4474491 A1 EP 4474491A1 EP 23807309 A EP23807309 A EP 23807309A EP 4474491 A1 EP4474491 A1 EP 4474491A1
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Prior art keywords
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steel plate
content
steel
low
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EP23807309.2A
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English (en)
French (fr)
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EP4474491A4 (de
Inventor
Shigeki Kitsuya
Shunichi Murakami
Jumpei KUGIYA
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JFE Steel Corp
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JFE Steel Corp
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Priority claimed from PCT/JP2023/013709 external-priority patent/WO2023223694A1/ja
Publication of EP4474491A1 publication Critical patent/EP4474491A1/de
Publication of EP4474491A4 publication Critical patent/EP4474491A4/de
Pending legal-status Critical Current

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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
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    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
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    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
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    • C21D2211/00—Microstructure comprising significant phases
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Definitions

  • This disclosure relates to a steel plate, particularly to a steel plate that has high strength and excellent low-temperature toughness and is suitable for use as structural steel used in low-temperature environments, such as liquefied gas storage tanks. This disclosure also relates to a method for producing the steel plate.
  • thick steel plates used for low-temperature structures such as liquefied gas storage tanks are required to have excellent low-temperature toughness to ensure safety against embrittlement fracture at low temperatures.
  • liquefied natural gas LNG
  • LNG liquefied natural gas
  • thick steel plates used for LNG storage tanks must have excellent toughness at temperatures of -164 °C or lower.
  • thick steel plates that contain high concentrations of Ni such as 7 % and 9 % and have excellent low-temperature toughness have been conventionally used for applications such as liquefied gas storage tanks.
  • JPH04-371520A proposes a method for producing 9 % Ni steel with a thickness of 40 mm or more by sequentially applying quenching, dual-phase region quenching, and tempering treatments to a hot-rolled steel plate.
  • JPH06-184630A proposes a method for easily producing a thick 9 % Ni steel plate with excellent low-temperature toughness.
  • PTL 2 proposes a method for easily producing a thick 9 % Ni steel plate with excellent low-temperature toughness.
  • y stable retained austenite
  • WO2020/136829A1 (PTL 3), a Ni-containing steel plate with excellent toughness is proposed, in which the average coarse grain size of the prior austenite measured at a 1/4t position of the steel plate is 20 ⁇ m or less.
  • the method for producing 9 % Ni steel proposed in PTL 1 requires three-step heat treatment of hot-rolled steel plates: quenching, dual-phase region quenching, and tempering. This is disadvantageous in terms of manufacturing cost and productivity.
  • the dual-phase region quenching must be performed using a furnace set to a special temperature different from that of the normal quenching. Therefore, there is a producing restriction that other products could not be produced on the production line where the aforementioned method is applied.
  • the steel plate of this disclosure has both high strength and excellent low-temperature toughness.
  • the steel plate can be produced by performing general reheating quenching and tempering after hot rolling, other products can be produced together on the same line where the steel plate are being produced, providing excellent manufacturability.
  • the steel plate in one of the disclosed embodiments has a specific chemical composition, microstructure, thickness, tensile strength, and yield stress. The reasons for the limitations are explained below.
  • the C is an element that has the effect of strengthening the steel plate.
  • the C content should be 0.01 % or more, preferably 0.03 % or more.
  • the C content is set to 0.15 % or less, preferably 0.10 % or less, more preferably 0.08 % or less.
  • Si 0.01 % or more and 1.00 % or less
  • Si is an element that acts as a deoxidizer in the steelmaking process. Si also has the effect of strengthening the steel plate due to solid solution strengthening. To achieve the effect, the Si content should be 0.01 % or more. On the other hand, when the Si content is more than 1.00 %, the low-temperature toughness decreases due to increased inclusions and additionally, the weldability and surface characteristics deteriorate. Therefore, the C content is set to 1.00 % or less, preferably 0.5 % or less, more preferably 0.3 % or less.
  • Mn 0.10 % or more and 2.00 % or less
  • Mn is an element that has the effect of increasing the quench hardenability of the steel plate and strengthening it.
