WO2017111290A1 - Pwht 저항성이 우수한 저온 압력용기용 강판 및 그 제조 방법 - Google Patents
Pwht 저항성이 우수한 저온 압력용기용 강판 및 그 제조 방법 Download PDFInfo
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- WO2017111290A1 WO2017111290A1 PCT/KR2016/012566 KR2016012566W WO2017111290A1 WO 2017111290 A1 WO2017111290 A1 WO 2017111290A1 KR 2016012566 W KR2016012566 W KR 2016012566W WO 2017111290 A1 WO2017111290 A1 WO 2017111290A1
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- pressure vessel
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Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties 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 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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- 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
- 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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- 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
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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
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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
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- 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
- C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
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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
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a thick steel plate used in low pressure vessels, vessels, storage tanks, structural steel, etc., and a method for manufacturing the same. More specifically, a low temperature pressure vessel steel plate having a tensile strength of 600 MPa or more having excellent PWHT resistance and low temperature toughness; The manufacturing method is related.
- ferrite As the high-strength thick steel for low temperature, ferrite, martensite structure, mixed structure composed of bainite structure, or near single phase structure mainly composed of bainite and ferrite are widely known.
- the high strength hot rolled steel produced through the normal NOMALIZING treatment may have a mixed structure of ferrite and pearlite.
- carbides are formed along the grain boundaries, and thus the strength and toughness of the steel are lowered, thereby making it impossible to guarantee the properties required for the PWHT.
- An example of the related art is the invention described in Korean Patent Publication No. 2012-0011289.
- the invention described in the above publication is a steel produced through the normal NOMALIZING, even if Ni is added, there is a problem that the strength and toughness of the steel after PWHT treatment can not be avoided.
- Patent Document 1 Republic of Korea Patent Publication No. 2012-0011289
- the present invention is to solve the problems of the prior art, by controlling the steel composition, cooling and heat treatment process to make the microstructure into a mixed structure of tempered bainite and tempered martensite for high strength low-temperature for high PWHT resistance for a long time
- An object of the present invention is to provide a pressure vessel steel sheet and a method of manufacturing the same.
- the present invention for achieving the above object, by weight, C: 0.07 ⁇ 0.17%, Si: 0.15 ⁇ 0.40%, Mn: 0.3 ⁇ 0.7%, P: 0.012% or less, S: 0.015% or less, Ni: 3.0 ⁇ 4.0%, W: 0.03 ⁇ 0.25%, balance Fe and unavoidable impurities, PWHT resistance steel plate with excellent PWHT resistance with 25 ⁇ 80 area% of tempered bainite and balance tempered martensite It is about.
- the steel sheet can maintain a tensile strength of 600MPa or more even if PWHT is performed for a maximum of 20 hours in the 580 ⁇ 640 °C section.
- the steel sheet may have a Charpy impact energy value at ⁇ 110 ° C. or higher at 200 J or more even when PWHT is performed for a maximum of 20 hours in a range of 580 ° C. to 640 ° C.
- the present invention in terms of weight%, C: 0.07-0.17%, Si: 0.15-0.40%, Mn: 0.3-0.7%, P: 0.012% or less, S: 0.015% or less, Ni: 3.0-4.0%, W : Reheating a steel slab composed of 0.03 to 0.25%, balance Fe and inevitable impurities at 1050 to 1250 ° C .;
- Low temperature PWHT resistance including; a step of tempering the water-cooled steel sheet ⁇ 1.5 ⁇ t + (10 ⁇ 30) ⁇ minutes (where t means the thickness of the steel (mm)) at 550 ⁇ 660 °C It relates to a method for producing a pressure vessel steel sheet.
- the tempering process may further include a step of PWHT up to 20 hours in the 580 ⁇ 640 °C section.
- the steel microstructure obtained by the tempering process may be composed of 25 to 80 area fraction (%) of tempered bainite and residual tempered martensite.
- the present invention having the above-described configuration can effectively provide a low-temperature pressure vessel steel sheet excellent in PWHT resistance that can be stably used at a low temperature of about -110 ° C while satisfying a tensile strength of 600 MPa or more.
- C 0.07 to 0.17%
- Si 0.15 to 0.40%
- Mn 0.3 to 0.7%
- P 0.012% or less
- S 0.015% or less
- Ni 3.0 to 4.0%
- W 0.03 to 0.25%
- the balance of Fe and unavoidable impurities the specific emphasis component and the reasons for limiting the components are as follows.
