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WO2024202929A1 - Tôle d'acier contenant du nickel pour applications à basse température et réservoir pour applications à basse température dans lesquelles ladite tôle d'acier est utilisée - Google Patents

Tôle d'acier contenant du nickel pour applications à basse température et réservoir pour applications à basse température dans lesquelles ladite tôle d'acier est utilisée Download PDF

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Publication number
WO2024202929A1
WO2024202929A1 PCT/JP2024/007773 JP2024007773W WO2024202929A1 WO 2024202929 A1 WO2024202929 A1 WO 2024202929A1 JP 2024007773 W JP2024007773 W JP 2024007773W WO 2024202929 A1 WO2024202929 A1 WO 2024202929A1
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mass
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toughness
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Japanese (ja)
Inventor
直樹 橋本
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Kobe Steel Ltd
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Kobe Steel Ltd
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Priority to KR1020257030198A priority Critical patent/KR20250150043A/ko
Priority to CN202480017850.4A priority patent/CN120769929A/zh
Priority to EP24779067.8A priority patent/EP4663802A1/fr
Publication of WO2024202929A1 publication Critical patent/WO2024202929A1/fr
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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
    • 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
    • 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
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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

Definitions

  • This disclosure relates to nickel-containing steel plate for low temperature use and a low temperature tank using the same.
  • LNG tanks are designed and constructed with particular consideration given to safety, and therefore, in addition to the steel materials and welding materials used, low-temperature toughness is also important for welded joints, and Charpy impact absorption energy values are specified in various standards, including ASTM (American Society for Testing and Materials).
  • Welding is essential when constructing structures such as low-temperature tanks using such nickel-containing steel plates, and it is essential to ensure the low-temperature toughness of the welded joints (welds) created by welding.
  • Patent Document 1 discloses that reducing Si and P is an effective method for improving the low-temperature toughness of the dual-phase HAZ (intercritically reheated heat-affected zone, hereafter sometimes referred to as "IC-HAZ"). Patent Document 1 also describes that refining martensite that forms locally in the IC-HAZ contributes to improving low-temperature toughness.
  • Patent Document 2 discloses the reduction of Si and the addition of Mo as a method for improving the CTOD characteristics of the HAZ.
  • Patent Document 3 describes a manufacturing method for 9% Ni steel in which the toughness of welded joints is improved by reducing the amount of silicon. It shows that reducing the amount of silicon reduces the amount of MA in the HAZ, which is heated to the two-phase region of ferrite and austenite.
  • Patent Document 4 discloses the reduction of Si, Al, and N as a method for improving HAZ toughness at the toe portion. It also shows that the reduction of Si and Al promotes auto-tempering, and that this effect is due to the reduction of AlN inclusions.
  • Patent Document 5 discloses that the toughness of the base material and welded joints can be improved by controlling the contents of C, Si, Al, and Mo. It also shows that the effect is due to the refinement of the structure during tempering by adding Mo, and the suppression of the formation of hardened phases.
  • Patent Document 6 discloses a method for producing 9% Ni steel with excellent toughness in the base material and welded joints, which involves reducing Si and performing two-stage hot rolling.
  • Japanese Unexamined Patent Publication No. 61-238911 Japanese Patent Application Publication No. 4-371520 Japanese Unexamined Patent Publication No. 7-126749 Patent No. 5126780 JP 2002-129280 A JP 2013-142197 A
  • GTAW automated TIG welding
  • SAW SAW
  • GTAW is a less efficient welding method
  • SAW also has the problem of being less efficient, since the maximum heat input is set to 50 kJ/cm or less to reduce the risk of brittle fracture from the weld heat-affected zone. For this reason, there is a strong demand for high-heat-input welding, with a welding heat input of more than 50 kJ/cm, in order to improve construction efficiency and reduce welding costs.
  • Patent Documents 1 to 6 were all evaluated for low heat input welded joints with a welding heat input of 50 kJ/cm or less, and sufficient consideration was not given to the suppression of MA formation in the IC-HAZ, where toughness deteriorates most when low-temperature nickel-containing steel plates are welded with high heat input, and to grain boundary embrittlement due to P. Therefore, there is a risk that the steel plates described in Patent Documents 1 to 6 will not be able to ensure sufficient low-temperature toughness of the welded joints to suppress brittle fracture of the tank when high heat input welding is applied.