  • the Mn content should be 0.10 % or more, preferably 0.40 % or more.
  • the Mo content is set to 2.00 % or less, preferably 1.00 % or less.
  • the P content When the P content exceeds 0.010 %, low-temperature toughness decreases. This is because P segregates to grain boundaries and decreases grain boundary strength, which becomes fracture origins. Therefore, the P content should be 0.010 % or less. Meanwhile, from the viewpoint of low-temperature toughness, it is desirable to reduce P as much as possible, so no lower limit is placed on the P content and the P content may be 0 %. Excessive reduction, however, leads to higher manufacturing costs and lower productivity. Therefore, from the standpoint of industrial production, it is preferable to set the P content to 0.001 % or more.
  • S forms MnS in the steel, which significantly degrades low-temperature toughness. Therefore, it is desirable to reduce S as much as possible, and the S content should be 0.0050 % or less, preferably 0.0020 % or less. Meanwhile, since it is desirable to reduce S as much as possible from the viewpoint of low-temperature toughness, not lower limit is placed on the S content and the S content may be 0 %. However, since excessive reduction leads to higher manufacturing costs and lower productivity, it is preferable to set the S content to 0.0001 % or more from the standpoint of industrial production.
  • Ni 5.0 % or more and 10.0 % or less
  • Ni is an element that has the effect of increasing the strength of the steel plate. Ni is also an extremely effective element for improving the low-temperature toughness of the steel plate. When the Ni content is less than 5.0 %, the desired strength and low-temperature toughness cannot be obtained. Therefore, the Ni content should be 5.0 % or more, preferably 6.5 % or more, more preferably 6.8 % or more, and even more preferably 8.0 % or more. On the other hand, Ni is an expensive element, so a higher content increases the steel plate cost. Therefore, the Ni content is set to 10.0 % or less, preferably 9.5 % or less.
  • Al 0.002 % or more and 0.100 % or less
  • Al is an element that acts as a deoxidizer and is commonly used in molten steel deoxidation processes. Al also reacts with N in the steel to form AlN. This reaction reduces solute N, resulting in improved low-temperature toughness.
  • the Al content should be 0.002 % or more, preferably 0.010 % or more, more preferably 0.020 % or more.
  • the C content is set to 0.100 % or less, preferably 0.070 % or less, more preferably 0.060 % or less.
  • N forms nitrides and carbonitride, thereby decreasing low-temperature toughness.
  • the N content should be 0.0080 % or less, preferably 0.0040 % or less.
  • the steel plate in one of the disclosed embodiments has a chemical composition containing the above elements with the balance being Fe and inevitable impurities.
  • the steel plate chemical composition in another embodiment of this disclosure may optionally further contain at least one of the elements below for the purpose of further improving the properties of the steel plate.
  • Cu is an element that has the effect of further increasing the strength of the steel plate by improving hardenability.
  • the Cu content should be 0.01 % or more.
  • the Cu content is set to 1.00 % or less, preferably 0.30 % or less.
  • Cr is an effective element for further improving the strength of the steel plate.
  • the Cr content should be 0.01 % or more.
  • Cr may precipitate as precipitates such as nitrides, carbide, and carbonitrides during rolling, and the precipitates become initiation points for corrosion and fracture, decreasing low-temperature toughness. Therefore, the Cr content is set to 1.50 % or less, preferably 1.00 % or less.
  • Mo is an element that has the effect of suppressing the susceptibility of the steel plate to tempering embrittlement. Mo also has the effect of further increasing the strength of the steel plate.
  • Mo content should be 0.03 % or more, preferably more than 0.05 %.
  • the Mo content is set to 1.0 % or less, preferably 0.30 % or less.
  • Nb 0.001 % or more and 0.030 % or less
  • Nb is an element that has the effect of further increasing the strength of the steel plate.
  • the Nb content should be 0.001 % or more, preferably 0.005 % or more, more preferably 0.007 % or more.
