EP0524335B1 - TÔles en acier au nickel, destinées aux utilisations à basse température et présentant une excellente tenacité des cordons de soudure - Google Patents

TÔles en acier au nickel, destinées aux utilisations à basse température et présentant une excellente tenacité des cordons de soudure Download PDF

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EP0524335B1
EP0524335B1 EP91112442A EP91112442A EP0524335B1 EP 0524335 B1 EP0524335 B1 EP 0524335B1 EP 91112442 A EP91112442 A EP 91112442A EP 91112442 A EP91112442 A EP 91112442A EP 0524335 B1 EP0524335 B1 EP 0524335B1
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toughness
steel plate
content
low
temperature service
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EP0524335A1 (fr
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Takahiro c/o Technical Research Div. Kubo
Yoshifumi c/o Technical Research Div. Nakano
Chiaki c/o Technical Research Div. Shiga
Osamu c/o Mizushima Works Tanigawa
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JFE Steel Corp
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Kawasaki Steel Corp
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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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C21D6/001—Heat treatment of ferrous alloys containing Ni

Definitions

  • the present invention relates to low-temperature service nickel steel plates, each with excellent weld toughness, and particularly to such steel plates for use in fabricating the bases and rooftops of a liquefied natural gas (LNG) container tanks, and, as well as those steel plates for use in building inboard tanks of liquefied natural gas container ships. Because these applications involve exposure to extra low temperatures below -160°C, weld toughness is of vital significance.
  • LNG liquefied natural gas
  • Ni steel has been a typical category for the production of LNG tank fabricating steel plates.
  • a thin type has heretofore usually been selected, reflecting the fact that both the base and rooftop do not undergo heavy stress.
  • high toughness especially at welds is required.
  • tempering is useful in dissolving the island martensite.
  • the island martensite once generated is partly dissolved in a subsequent welding heat cycle (equivalent to tempering), with the apparent loss of dual phase regional toughness failing to take place.
  • the number of passes required is not more than three.
  • the island martensite is left totally undissolved after a subsequent welding heat cycle, whereby the dual phase region undergoes an outstanding toughness loss, with an increase in brittleness.
  • the plates so processed also meet, as necessary, the requirements for respective strengths (yield strength: more than 60 kgf/mm 2 , tensile strength: 70 to 85 kgf/mm 2 ) called for in the ASTM Standards (A553, A844) and the JIS Standards (SL9 N60).
  • the present invention can readily provide a low-temperature service structural nickel steel plate with excellent low-temperature toughness, particularly superior toughness at the welds, each inclusive of the coarse grain, fine grain and dual phase regions, and further provide such physical properties enabling to reinforcement of mechanical strength.
  • Each categorical steel according to the present invention has its chemical composition selected in the range specified above for content of elements, following the account given below.
  • Si is one of the characteristic elements involved in the present invention. This is because the compositional quantitative reduction of Si results in decreasing the volume of the island martensite generated in an area thermally affected due to heating from welding within the dual phase region. Si proves very useful in improving toughness in the dual phase region. To assure the toughness characteristic, it is required that where no Nb has been added, the content of Si be not more than 0.22%. If some Nb has been included, the content thereof must be not more than 0.25%.