  • This disclosure has been made in light of these circumstances, and aims to provide a nickel-containing steel plate for low-temperature use that can ensure sufficient low-temperature toughness of welded joints even when large heat input welding is applied, and a low-temperature tank that uses said steel plate.
  • Aspect 1 of the present invention is C: 0.01 to 0.12% by mass, Si: 0.01 to 0.18% by mass, Mn: 0.2 to 1.8% by mass, P: 0.0100% by mass or less (including 0% by mass), S: 0.0100% by mass or less (including 0% by mass), Al: 0.001 to 0.100% by mass, N: 0.0080 mass% or less (including 0 mass%), Mo: 0.01 to 0.10% by mass, Ni: 8.75 to 10.0% by mass, Cu: 0.70% by mass or less (including 0% by mass), and Cr: 0.20% by mass or less (including 0% by mass) The balance is Fe and unavoidable impurities.
  • the nickel-containing steel sheet for low temperature use has a DI value expressed by the following formula (1) of 1.03 or more and 1.65 or less, and a value calculated using the following formula (2) of 7.06 or less.
  • DI 1.16 ⁇ ([C]/10) ⁇ (0.7[Si]+1) ⁇ (3.33[Mn]+1) ⁇ (0.35[Cu]+1) ⁇ (0.36[Ni]+1) ⁇ (2.16[Cr]+1) ⁇ (3[Mo]+1) ⁇ (1.75[V]+1) ⁇ (200[B]+1) ...(1)
  • [ ] indicates the content of the element shown within, expressed as mass %.
  • [ ] indicates the content of the element shown within, expressed as mass %.
  • Aspect 2 of the present invention is a low-temperature tank using the low-temperature nickel-containing steel plate described in aspect 1.
  • a nickel-containing steel plate for low-temperature use that can ensure sufficient low-temperature toughness of the welded joint even when high heat input welding is applied
  • a low-temperature tank e.g., a tank for storing low-temperature liquefied gas such as LNG, which is a clean energy source
  • LNG low-temperature liquefied gas
  • 1 is a graph showing the relationship between DI value and base material strength (yield stress and tensile strength). 1 is a graph showing the relationship between the value of the first term of equation (2) and the MA area fraction. 1 is a graph showing the relationship between the value of formula (2) and the Charpy impact absorption energy value vE ⁇ 196 at ⁇ 196° C.
  • the present inventors have conducted extensive research to solve the above problems. As a result, they have found that a desired tensile strength can be obtained without impairing the low-temperature toughness of the base metal and joint by not only optimizing the range of the content of each element but also by setting the DI value defined by the formula (1) described below to an appropriate value, and further that by setting the value defined by the formula (2) described below within a predetermined range, the formation of MA (Martensite-Austenite constituent, island martensite) and grain boundary embrittlement in the IC-HAZ during high heat input welding can be suppressed, thereby more reliably improving the low-temperature toughness, and have arrived at the present invention.
  • MA Martensite-Austenite constituent, island martensite
  • the nickel-containing steel plate for low temperature use according to the embodiment of the present invention has the chemical composition described below.
  • C 0.01 mass% or more, 0.12 mass% or less
  • C is one of the elements that characterize the embodiment of the present invention, and if its content exceeds 0.12 mass%, it promotes the formation of MA (island martensite) in the IC-HAZ during high heat input welding, and deteriorates the low-temperature toughness of the joint. For this reason, the upper limit of the C content is set to 0.12 mass%.
  • C is an element that increases the strength of steel, and it is necessary to contain 0.01 mass% or more in order to ensure the desired strength. Therefore, the C content is set to a range of 0.01 to 0.12 mass%.
  • the upper limit of the C content is preferably 0.10 mass%, more preferably 0.08 mass%.
  • Si 0.01% by mass or more, 0.18% by mass or less
  • Si is one of the elements that characterize the embodiment of the present invention.
  • Si content is set to 0.18 mass % or less.
  • Si is an element necessary as a deoxidizer and for ensuring strength, and if the content is less than 0.01 mass%, the effect is insufficient. Therefore, the Si content is set to 0.01
  • the lower the Si content the more the formation of MA in the IC-HAZ is suppressed, so the upper limit of the Si content is preferably 0.14 mass%.