- C is preferably limited to 0.07 to 0.17%. This is because when the content is less than 0.07%, the strength of the matrix on the matrix is lowered, and when it exceeds 0.17%, the weldability of the steel sheet is greatly deteriorated.
- Si is a component added for the deoxidation effect, the solid solution strengthening effect, and the impact transition temperature raising effect, and in order to achieve such an addition effect, it is preferable to add 0.15% or more. However, if the content exceeds 0.40%, the weldability is lowered and the oxide film is severely formed on the surface of the steel sheet, so that the content is preferably limited to 0.15 to 0.40%.
- Mn forms MnS, which is a non-metallic inclusion drawn together with S, lowers the normal temperature elongation and low temperature toughness
- Mn is preferably managed at 0.7% or less.
- the amount of Mn added is preferably limited to 0.3 to 0.7%.
- P is an element that impairs low-temperature toughness, and it is preferable to suppress the content as much as possible, but it is desirable to manage it within 0.012% or less because excessive cost is required to remove it in the steelmaking process.
- S is also an element that adversely affects low temperature toughness along with P, but like P, it may be excessively expensive to remove in the steelmaking process, so it is appropriate to manage it within 0.015%.
- Ni is the most effective element for improving low temperature toughness. However, if the added amount is less than 3.0%, the low-temperature toughness is lowered, and if it is added in excess of 4.0%, the production cost is increased, and therefore it is preferably added within the range of 3.0 to 4.0%.
- W is an important element which increases the strength of the steel by solidifying the austenite to increase the hardenability of the austenite and to precipitate as carbide (W 2 C) to match the matrix (Matrix).
- W 2 C carbide
- Motrix matrix
- the steel sheet of the present invention has a microstructure of 25 to 80 area% of tempered bainite and the balance of tempered martensite. If the tempered bainite fraction is less than 25%, the amount of tempered martensite may be excessive to degrade the low temperature toughness of the steel sheet. On the other hand, if it exceeds 80%, it may be difficult to secure the strength of the target steel sheet.
- it may be composed of 30 to 70 area fraction (%) of tempered bainite and residual tempered martensite.
- the steel sheet having the above-described emphasis component and microstructure, as well as PWHT for up to 20 hours in a section of 580 ⁇ 640 °C can effectively maintain the tensile strength to 600MPa or more as well as have excellent low temperature toughness.
- Steel sheet manufacturing method of the present invention the step of reheating the steel slab having a steel composition as described above at 1050 ⁇ 1250 °C; A hot rolling step of hot rolling the reheated steel slab and finishing rolling at a temperature of 800 ° C. or higher to obtain a hot rolled steel sheet; Cooling the hot rolled steel sheet at a cooling rate of 2.5 to 30 ° C./sec after heating at 800 to 950 ° C .; And tempering the water-cooled steel for ⁇ 1.5 ⁇ t + (10-30) ⁇ minutes, where t denotes the thickness (mm) of the steel, at 550-660 ° C .;
- the steel slab having the steel composition is reheated at 1050 to 1250 ° C. If the reheating temperature is lower than 1050 °C, it is difficult to solute the solute atoms, and if the reheating temperature exceeds 1250 °C austenite grain size becomes too coarse to reduce the properties of the steel sheet.
- the reheated steel slab is hot rolled.
- the reheated steel slab is hot rolled and the rolling is finished at a temperature of 800 ° C. or higher.
- the hot rolling temperature is less than 800 ° C, the hot deformation resistance during rolling may increase, resulting in a load of the rolling mill.
- the rolling reduction per pass during the hot rolling is preferably 5 to 30%.
- the hot rolled steel sheet is cooled at a cooling rate of 2.5 ⁇ 30 °C / sec after heating at 800 ⁇ 950 °C.
- the heating temperature is less than 800 ° C, it is difficult to sufficiently solidify the alloy component, and if the heating temperature exceeds 950 ° C, grains may coarsen and damage toughness.
- the cooling rate is less than 2.5 °C / sec martensite structure can not be obtained, while the cooling rate is more than 30 °C / sec because a large amount of cooling water is required, there is an economic burden requiring additional cooling equipment cooling rate is It is preferable to limit to 2.5-30 degreeC / sec.
- the water-cooled steel sheet is tempered.