  • Mn is also one of the characteristic elements included in the present invention, along with Si. Decreasing the Mn-content renders usefulness to decrease along with the decrease in Si-content, the volume of the island martensite generated in the dual phase region subjected to heating from welding and incurring of a subsequent thermal effect. With this in view, it is necessary that the Mn-content be not more than 0.47% in the case where no Nb has not been added and that the Mn content be not more than 0.50% for the case with Nb added.
  • the lower limit of the Mn-content was set at 0.05%.
  • the toughness at the welds was examined in submerged arc welding of a steel plate which is produced with such a basic chemical composition of P: 0.004%, S: 0.001%, Ni: 8 to 11%, and Al: 0.03% fixed while the C-, Si- and Mn-contents are variously changed over a range of 123C+(8Si+9Mn) ⁇ 12%.
  • the notches provided in a test piece steel plate prepared for the weld toughness proof test, and which are located at the positions 4 mm and 8 mm off the weld fusion boundary, correspond respectively to the fine grain and dual phase regions.
  • Fig. 1 shows the relation between the toughness at the point 4 mm off the fusion boundary and (8Si+9Mn) while Fig. 2 shows the relation between the toughness at the position 8 mm off the fusion boundary and (8Si+9Mn).
  • Figs. 3 and 4 present the relationship between the toughness at the position 4 mm off the fusion boundary and (8Si+9Mn) and the relationship between the toughness at the position 8 mm off the fusion boundary and (8Si+9Mn).
  • superior low-temperature toughness is achieved both at the fine grain and dual phase regions where the total contents of Si and Mn are within a range of 2.2% ⁇ (8Si+9Mn) ⁇ 5.9%.
  • C is another of the elements characteristic of the present invention. Decreasing the content of C, similarly to the respective cases of Si and Mn, coincides with reducing the volume of the island martensite within the dual phase region subjected to heating, whereby the toughness therein is improved. Also, in the fine grain region formed after heating, there is generated the island martensite, but decreasing the content of C in said fine grain region serves to suppress generation of the island martensite without increasing the size of grains up to the magnitude of coarse grains. The reduction in C-content is effective to improve the toughness within the fine grain region.
  • selecting the C-content at less than 0.03% for the case where no Nb has been added entails increasing the size of coarse grains, with the result that the toughness therein declines, the C-content of 0.03% is preferred.
  • C is a useful element to assure of sufficient mechanical strength.
  • Fig. 5 gives the relation between the toughness at the position 4 mm off the fusion boundary and 123C+(8Si+9Mn)
  • Fig. 6 the relation between the toughness at the position 8 mm off the fusion boundary and 123C+(8Si+9Mn).
  • Figs. 7 and 8 present the relation between the toughness at the position 4 mm off the fusion boundary and 123C+(8Si+9Mn), and the relation between the toughness at the position 8 mm off the fusion boundary and 123C+(8Si+9Mn), respectively.
  • superior low-temperature toughness both within the fine grain and dual phase regions where the total contents of Si and Mn are selected such as meet the relation of 123C+(8Si+9Mn) ⁇ 13.5%.
  • P is also one of the elements characteristic of the present element. Decreasing the content of P has a favorable effect on the improvement of the toughness at each of a base metal and welds, particularly the toughness within the dual phase region which has gone through heating from welding. It is accordingly desired to restrain mixing with P as far as possible, but the P-content of not more than 0.005% is permissible.
  • S also adversely affects the toughness respectively of a base metal and welds. With this taken into account, it is desired that the content of S be minimized at far as possible. However, the S-content of not more than 0.005% is permissible.