  • the Nb content is set to 0.030 % or less, preferably 0.025 % or less, more preferably 0.022 % or less.
  • V 0.01 % or more and 0.10 % or less
  • V is an element that has the effect of further increasing the strength of the steel plate.
  • the V content should be 0.01 % or more, preferably 0.02 % or more, more preferably 0.03 % or more.
  • the V content is set to 0.10 % or less, preferably 0.09 % or less, more preferably 0.08 % or less.
  • Ti is an element that precipitates as nitrides or carbonitrides and has the effect of further refining the austenite grains in the steel plate microstructure.
  • the Ti content should be 0.003 % or more, preferably 0.005 % or more, more preferably 0.007 % or more.
  • the Ti content is set to 0.050 % or less, preferably 0.035 % or less, more preferably 0.032 % or less.
  • B is an element that has the effect of further increasing the strength of the steel plate.
  • the B content should be 0.0003 % or more.
  • the B content is set to 0.0050 % or less, preferably 0.0030 % or less.
  • Sn is an element that has the effect of improving the corrosion resistance of the steel plate and is effective even when contained in small amounts. Therefore, when Sn is added, the Sn content should be 0.01 % or more. On the other hand, an excess of Sn decreases low-temperature toughness. Therefore, the Sn content is set to 0.30 % or less, preferably 0.25 % or less.
  • Sb like Sn, is an element that has the effect of improving the corrosion resistance of the steel plate and is effective even when contained in small amounts. Therefore, when Sb is added, the Sb content should be 0.01 % or more. On the other hand, an excess of Sb decreases low-temperature toughness, and additionally increases costs. Therefore, the Sb content is set to 0.30 % or less, preferably 0.25 % or less.
  • W is an element that has the effect of improving the corrosion resistance of the steel plate and is effective even when contained in small amounts. Therefore, when W is added, the W content should be more than 0 %, preferably 0.01 % or more, more preferably 0.05 % or more. On the other hand, an excess of W decreases low-temperature toughness, and additionally increases costs. Therefore, the W content is set to 2.00 % or less, preferably 0.50 % or less.
  • Co like Sn, Sb, and W, is an element that has the effect of improving the corrosion resistance of the steel plate and is effective even when contained in small amounts. Therefore, when Co is added, the Co content should be more than 0 %, preferably 0.01 % or more, more preferably 0.05 % or more. On the other hand, an excess of Co increases costs. Therefore, the Co content is set to 2.00 % or less, preferably 1.50 % or less.
  • Ca is an effective element for morphological control of inclusions such as MnS.
  • the morphological control of inclusions means suppressing the formation of elongated sulfide inclusions and forming granular inclusions. Through this morphological control of inclusions, the low-temperature toughness can be further improved, as well as sulfide stress corrosion cracking resistance.
  • the Ca content should be 0.0005 % or more, preferably 0.0010 % or more.
  • high Ca content may increase the amount of nonmetallic inclusions and decrease low-temperature toughness. Therefore, the Ca content is set to 0.0050 % or less, preferably 0.0040 % or less.
  • Mg is an effective element for morphological control of inclusions such as MnS. Through this morphological control of inclusions, the low-temperature toughness can be further improved, as well as sulfide stress corrosion cracking resistance.
  • the Mg content should be 0.0005 % or more, preferably 0.0010 % or more.
  • high Mg content may increase the amount of nonmetallic inclusions and decrease low-temperature toughness. Therefore, the Mg content is set to 0.0100 % or less, preferably 0.0050 % or less, more preferably 0.0040 % or less.
  • Zr like Ca and Mg, is an effective element for morphological control of inclusions such as MnS. Through this morphological control of inclusions, the low-temperature toughness can be further improved, as well as sulfide stress corrosion cracking resistance.
  • the Zr content should be 0.0005 % or more, preferably 0.0010 % or more.
  • high Zr content may increase the amount of nonmetallic inclusions and decrease low-temperature toughness. Therefore, the Zr content is set to 0.0050 % or less, preferably 0.0040 % or less.