- the water-cooled steel sheet is tempered for ⁇ 1.5 ⁇ t + (10-30) ⁇ minutes (where t means the thickness of the steel (mm)) at 550 to 660 ° C. If the tempering temperature is less than 550 ° C., the toughness may be lowered due to excess strength, and if the tempering temperature is higher than 660 ° C., excessive strength may be reduced.
- the tempering time is performed for ⁇ 1.5 ⁇ t + (10 ⁇ 30) ⁇ minutes (where t means the thickness of the steel (mm)), but the specific reason is as follows.
- the tempering time is shorter than the above standard, it is difficult to obtain the tempered martensite structure, whereas if the tempering time exceeds the reference time, the overall productivity is impaired.
- it may be composed of 30 to 70 area fraction (%) of tempered bainite and residual tempered martensite.
- the tempered steel sheet may be subjected to a PWHT heat treatment to remove stresses in the welded part after welding for manufacturing the pressure vessel. That is, it may further include a process of PWHT for up to 20 hours in the 580 ⁇ 640 °C section.
- these steel slabs were reheated at 1100 °C.
- the reheated steel slab was hot rolled at a rolling reduction of 15% per pass, and hot rolling was finished at 900 ° C. to prepare hot rolled steel sheets having a predetermined thickness.
- the hot rolled steel sheets were heated and water-cooled at the austenitization temperature under the conditions shown in Table 2, and then tempered at the temperatures and times shown in Table 2 below. And the tampered steel sheet was also subjected to the PWHT treatment under the conditions of Table 2.
- low-temperature toughness is a result of evaluating a specimen having a V notch at -110 ° C as a Charpy impact energy value obtained by performing a Charpy impact test.
- the tempered bainite and the balance of 25-80% in an area fraction after tempering treatment Since the tempered martensite structure can be obtained, it can be seen that the yield strength and the tensile strength after the PWHT are superior to about 100 MPa and 80 MPa, respectively, while the low temperature toughness of -110 ° C. is also better than 70 J, respectively, compared to the comparative example.
- the comparative steel d does not contain W, the strength of the steel was relatively low, and in the case of Comparative Examples 1 and 2, no tempered bainite was formed because water cooling was not performed and air cooling was performed. Yield strength and tensile strength were lower than those of the invention, and low temperature toughness of -110 ° C was also low.
Abstract
Description
강종 | 조성성분(중량%) | ||||||
C | Mn | Si | P | S | Ni | W | |
발명강a | 0.10 | 0.62 | 0.29 | 0.009 | 0.0012 | 3.49 | 0.08 |
발명강b | 0.09 | 0.60 | 0.27 | 0.008 | 0.0010 | 3.45 | 0.11 |
발명강c | 0.10 | 0.65 | 0.28 | 0.010 | 0.0011 | 3.55 | 0.18 |
비교강d | 0.11 | 0.68 | 0.29 | 0.012 | 0.0012 | 3.50 | - |
구분 | 강종 | 가열온도(℃) | 수냉속도(℃/s) | 템퍼링온도(℃) | 템퍼링시간(분) | PWHT온도(℃) | PWHT시간(hr) | 템퍼드 베이나이트 면적분율(%) | YS(Mpa) | TS(Mpa) | -110℃충격인성(J) |
발명예1 | a | 850 | 15.0 | 650 | 50 | 630 | 15 | 60 | 568 | 608 | 256 |
발명예2 | 860 | 8.5 | 650 | 90 | 630 | 20 | 55 | 557 | 602 | 251 | |
발명예3 | b | 850 | 15.0 | 650 | 50 | 630 | 15 | 53 | 558 | 610 | 227 |
발명예4 | 860 | 8.5 | 650 | 90 | 630 | 20 | 50 | 557 | 605 | 233 | |
발명예5 | c | 850 | 15.0 | 650 | 50 | 630 | 15 | 48 | 560 | 615 | 230 |
발명예6 | 850 | 8.5 | 650 | 90 | 630 | 20 | 45 | 551 | 610 | 215 | |
비교예1 | d | 850 | 공냉 | 650 | 50 | 630 | 15 | 0 | 458 | 523 | 155 |
비교예2 | 850 | 공냉 | 650 | 90 | 630 | 20 | 0 | 442 | 516 | 148 |
Claims (10)
- 중량%로, C: 0.07 ~ 0.17%, Si: 0.15 ~ 0.40%, Mn: 0.3 ~ 0.7%, P: 0.012% 이하, S: 0.015%이하, Ni: 3.0 ~ 4.0%, W: 0.03~0.25%, 잔부 Fe 및 불가피한 불순물로 이루어지며, 강 미세조직이 25~80 면적%의 템퍼드 베이나이트와 잔부 템퍼드 마르텐사이트로 이루어진 PWHT 저항성이 우수한 저온용 압력용기 강판.