  • Mn 0.2 mass% or more, 1.8 mass% or less
  • Mn is an element necessary for improving the hardenability of steel and ensuring strength. If the Mn content is less than 0.2 mass%, the effect is insufficient, and if the Mn content exceeds 1.8 mass%, the toughness is deteriorated. Therefore, the Mn content is set to a range of 0.2 to 1.8 mass%, and the preferred range of the Mn content is 0.3 to 1.2 mass%.
  • P 0.0100% by mass or less (including 0% by mass)
  • P is one of the elements that characterize the embodiment of the present invention, and is inevitably present in steel as an impurity. It segregates at grain boundaries and deteriorates the low-temperature toughness of the base material and the welded joint. Therefore, the upper limit is set to 0.0100 mass%. In order to improve the low-temperature toughness of the welded joint, the lower the P content, the more desirable it is.
  • including 0 mass % means a content in accordance with an embodiment that is not intentionally added, for example, a content at the level of unavoidable impurities (it does not exclude cases where the content is intentionally added within a specified range).
  • not including 0 mass % means that the element in question is intentionally added.
  • S 0.0100% by mass or less (including 0% by mass)
  • S is an element present in steel as an inevitable impurity, and if the content is too high, elongated MnS becomes the starting point of brittle fracture, degrading the toughness of the base material and the welded joint. Therefore, the upper limit of the S content is set to 0.0100 mass%. In order to improve the toughness of the joint, the lower the S content, the better.
  • Al 0.001% by mass or more, 0.100% by mass or less
  • Al is a deoxidizer and is an effective element for suppressing the coarsening of crystal grains and ensuring toughness, but if its content is less than 0.001 mass %, a sufficient effect cannot be obtained. On the other hand, if the Al content exceeds 0.100 mass%, brittle fracture occurs starting from the alumina inclusions, deteriorating the toughness. The range is % by mass.
  • N 0.0080% by mass or less (including 0% by mass)
  • N is an impurity that deteriorates the toughness of the base material and the welded joint through the formation of precipitates such as AlN, so the upper limit is set to 0.0080 mass%. In order to improve the toughness of the joint, the lower the N content, the better.
  • Ni 8.75% by mass or more, 10.0% by mass or less
  • Ni is a basic element added to ensure toughness at cryogenic temperatures (low temperature toughness), and in the embodiment of the present invention, the Ni content is set to 8.75 mass% or more. The higher the Ni content, the better the steel. Although low temperature toughness can be obtained, the effect of improving the properties is small with the increase in alloy cost when the Ni content exceeds 10.0 mass %. Therefore, the Ni content is set to the range of 8.75 to 10.0 mass %. From the viewpoint of ensuring low-temperature toughness and reducing alloy costs, the Ni content is more preferably in the range of 8.95 to 9.85 mass %.
  • Mo 0.01% by mass or more and 0.10% by mass or less
  • Mo is one of the elements that characterize the embodiment of the present invention.
  • Mo is one of the elements that characterize the embodiment of the present invention.
  • Cu 0.70% by mass or less (including 0% by mass)
  • Cu is an element contained in steel in trace amounts as an unavoidable impurity, and is usually contained at an impurity level of about 0.03 mass % or less.
  • the Cu content exceeds 0.70 mass%, it deteriorates toughness. Therefore, when Cu is intentionally added, the Cu content is 0.70 mass% or less (excluding 0 mass%).
  • the lower limit of the Cu content is preferably 0.05 mass%.
  • Cr 0.20 mass% or less (including 0 mass%)
  • Cr is an element contained in steel in trace amounts as an unavoidable impurity, and is usually contained at an impurity level of about 0.08 mass % or less. Cr may be added intentionally as necessary to improve the hardenability and strength of steel. On the other hand, if the content exceeds 0.20 mass%, it deteriorates toughness. Therefore, when Cr is intentionally added, the Cr content is set to 0.20 mass% or less (excluding 0 mass%). In order to reliably obtain the above-mentioned effects, the lower limit of the Cr content is preferably 0.10 mass%.
  • the balance is iron and inevitable impurities.