  • Ni is helpful to assure the low-temperature structural nickel steels having high toughness, the Ni-content of less than 7.5% is not useful. Meanwhile, it is found that increasing the Ni-content beyond 12% fails to provide higher usefulness proportionally to its added quantity, but rather results in the saturation of usefulness, thus being uneconomical. Considering this, the Hi-content is limited to a range of 7.5 to 12.0%.
  • Al is an element essential for deoxidation. But the Al-content of less than 0.01% is not useful in this purpose. Raising the Al-content beyond 0.10% gives rise to the trouble of impairing its serviceability over purification. With this in view, the Al-content is limited to a range of 0.01 to 0.10%.
  • Nb is an element useful not only for bettering the mechanical strength of both a base metal and welds via separating functional intensification, but also for improving the toughness of the entirety of a thermally affected area including the base metal and welds through lessening the size of grains.
  • Nb-content of less than 0.005% fails to carry serviceability for high toughness maintenance and prescribed mechanical strength assurance, and that increasing the Nb-content beyond 0.03% is neither useful to boost the mechanical strength, but rather results in impairing toughness, it is necessary to keep the Nb-content within a range of 0.005 to 0.03%.
  • V contributes to effectively improve the mechanical strength through separating functional intensification. With this in mind. it is allowed to add V to increase the mechanical strength. However, the V-content of less than 0.005% fails to improve mechanical strength. Meanwhile, increasing the V-content beyond 0.03% produces toughness impairment. Noting this, it is necessary to limit the V-content within a range of 0.005 to 0.03%.
  • any of the conventional known processes enumerated below for metal making is applicable. They comprise each post-rolling reheat quenching and tempering (RQ-T), post-rolling reheat quenching, dual phase region quenching and tempering (RQ-Q'-T), post-rolling direct quenching and tempering (DQ-T), and post-rolling direct quenching, dual phase region quenching and tempering (DQ-Q'-T), and so forth.
  • RQ-T post-rolling reheat quenching and tempering
  • RQ-Q'-T dual phase region quenching and tempering
  • DQ-T post-rolling direct quenching and tempering
  • DQ-Q'-T post-rolling direct quenching, dual phase region quenching and tempering
  • the chemical compositional content ranges proposed by the present invention are especially useful with the steel plate of a thickness of not more than 10 mm.
  • the steel plates (numbered 13 and 14), each with the Si-content exceeding 0.22%, and those (numbered 15 and 16), each with the Mn-content surpassing 0.47% displayed a conspicuous loss in the toughness at the position 8 mm off the fusion boundary.
  • the whole of these steel plates were of such chemical compositions as to meet the relation of 3% ⁇ (8Si+9Mn) ⁇ 5.5% in respect of the Si- and Mn-contents.
  • the steel plate numbered 20 of which chemical composition is disclosed in said Japanese Unexamined Patent Publication No. 63-128118 was likewise observed to possess a remarkable loss in the toughness at each of the respective positions 4 mm and 8 mm off the fusion boundary.
  • Steel slabs comprising a variety of chemical compositions (each inclusive of Nb) shown in Table 3 underwent hot rolling down to a thickness of 6 mm under a heating temperature of 1200°C and a finish rolling temperature of 800°C, then cooling to a room temperature, reheat quenching which comprised of 30-minute heating at 780°C and water-cooling immediately thereafter, and 45-minute tempering at 570°C (RQ-T). Thereafter, each plate was subjected to submerged arc welding under the condition inclusive of a heat input of 20 kJ/cm, and 2 passes, using an austenitic steel wire. Subsequently, the base metal was examined for mechanical strength and toughness, with each weld likewise undergoing a toughness examination.
  • the steel plates (numbered 1 to 7), each prepared in an optimal chemical compositional content range as prescribed in the present invention had excellent toughness characteristics at welds.