- 제 1항에 있어서, 상기 강판은 580~640℃구간에서 최대 20시간 동안 PWHT를 실시하여도 인장강도를 600MPa 이상으로 유지하는 것을 특징으로 하는 PWHT 저항성이 우수한 저온용 압력용기 강판.
- 제 1항에 있어서, 상기 강 미세조직은 30~70 면적%의 템퍼드 베이나이트와 잔부 템퍼드 마르텐사이트로 이루어지는 것임을 특징으로 하는 PWHT 저항성이 우수한 저온용 압력용기 강판의 제조방법.
- 제 1항에 있어서, 상기 강판은 580~640℃ 구간에서 최대 20시간 동안 PWHT를 실시하여도 -110℃에서의 샤르피 충격에너지값이 200J 이상인 것을 특징으로 하는 PWHT 저항성이 우수한 저온용 압력용기 강판.
- 중량%로, C: 0.07 ~ 0.17%, Si: 0.15 ~ 0.40%, Mn: 0.3 ~ 0.7%, P: 0.012% 이하, S: 0.015%이하, Ni: 3.0 ~ 4.0%, W: 0.03~0.25%, 잔부 Fe 및 불가피한 불순물로 이루어진 강 슬라브를 1050 ~ 1250℃에서 재가열하는 공정;상기 재가열된 강 슬라브를 열간 압연하고, 800℃ 이상의 온도에서 압연을 종료하여 열연강판을 얻는 열간압연 공정;상기 열간 압연된 강판을 800 ~ 950℃로 가열 후 수냉하는 공정; 및상기 수냉된 강재를 550 ~ 660℃에서 {1.5×t + (10~30)}분 [여기서 t는 강재의 두께(mm)를 의미한다] 동안 템퍼링 처리하는 공정;을포함하는 PWHT 저항성이 우수한 저온용 압력용기 강판의 제조방법.
- 제 5항에 있어서, 상기 템퍼링 공정 이후에, 580~640℃구간에서 최대 20시간 PWHT하는 공정을 추가로 포함하는 PWHT 저항성이 우수한 저온용 압력용기 강판의 제조방법.
- 제 5항에 있어서, 상기 템퍼링 공정으로 얻이진 강 미세조직은 25~80 면적%의 템퍼드 베이나이트와 잔부 템퍼드 마르텐사이트로 이루어지는 것임을 특징으로 하는 PWHT 저항성이 우수한 저온용 압력용기 강판의 제조방법.
- 제 5항에 있어서, 상기 템퍼링 공정으로 얻이진 강 미세조직은 30~70 면적%의 템퍼드 베이나이트와 잔부 템퍼드 마르텐사이트로 이루어지는 것임을 특징으로 하는 PWHT 저항성이 우수한 저온용 압력용기 강판의 제조방법.
- 제 5항에 있어서,상기 열간 압연 공정에서 패스당 압하율은 5 ~ 30%인 것을 특징으로 하는 PWHT 저항성이 우수한 저온용 압력용기 강판의 제조방법.
- 제 5항에 있어서,상기 수냉공정에서 냉각속도는 2.5~30℃/sec인 것을 특징으로 하는 PWHT 저항성이 우수한 저온용 압력용기 강판의 제조방법.
