EP3395984A1 - Stahlblech mit ausgezeichneter pwht-beständigkeit für niedertemperaturdruckbehälter und verfahren zur herstellung - Google Patents

Stahlblech mit ausgezeichneter pwht-beständigkeit für niedertemperaturdruckbehälter und verfahren zur herstellung Download PDF

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Publication number
EP3395984A1
EP3395984A1 EP16879157.2A EP16879157A EP3395984A1 EP 3395984 A1 EP3395984 A1 EP 3395984A1 EP 16879157 A EP16879157 A EP 16879157A EP 3395984 A1 EP3395984 A1 EP 3395984A1
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EP
European Patent Office
Prior art keywords
steel
steel plate
balance
temperature
pwht
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Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP16879157.2A
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English (en)
French (fr)
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EP3395984B1 (de
EP3395984A4 (de
Inventor
Soon-Taik Hong
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Posco Holdings Inc
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Posco Co Ltd
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Publication of EP3395984A4 publication Critical patent/EP3395984A4/de
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Classifications

    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • 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
    • 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
    • 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")
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • 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
    • 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
    • C21D8/0226—Hot rolling
    • 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
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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
    • 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 disclosure relates to a thick steel plate used in a low-temperature pressure vessel, a ship, a storage tank, a structural steel, and the like, and a method for manufacturing the same, and more particularly, to a steel plate having excellent PWHT resistance and low-temperature toughness for a low-temperature pressure vessel in which a tensile strength is 600 MPa or more, and a method for manufacturing the same.
  • a mixed structure including ferrite, a martensite structure, and a bainite structure, or a nearly single-phase structure mainly consisting of bainite and ferrite, or the like, is widely known.
  • the high strength hot rolled steel material manufactured through a general normalizing treatment may have a mixed structure of ferrite and pearlite.
  • a PWHT treatment is performed in a subsequent process of a steel material having the structure, a carbide is formed along a grain boundary, and thus, strength and toughness of the steel material are lowered, failing to guarantee physical properties required for PWHT.
  • An example of the conventional technique regarding this is disclosed in Korean Patent Laid-Open Publication No. 2012-0011289 .
  • the Korean Patent Laid-Open Publication suggests a high strength steel material for LPG having a strength of 500 MPa or more including: in terms of wt%, 0.08-0.15% of C, 0.2-0.3% of Si, 0.5-1.2% of Mn, 0.01-0.02% of P, 0.004-0.006% of S, more than 0%-0.01% or less of Ti, 0.05-0.1% of Mo, 3.0-5.0% of Ni, and a balance of Fe and inevitable impurities, characterized in that Ni and Mo are added to the steel composition component.
  • Patent Document 1 Korean Patent Laid-Open Publication No. 2012-0011289
  • An aspect of the present disclosure is to provide a steel plate having excellent PWHT resistance for an extended period of time and high strength of a low-temperature pressure vessel by controlling a steel composition, and cooling and heat treatment processes to form a microstructure into a mixed structure of tempered bainite and tempered martensite, and a method for manufacturing the same.
  • a steel plate having excellent PWHT resistance for a low-temperature pressure vessel includes: in terms of wt%, 0.07-0.17% of C, 0.15-0.40% of Si, 0.3-0.7% of Mn, 0.012% or less of P, 0.015% or less of S, 3.0-4.0% of Ni, 0.03-0.25% of W, and a balance of Fe and inevitable impurities, wherein the steel plate has a microstructure including 25-80 area% of tempered bainite and a balance of tempered martensite.
  • the steel plate may maintain tensile strength at 600 MPa or more even when the steel plate is subjected to PWHT for a maximum of 20 hours at 580-640°C.
  • the steel plate may have a Charpy impact energy value of 200J or more at -110°C even when the steel plate is subjected to PWHT for a maximum of 20 hours at 580-640°C.
  • a method for manufacturing a steel plate having excellent PWHT resistance for a low-temperature pressure vessel includes:
  • the method may further include: a PWHT process for a maximum of 20 hours at 580-640°C after the tempering.
  • a steel microstructure obtained by the tempering may have 25-80 area fraction % of tempered bainite and a balance of tempered martensite.