  • inevitable impurities elements (e.g., As, Sb, Nb, O, H, etc.) that are brought in due to the conditions of raw materials, materials, manufacturing facilities, etc. are allowed to be mixed in.
  • P and S are elements whose content is usually the lower the better and therefore are unavoidable impurities, but whose composition ranges are separately defined as above. Therefore, in this specification, the "unavoidable impurities" constituting the balance are a concept excluding elements whose composition ranges are separately defined.
  • the nickel-containing steel sheet for low temperature use according to the embodiment of the present invention has a DI value represented by the following formula (1) of 1.03 or more and 1.65 or less.
  • DI 1.16 ⁇ ([C]/10) ⁇ (0.7[Si]+1) ⁇ (3.33[Mn]+1) ⁇ (0.35[Cu]+1) ⁇ (0.36[Ni]+1) ⁇ (2.16[Cr]+1) ⁇ (3[Mo]+1) ⁇ (1.75[V]+1) ⁇ (200[B]+1) ...(1)
  • the brackets [ ] indicate the content of the element shown within, expressed in mass %. That is, for example, [C] means the content of C, expressed in mass %.
  • the yield stress must be 590 MPa or more and the tensile strength must be 680 MPa or more.
  • the upper limit of tensile strength (TS) should be 830 MPa or less, and more preferably 800 MPa or less.
  • the DI value defined in the above formula (1) is a general parameter that indicates the hardenability of steel material, and the higher the DI value, the greater the dislocation density introduced into the material during hardening. For this reason, by controlling the DI value, it is possible to control the strength of low-temperature nickel-containing steel plate manufactured by quenching-tempering, quenching-intermediate heat treatment-tempering, or direct quenching-tempering, which are manufacturing methods commonly applied to low-temperature nickel-containing steel plate. If the DI value is in the range of 1.03 to 1.65, it is possible to keep the strength within the above range without impairing the toughness of the base material and welded joint.
  • the Charpy impact absorption energy value vE- 196 of the IC-HAZ portion of the welded joint at -196°C is 34J or more, and brittle fracture is suppressed even in applications requiring toughness at extremely low temperatures such as LNG tanks, and excellent toughness of the welded joint can be ensured.
  • the Charpy impact absorption energy value vE -196 being 34J or more means that the standard value (average 34J or more) of the L-direction Charpy impact absorption energy value of 9% Ni steel (joint) specified in the ASTM standards (ASTM A553/A553M: 2022 and ASTM A844/A844M: 2022) is satisfied.
  • a step of quenching from a two-phase region of Ac 1 point or more and Ac 3 point or less may be included between quenching and tempering, or the steel sheet may be produced by directly quenching a hot-rolled steel sheet after hot rolling online and then tempering it in a temperature range of Ac 1 point or less.
  • the nickel-containing steel plates for low temperature according to the embodiments of the present invention obtained in this manner can be used and welded to obtain a low temperature tank (for example, a tank for storing low temperature liquefied gas such as LNG, which is a clean energy source) according to the embodiments of the present invention.
  • a low temperature tank for example, a tank for storing low temperature liquefied gas such as LNG, which is a clean energy source
  • the welded joints have excellent low temperature toughness even when welding is performed using a large heat input welding method, and therefore a low temperature tank with sufficient low temperature toughness can be obtained.
  • high heat input welding refers to a welding method in which the welding heat input exceeds 50 kJ/cm, as described in Note (6) of Table M4.2 on page 16 of the "2021 Rules for Steel Ships, Part M” published by Nippon Kaiji Kyokai.
  • a sample for thermal cycle testing was obtained by cutting out a sample having a size of 12 mm x 33 mm x 55 mm from the t/4 position of the obtained steel plate sample (a position at a distance of 1/4 of the plate thickness t from the surface (main surface) of the steel plate toward the center) so that the plate thickness direction was 12 mm and the rolling direction was parallel to the 55 mm direction. Also, a bar-shaped test piece was taken from the steel plate sample at the t/4 position in a direction perpendicular to the rolling direction, and this was used as a sample for a tensile test.