  • Ta 0.01 % or more and 0.20 % or less
  • REM rare earth metal
  • the REM content should be 0.0010 % or more, preferably 0.0020 % or more.
  • high REM content may increase the amount of nonmetallic inclusions and decrease low-temperature toughness. Therefore, the REM content is set to 0.0200 % or less.
  • the steel plate according to one of the disclosed embodiments satisfies the following conditions (1) to (3) for microstructure.
  • the content of retained austenite at the 1/4 thickness position is set to, in volume fraction, less than 3.0 %, preferably 2.8 % or less, more preferably 2.6 % or less.
  • no lower limit is placed on the volume fraction of retained austenite and the volume fraction of retained austenite may be 0 %, or 0.5 % or more.
  • the volume fraction of retained austenite can be measured by X-ray diffraction. More specifically, it can be measured by the method described in the EXAMPLES section.
  • the maximum prior austenite grain size at the 1/2 thickness position is set to 100 ⁇ m or less, preferably 80 ⁇ m or less.
  • the maximum grain size is preferably more than 20 ⁇ m, more preferably 22 ⁇ m or more, even more preferably 25 ⁇ m or more.
  • the circle equivalent diameter shall be used as the prior austenite grain size.
  • the average grain size a and average value b can be measured by optical microscopy. More specifically, they can be measured by the method described in the EXAMPLES section.
  • the aspect ratio of prior austenite grains at the 1/2 thickness position is not limited but is preferably 2.0 or less.
  • the aspect ratio is 2.0 or less, the anisotropy of mechanical properties, especially low-temperature toughness, is improved.
  • the aspect ratio of prior austenite grains can be measured by optical microscopy. More specifically, it can be measured by the method described in the EXAMPLES section.
  • the steel plate thickness should be 40 mm or less. Furthermore, when the plate thickness is 40 mm or less, the heat treatment time is shorter, which can reduce the effect of tempering embrittlement during tempering. Therefore, the restriction of Si content is small in this disclosure. On the other hand, no lower limit is placed on the plate thickness, but the plate thickness is preferably 6 mm or more.
  • the tensile strength (TS) of the steel plate according to this disclosure is set to 690 MPa or more.
  • the steel plate has a high tensile strength of 690 MPa or more, and thus it can be suitably used for applications such as LNG tanks.
  • no upper limit is placed on the tensile strength, but tensile strength may be, for example, 830 MPa or less, or 800 MPa or less.
  • the yield stress (YS) of the steel plate according to this disclosure is set to 585 MPa or more.
  • the steel plate has a high yield stress of 585 MPa or more, and thus it can be suitably used for applications such as LNG tanks.
  • no upper limit is placed on the yield stress, but yield stress may be, for example, 790 MPa or less, or 770 MPa or less.
  • the tensile strength and yield stress can be measured by tensile test in accordance with JIS Z 2204. More specifically, they can be measured by the method described in the EXAMPLES section.
  • the low-temperature toughness of the steel plate according to this disclosure preferably has an absorbed energy vE -196 at -196 °C of 100 J or more.
  • the steel plate has high low-temperature toughness of a vE -196 of 100 J or more, making it suitable for use in LNG tanks and other applications.
  • the absorbed energy vE -196 is preferably 150 J or more.
  • no upper limit is placed on the absorbed energy vE -196 , but the absorbed energy may be, for example, 400 J or less, or 350 J or less.
  • the absorbed energy vE -196 can be measured by Charpy impact test in accordance with JIS Z 2242. More specifically, it can be measured by the method described in the EXAMPLES section.
  • the following describes a method for producing a steel plate according to one of the disclosed embodiments.
  • the steel plate can be produced by sequentially applying the processes (1) to (5) below to a steel material having the chemical composition described above:
  • temperatures given in “°C” refer to the temperature at the 1/2 thickness position.
  • the temperature at the 1/2 thickness position can be determined by differential calculations or other means.
  • the steel material may be, for example, a steel slab.
  • the steel material may be produced by any method, but for example, can be produced by smelting steel having the aforementioned chemical composition by a conventional method and subjecting the smelted steel to casting.