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US16/063,990 US20180371568A1 (en) | 2015-12-22 | 2016-11-03 | Steel plate having excellent pwht resistance for low-temperature pressure vessel and method for manufacturing same |
EP16879157.2A EP3395984B1 (en) | 2015-12-22 | 2016-11-03 | Steel sheet having excellent pwht resistance for low-temperature pressure vessel and method for manufacturing same |
CN201680075744.7A CN108431272B (zh) | 2015-12-22 | 2016-11-03 | 对pwht具有优异抗性的低温压力容器用钢板及其制造方法 |
JP2018532673A JP6700400B2 (ja) | 2015-12-22 | 2016-11-03 | Pwht抵抗性に優れた低温圧力容器用鋼板及びその製造方法 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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KR10-2015-0183528 | 2015-12-22 | ||
KR1020150183528A KR101758497B1 (ko) | 2015-12-22 | 2015-12-22 | Pwht 저항성이 우수한 저온 압력용기용 강판 및 그 제조 방법 |
Publications (2)
Publication Number | Publication Date |
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WO2017111290A1 true WO2017111290A1 (ko) | 2017-06-29 |
WO2017111290A8 WO2017111290A8 (ko) | 2017-12-21 |
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PCT/KR2016/012566 WO2017111290A1 (ko) | 2015-12-22 | 2016-11-03 | Pwht 저항성이 우수한 저온 압력용기용 강판 및 그 제조 방법 |
Country Status (6)
Country | Link |
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US (1) | US20180371568A1 (ko) |
EP (1) | EP3395984B1 (ko) |
JP (1) | JP6700400B2 (ko) |
KR (1) | KR101758497B1 (ko) |
CN (1) | CN108431272B (ko) |
WO (1) | WO2017111290A1 (ko) |
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EP3835448A4 (en) * | 2018-08-07 | 2021-07-07 | Posco | STEEL FOR PRESSURE VESSELS WITH EXCELLENT SURFACE QUALITY AND IMPACT RESISTANCE AND THE PROCESS FOR ITS MANUFACTURING |
EP3872208A4 (en) * | 2018-10-26 | 2021-12-08 | Posco | STEEL PLATE FOR PRESSURE VESSELS WITH EXCELLENT LOW-TEMPERATURE TOUGHNESS AND EXTENSION RESISTANCE, AND THE PROCESS FOR THEIR MANUFACTURING |
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KR101998991B1 (ko) * | 2017-12-15 | 2019-07-10 | 주식회사 포스코 | 인장강도 및 저온충격인성이 우수한 압력용기용 강판 및 그 제조방법 |
KR102200225B1 (ko) * | 2019-09-03 | 2021-01-07 | 주식회사 포스코 | 극저온 횡팽창이 우수한 압력용기용 강판 및 그 제조 방법 |
KR102280641B1 (ko) * | 2019-10-22 | 2021-07-22 | 주식회사 포스코 | 고온 용접후열처리 저항성이 우수한 압력용기용 강판 및 그 제조방법 |
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CN113088807A (zh) * | 2021-02-25 | 2021-07-09 | 舞阳钢铁有限责任公司 | 一种高韧性低温压力容器用钢板及其生产方法 |
CN113549815B (zh) * | 2021-06-25 | 2022-09-16 | 鞍钢股份有限公司 | 一种低温用低合金压力容器用钢板及生产方法 |
CN115341152A (zh) * | 2022-08-31 | 2022-11-15 | 鞍钢股份有限公司 | 一种节镍型-100℃低温钢及其制造方法 |
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- 2016-11-03 CN CN201680075744.7A patent/CN108431272B/zh active Active
- 2016-11-03 JP JP2018532673A patent/JP6700400B2/ja active Active
- 2016-11-03 US US16/063,990 patent/US20180371568A1/en not_active Abandoned
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EP3835448A4 (en) * | 2018-08-07 | 2021-07-07 | Posco | STEEL FOR PRESSURE VESSELS WITH EXCELLENT SURFACE QUALITY AND IMPACT RESISTANCE AND THE PROCESS FOR ITS MANUFACTURING |
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EP3872208A4 (en) * | 2018-10-26 | 2021-12-08 | Posco | STEEL PLATE FOR PRESSURE VESSELS WITH EXCELLENT LOW-TEMPERATURE TOUGHNESS AND EXTENSION RESISTANCE, AND THE PROCESS FOR THEIR MANUFACTURING |
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Also Published As
Publication number | Publication date |
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JP6700400B2 (ja) | 2020-05-27 |
KR20170075050A (ko) | 2017-07-03 |
EP3395984A1 (en) | 2018-10-31 |
JP2019505672A (ja) | 2019-02-28 |
WO2017111290A8 (ko) | 2017-12-21 |
CN108431272A (zh) | 2018-08-21 |
EP3395984B1 (en) | 2020-01-29 |
CN108431272B (zh) | 2020-07-28 |
US20180371568A1 (en) | 2018-12-27 |
EP3395984A4 (en) | 2018-12-26 |
KR101758497B1 (ko) | 2017-07-27 |
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