  • V-notch Charpy standard test sample in accordance with Japanese Industrial Standard JIS 2242: 2018 was prepared from each heat cycle test sample. Then, using the V-notch Charpy standard test sample, a Charpy impact test was performed at -196 ° C., and the Charpy impact absorption energy value vE -196 was measured. For one type of sample (for one sample No.), the impact test was performed three times. The measurement results of vE -196 for each of the three tests are shown in the "each" column of Table 2, and the average value is shown in the "ave.” column of Table 2.
  • MA area fraction The amount of MA in the thermal cycle test sample after the above-mentioned simulated thermal history was measured. After wet polishing, the sample was etched with Repellant after excluding the end 3 mm of the thermal cycle test sample to which the simulated thermal history had been given. The structure of a 155 ⁇ m ⁇ 202 ⁇ m area was observed with an optical microscope at a magnification of 400 times to identify MA from the contrast, and the area fraction of MA was calculated. The results are shown in Table 2.
  • Figure 1 shows the relationship between the DI value and the base material strength (yield stress and tensile strength)
  • Figure 2 shows the relationship between the value of the first term of formula (2) and the MA area fraction
  • Figure 3 shows the relationship between the value of formula (2) and the Charpy impact absorption energy value vE -196 (average value of three samples) at -196°C.
  • the dotted line in Figure 3 is a quadratic approximation curve.
  • Samples No. 1 to 8 which have the chemical composition specified in the embodiment of the present invention and have DI values and values of formula (2) within the specified range, have sufficient strength and low-temperature toughness.
  • they have the strength required as a structural material for application to low-temperature tanks such as LNG, and can ensure sufficient low-temperature toughness for low-temperature tanks even when subjected to thermal history in the IC-HAZ, which is prone to toughness degradation during high-heat-input welding, and therefore can be said to contribute to improving welding construction efficiency by applying high-heat-input welding.
  • sample No. 9 has an excessive amount of Si and an insufficient amount of Mo, and the value of formula (2) is outside the predetermined range. For this reason, when a thermal history of high heat input welding is applied, the formation of MA is remarkable, and further, the influence of grain boundary embrittlement due to P is large, and sufficient low-temperature toughness cannot be secured when high heat input welding is applied.
  • the value of formula (2) is outside the predetermined range because the content ratio of Mo to P is small, so that the effect of grain boundary embrittlement due to P becomes significant, and sufficient low-temperature toughness cannot be ensured when large heat input welding is applied.

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Abstract

L'invention concerne une tôle d'acier contenant du nickel pour des applications à basse température contenant C : 0,01 à 0,12 % en masse, Si : 0,01 à 0,18 % en masse, Mn : 0,2 à 1,8 % en masse, P : 0,0100 % en masse ou moins (y compris 0 % en masse), S : 0,0100 % en masse ou moins (y compris 0 % en masse), Al : 0,001 à 0,100 % en masse, N : 0,0080 % en masse ou moins (y compris 0 % en masse), Mo : 0,01 à 0,10 % en masse, Ni : 8,75 à 10,0 % en masse, Cu : 0,70 % en masse ou moins (y compris 0 % en masse) et Cr : 0,20 % en masse ou moins (y compris 0 % en masse), et le reste étant constitué de Fe et d'impuretés inévitables. Dans la tôle d'acier contenant du nickel pour des applications à basse température, la valeur DI est de 1,03 à 1,65, et une valeur calculée en utilisant une formule prédéterminée est de 7,06 ou moins.