  • the smelting can be performed by any method using a converter, an electric furnace, an induction furnace, and the like.
  • the casting is preferably performed by continuous casting from the standpoint of productivity but may be performed by ingot casting.
  • the steel material is heated to a heating temperature of 900 °C or higher and 1200 °C or lower.
  • the heating may be performed after the steel material obtained by casting or other methods has been once cooled, or the steel material obtained may be directly subjected to the heating without cooling.
  • the steel material is heated in order to dissolve the precipitates in the microstructure of the steel material.
  • the heating temperature is set to 900 °C or higher.
  • the heating temperature of the steel material is set to 1200 °C or lower, preferably 1150 °C or lower.
  • the heating time is not limited but is preferably 2 hours or more. The heating time is preferably 8 hours or less.
  • the steel material heated in the heating process is hot rolled to make a hot-rolled steel plate with a thickness of 40 mm or less.
  • Rolling finish temperature is not limited, but is preferably 700 °C or higher, which is austenite single phase region. No upper limit is placed on the rolling finish temperature, but the rolling finish temperature is preferably 950 °C or lower, more preferably 920 °C or lower.
  • the rolling reduction ratio in the hot rolling process is set to 5 or more, preferably 6 or more, more preferably 10 or more.
  • no upper limit is placed on the rolling reduction ratio, but the rolling reduction ratio is preferably 50 or less.
  • the rolling reduction ratio is defined as (thickness of steel material / thickness of hot-rolled steel plate after hot rolling).
  • the number of passes where the rolling reduction per pass is 10 % or more out of the final 5 passes of the hot rolling process is set to 2 or more.
  • the number of passes is less than 2, homogenization of austenite grains does not progress sufficiently.
  • b/a in the final steel plate becomes more than 4.0, and low-temperature toughness deteriorates.
  • the number of passes where the rolling reduction per pass is 10 % or more out of the final 5 passes of the hot rolling process is preferably 3 or more, more preferably 4 or more, even more preferably 5.
  • the cooling stop temperature in the cooling process is not particularly limited, but may be, for example, room temperature (e.g., 20 °C) or higher.
  • the cooling stop temperature is preferably 400 °C or lower.
  • the cooling is not limited and can be performed by any method, for example, air cooling or water cooling.
  • Water cooling such as spray cooling, mist cooling, or laminar cooling, may be performed to enhance required properties such as strength and low-temperature toughness.
  • spray cooling mist cooling
  • laminar cooling may be performed to enhance required properties such as strength and low-temperature toughness.
  • air cooling is preferred.
  • the cooled hot-rolled steel plate is quenched after being heated to a reheating temperature of Ac3 point or higher and 900 °C or lower. Reheating to Ac3 point or higher causes reverse transformation of the microstructure of the entire hot-rolled steel plate to austenite. As a result, the microstructure of steel plate is further refined, which improves low-temperature toughness.
  • the reheating temperature is lower than Ac3 point, the ferrite phase shall be included in the microstructure of the steel plate after heating, which makes the microstructure less uniform and decreases low-temperature toughness.
  • austenite grains grow and coarsen, resulting in a decrease in low-temperature toughness.
  • Ac3 point is calculated by the following formula (1).
  • Ac3(°C) 937.2 - 436.5C + 56Si - 19.7Mn - 16.3Cu - 26.6Ni - 4.9Cr + 38.1Mo + 124.8V + 136.3Ti - 19.1Nb + 198.4Al + 3315B where each element symbol in Formula (1) indicates a content, in mass%, of a corresponding element and is taken to be 0 when the corresponding element is not contained.
  • Quenching can be performed under any conditions without limitation, but preferably by water cooling.
  • the conditions for quenching are not limited but cooling to a cooling stop temperature of lower than 200 °C is preferred.
  • the cooling stop temperature is more preferably 100 °C or lower, even more preferably 50 °C or lower.
  • no lower limit is placed on the cooling stop temperature, but for example, the cooling stop temperature may be room temperature or higher.