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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)
  • Arc Welding In General (AREA)

Claims (9)

  1. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance à la soudure, ayant la composition suivante :
    C :   pas moins de 0,03% en poids
    Si :   0,02 à 0,22% en poids
    Mn :   0,05 à 0,47% en poids
    P :   pas plus de 0,005% en poids
    S :   pas plus de 0,005% en poids
    Ni :   7,5 à 12,0% en poids
    Al :   0,01 à 0,10% en poids, et
    équilibre :   Fe sans impuretés
    de laquelle proviennent les relations suivantes ; 3% en poids ≤ (8Si + 9Mn) ≤ 5,5% en poids
    Figure imgb0025
     et 123C + (8Si + 9Mn) ≤ 12% en poids
    Figure imgb0026
  2. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance à la soudure, ayant la composition suivante :
    Si :   0,02 à 0,25% en poids
    Mn :   0,05 à 0,50% en poids
    P :   pas plus de 0,005% en poids
    S :   pas plus de 0,005% en poids
    Ni :   7,5 à 12,0% en poids
    Al :   0,01 à 0,10% en poids
    Nb :   0,005 à 0,03% en poids, et
    équilibre :   Fe sans impuretés
    de laquelle proviennent les relations suivantes ; 2,2% en poids ≤ (8Si + 9Mn) ≤ 5,9% en poids
    Figure imgb0027
     et 9,5% en poids ≤ 123C + (8Si + 9Mn) ≤ 13,5% en poids
    Figure imgb0028
  3. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance à la soudure, ayant la composition suivante :
    Si :   0,02 à 0,25% en poids
    Mn :   0,05 à 0,50% en poids
    P :   pas plus de 0,005% en poids
    S :   pas plus de 0,005% en poids
    Ni :   7,5 à 12,0% en poids
    Al :   0,01 à 0,10% en poids
    Nb :   0,005 à 0,03% en poids
    V :   0,005 à 0,03% en poids, et
    équilibre :   Fe sans impuretés
    de laquelle proviennent les relations suivantes ; 2,2% en poids ≤ (8Si + 9Mn) ≤ 5,9% en poids
    Figure imgb0029
     et 9,5% en poids ≤ 123C + (8Si + 9Mn) ≤ 13,5% en poids
    Figure imgb0030
  4. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance à la soudure, selon la revendication 1, dans laquelle la plaque en acier présente une épaisseur inférieure à 10 mm.
  5. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance à la soudure, selon la revendication 1, dans laquelle chaque soudure de ladite plaque en acier est conçue de façon à ne pas dépasser trois passages par cycle de soudure.
  6. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance au soudage, selon la revendication 2, dans laquelle ladite plaque en acier a une épaisseur inférieure à 10 mm.
  7. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance au soudage, selon la revendication 3, dans laquelle ladite plaque en acier a une épaisseur inférieure à 10 mm.
  8. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance au soudage, selon la revendication 2, dans laquelle chaque soudure de ladite plaque en acier est conçue de façon à ne pas dépasser trois passages par cycle de soudure.
  9. Plaque en acier au nickel fonctionnant à basse température et présentant une excellente résistance au soudage, selon la revendication 3, dans laquelle chaque soudure de ladite plaque en acier est conçue de façon à ne pas dépasser trois passages par cycle de soudure.
EP91112442A 1990-01-25 1991-07-24 TÔles en acier au nickel, destinées aux utilisations à basse température et présentant une excellente tenacité des cordons de soudure Expired - Lifetime EP0524335B1 (fr)

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DE1991620266 DE69120266T2 (de) 1991-07-24 1991-07-24 Grobbleche aus Nickelstahl für Verwendung bei niedriger Temperatur versehen mit Schweissnähten von sehr hoher Zähigkeit

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JP2013738A JP2557993B2 (ja) 1990-01-25 1990-01-25 溶接部靭性の優れた低温用薄物ニッケル鋼板

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US11371121B2 (en) 2017-10-26 2022-06-28 Nippon Steel Corporation Nickel-containing steel for low temperature
CN111263827B (zh) 2017-10-26 2021-12-21 日本制铁株式会社 低温用含镍钢
US11384416B2 (en) 2017-10-26 2022-07-12 Nippon Steel Corporation Nickel-containing steel for low temperature
US11371127B2 (en) 2017-10-26 2022-06-28 Nippon Steel Corporation Nickel-containing steel for low temperature
JP6984320B2 (ja) * 2017-10-31 2021-12-17 日本製鉄株式会社 靭性に優れた低温用ニッケル含有鋼板およびその製造方法

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63290246A (ja) * 1987-05-22 1988-11-28 Kawasaki Steel Corp 溶接部靭性の優れた低温用鋼

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Publication number Priority date Publication date Assignee Title
NL298097A (fr) * 1962-09-21
FR1454534A (fr) * 1965-08-27 1966-02-11 Siderurgie Fse Inst Rech Alliage à caractéristiques élevées
JPS58217629A (ja) * 1982-06-12 1983-12-17 Kobe Steel Ltd 溶接継手部の靭性のすぐれた低温用鋼の製造方法
JPS61127815A (ja) * 1984-11-26 1986-06-16 Nippon Steel Corp 高アレスト性含Ｎｉ鋼の製造法
JPS63128118A (ja) * 1986-11-18 1988-05-31 Sumitomo Metal Ind Ltd 低温靭性にすぐれた低温用鋼の製造法

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63290246A (ja) * 1987-05-22 1988-11-28 Kawasaki Steel Corp 溶接部靭性の優れた低温用鋼

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
pages 681 - 688; WITZKE ET AL.: 'Development of strong and tough cryogenic Fe- 12Ni alloys containing reactive metal additions' *

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JPH03223442A (ja) 1991-10-02
JP2557993B2 (ja) 1996-11-27

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