PCT/JP2024/007773 2023-03-30 2024-03-01 Tôle d'acier contenant du nickel pour applications à basse température et réservoir pour applications à basse température dans lesquelles ladite tôle d'acier est utilisée Pending WO2024202929A1 (fr)

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KR1020257030198A KR20250150043A (ko) 2023-03-30 2024-03-01 저온용 니켈 함유 강판 및 이를 이용한 저온용 탱크
CN202480017850.4A CN120769929A (zh) 2023-03-30 2024-03-01 低温用含镍钢板和使用它的低温用储罐
EP24779067.8A EP4663802A1 (fr) 2023-03-30 2024-03-01 Tôle d'acier contenant du nickel pour applications à basse température et réservoir pour applications à basse température dans lesquelles ladite tôle d'acier est utilisée

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Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61238911A (ja) 1985-04-12 1986-10-24 Nippon Steel Corp 溶接熱影響部の靭性の優れた低温用鋼の製造法
JPH04371520A (ja) 1991-06-19 1992-12-24 Nippon Steel Corp 母材および溶接熱影響部のＣＴＯＤ特性の優れた厚肉９％Ｎｉ鋼の製造法
JPH07126749A (ja) 1993-11-09 1995-05-16 Kobe Steel Ltd 溶接部の靱性の優れた９％Ｎｉ鋼の製造方法
JP2002012951A (ja) * 2000-06-28 2002-01-15 Nippon Steel Corp 応力除去焼鈍後の溶接部靭性に優れた厚肉９％Ｎｉ鋼
JP2002129280A (ja) 2001-09-13 2002-05-09 Sumitomo Metal Ind Ltd 低温用Ｎｉ含有鋼とその製造方法
CN101717887A (zh) * 2009-11-13 2010-06-02 北京科技大学 一种基于回转奥氏体韧化的低温钢及其制备方法
JP5126780B2 (ja) 2006-01-13 2013-01-23 新日鐵住金株式会社 溶接熱影響部のｃｔｏｄ特性に優れた極低温用鋼
JP2013014811A (ja) * 2011-07-06 2013-01-24 Nippon Steel & Sumitomo Metal Corp 極低温用鋼材およびその製造方法
JP2013142197A (ja) 2012-01-13 2013-07-22 Nippon Steel & Sumitomo Metal Corp −１９６℃におけるシャルピー試験値が母材、溶接継手共に１００Ｊ以上である靭性と生産性に優れたＮｉ添加鋼板およびその製造方法
JP2018043288A (ja) * 2016-09-13 2018-03-22 株式会社神戸製鋼所 エレクトロスラグ溶接用ワイヤ、エレクトロスラグ溶接用フラックス及び溶接継手
JP2022015244A (ja) * 2020-07-08 2022-01-21 日本製鉄株式会社 低温用Ｎｉ鋼を用いた溶接継手の製造方法及びこれにより得られた溶接継手
JP2023055986A (ja) 2021-11-02 2023-04-18 東北パイオニア株式会社 スピーカ装置

Patent Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61238911A (ja) 1985-04-12 1986-10-24 Nippon Steel Corp 溶接熱影響部の靭性の優れた低温用鋼の製造法
JPH04371520A (ja) 1991-06-19 1992-12-24 Nippon Steel Corp 母材および溶接熱影響部のＣＴＯＤ特性の優れた厚肉９％Ｎｉ鋼の製造法
JPH07126749A (ja) 1993-11-09 1995-05-16 Kobe Steel Ltd 溶接部の靱性の優れた９％Ｎｉ鋼の製造方法
JP2002012951A (ja) * 2000-06-28 2002-01-15 Nippon Steel Corp 応力除去焼鈍後の溶接部靭性に優れた厚肉９％Ｎｉ鋼
JP2002129280A (ja) 2001-09-13 2002-05-09 Sumitomo Metal Ind Ltd 低温用Ｎｉ含有鋼とその製造方法
JP5126780B2 (ja) 2006-01-13 2013-01-23 新日鐵住金株式会社 溶接熱影響部のｃｔｏｄ特性に優れた極低温用鋼
CN101717887A (zh) * 2009-11-13 2010-06-02 北京科技大学 一种基于回转奥氏体韧化的低温钢及其制备方法
JP2013014811A (ja) * 2011-07-06 2013-01-24 Nippon Steel & Sumitomo Metal Corp 極低温用鋼材およびその製造方法
JP2013142197A (ja) 2012-01-13 2013-07-22 Nippon Steel & Sumitomo Metal Corp −１９６℃におけるシャルピー試験値が母材、溶接継手共に１００Ｊ以上である靭性と生産性に優れたＮｉ添加鋼板およびその製造方法
JP2018043288A (ja) * 2016-09-13 2018-03-22 株式会社神戸製鋼所 エレクトロスラグ溶接用ワイヤ、エレクトロスラグ溶接用フラックス及び溶接継手
JP2022015244A (ja) * 2020-07-08 2022-01-21 日本製鉄株式会社 低温用Ｎｉ鋼を用いた溶接継手の製造方法及びこれにより得られた溶接継手
JP2023055986A (ja) 2021-11-02 2023-04-18 東北パイオニア株式会社 スピーカ装置

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