  • the reheated and quenched steel plate is tempered at a tempering temperature of 500 °C or higher and 650 °C or lower.
  • the tempering temperature is lower than 500 °C, the yield stress is decreased.
  • the tempering temperature exceeds 650 °C, the strength is significantly decreased due to recrystallization of the steel plate microstructure. Therefore, the tempering temperature is set to 500 °C or higher and 650 °C or lower.
  • the method for cooling is not limited and can be performed by any method, for example, air cooling or water cooling.
  • Steel slabs as steel materials were prepared by smelting steels having the chemical compositions listed in Table 1.
  • the obtained steel slabs were sequentially subjected to heating, hot rolling, cooling, reheating quenching, and tempering under the conditions listed in Table 2 to produce steel plates.
  • the steel plates were reheated to the reheating temperatures listed in Table 2 and then cooled to a cooling stop temperature below 200 °C.
  • a test piece for X-ray diffraction was taken parallel to the plate surface so that the measurement surface was at the 1/4 thickness position of the obtained steel plate.
  • the test piece was subjected to mirror polishing and electropolishing before being subjected to X-ray diffraction.
  • the diffraction intensities of the (200) and (211) planes of ⁇ -Fe and the (200), (220), and (311) planes of ⁇ -Fe appearing in the symmetrical reflection X-ray diffraction pattern were determined, and the content of retained austenite Vy was calculated using the following formula.
  • V ⁇ 100 / I ⁇ R ⁇ / I ⁇ R ⁇ + 1
  • Vy volume fraction of retained austenite
  • I diffracted X-ray intensity
  • R theoretical intensity value per unit volume.
  • the integrated intensity after background removal was used as the diffracted X-ray intensity I. Since sufficient measurement accuracy cannot be obtained when the content of retained austenite is extremely small, when the calculated retained austenite content was 0.5 % or less, the microstructure was considered to contain virtually no retained austenite (0 %), and the volume fraction column of retained austenite (y) in Table 3 was blank (-).
  • the steel plates in all the examples and comparative examples had a microstructure composed mainly of tempered martensite and bainite. Specifically, the total area ratio of tempered martensite and bainite was 90 % or more.
  • a test piece for microstructure observation was taken so that the observation position was at 1/2 thickness position.
  • the test piece was embedded in resin so that the cross section in the rolling direction (L-direction) was the observation plane and subjected to mirror polishing.
  • Picric acid corrosion was then performed, followed by observation under an optical microscopy at 200x magnification.
  • the images of the 10 fields of view taken were analyzed to determine the maximum prior austenite grain size and the ratio b/a, an average value b in the top 5 % of prior austenite grain sizes to an average prior austenite grain size a.
  • the circle equivalent diameter was used as the prior austenite grain size.
  • the ratio obtained by dividing the major axis by the minor axis in an elliptical approximation of the prior austenite grain was calculated as aspect ratio.
  • a No. 5 test piece as described in JIS Z 2201 was taken so that the plate transverse direction (C direction) of the steel plate coincided with the tensile direction, and a tensile test was conducted in accordance with JIS Z 2204 to determine yield stress (YS) and tensile strength (TS).
  • Charpy impact test was performed to evaluate low-temperature toughness. Specifically, a test piece for Charpy impact test with a 2 mm V-notch was first taken from the steel plate so that the rolling direction (L-direction) of the steel plate was the long side. The test piece was cooled to -196 °C in liquid nitrogen, and Charpy impact test was conducted in accordance with JIS Z 2242 to measure the absorbed energy vE -196 at -196 °C. The same measurements were made on three test pieces, and the average of absorbed energy values vE -196 obtained is listed in Table 3. When the plate thickness was 12 mm or less, a sub-size test piece was used for evaluation.
  • the steel plates of this disclosure satisfied the above properties and had excellent strength (tensile strength and yield stress), low-temperature toughness, and manufacturability.
  • the steel plates of comparative examples that fell outside the scope of this disclosure were inferior in at least one of strength (tensile strength and yield stress), low-temperature toughness, or manufacturability.

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