  • a steel plate having excellent PWHT resistance for a low-temperature pressure vessel, stably usable at a low temperature of about -110°C while satisfying a tensile strength of 600 MPa or more, may be effective provided.
  • the steel plate of the present disclosure includes, in terms of wt%, 0.07-0.17% of C, 0.15-0.40% of Si, 0.3-0.7% of Mn, 0.012% or less of P, 0.015% or less of S, 3.0-4.0% of Ni, 0.03-0.25% of W, and a balance of Fe and inevitable impurities, and specific steel composition components and reasons for limiting the components are as follows.
  • C is preferably limited to a content of 0.07-0.17%.
  • the content is less than 0.07%, a self-strength of a matrix may be deteriorated.
  • the content is more than 0.17%, weldability of the steel plate may be greatly deteriorated.
  • Si is a component to be added for a deoxidation effect, a solid-solution strengthening effect and an impact transition temperature increasing effect, and is preferably added in a content of 0.15% or more in order to achieve these additive effects.
  • the content of Si is more than 0.40%, the weldability is lowered and an oxide film is excessively formed on a surface of the steel plate, such that the content thereof is preferably limited to 0.15-0.40%.
  • Mn forms MnS, a non-metallic inclusion elongated together with S, to lower a room temperature elongation and a low-temperature toughness, such that a content of Mn is preferably controlled to be 0.7% or less.
  • a content of Mn is preferably controlled to be 0.7% or less.
  • due to characteristics of the components of the present disclosure when the content of Mn is less than 0.3%, it is difficult to ensure adequate strength, such that an added content of Mn is preferably limited to 0.3-0.7%.
  • P is an element that deteriorates low-temperature toughness, such that a content of P is preferably suppressed as much as possible.
  • the content of P may be controlled within a range of 0.012% or less.
  • S is also an element that adversely affects low-temperature toughness together with P, but as similar to P, excessive cost may be required to remove S in a steelmaking process, such that the content of S may be controlled within a range of 0.015% or less.
  • Ni is the most effective element for improving low-temperature toughness. However, when an added content of Ni is less than 3.0%, low-temperature toughness may be deteriorated. When the added content is more than 4.0%, production cost may be increased. Therefore, Ni is preferably added within a range of 3.0 to 4.0%.
  • W is an important element that is solid-solutionized in austenite to increase curing ability of austenite and precipitates into a carbide (W 2 C) matched with a matrix to increase a strength of the steel.
  • W is added in a content of less than 0.03%, an addition effect may not be expected.
  • W is added in a content of more than 0.25%, a coarse precipitate may be formed during a casting process to deteriorate low-temperature toughness, such that the content of W is preferably limited to 0.03-0.25%.
  • the steel plate of the present disclosure may have a microstructure including 25-80 area% of tempered bainite and a balance of tempered martensite.
  • a fraction of the tempered bainite is less than 25%, an amount of the tempered martensite may be excessive, and low-temperature toughness of the steel plate may be deteriorated.
  • the fraction of the tempered bainite is more than 80%, it may be difficult to secure desired strength of the steel plate.
  • the microstructure may include 30-70 area fraction% of tempered bainite and a balance of tempered martensite.
  • the steel plate having the above-described steel composition components and microstructure may effectively maintain tensile strength at 600 MPa or more and have excellent low-temperature toughness even when the steel plate is subjected to PWHT for a maximum of 20 hours at 580-640°C.
  • the method for the steel plate of the present disclosure includes: reheating a steel slab having the above-described steel composition components at 1050-1250°C; hot rolling the reheated steel slab and terminating the rolling at a temperature of 800°C or more to obtain a hot rolled steel plate; heating the hot rolled steel plate to 800-950°C, followed by water cooling at a cooling rate of 2.5-30°C/sec; and tempering the water cooled steel material at 550-660°C for ⁇ 1.5 ⁇ t + (10-30) ⁇ minutes [wherein t is a thickness (mm) of the steel material] .
  • the steel slab having the steel composition component is reheated at 1050-1250°C.
  • a reheating temperature is less than 1050°C, a solute atom may be difficult to be solid-solutionized, and when the reheating temperature is more than 1250°C, an austenite crystal grain size may be excessively coarse to lower physical properties of the steel plate.
  • the reheated steel slab may be hot rolled.
  • the reheated steel slab may be hot rolled, and the rolling may be terminated at a temperature of 800°C or more.
  • a hot rolling temperature is less than 800°C, hot deformation resistance may increase at the time of rolling, which may result in a load on a rolling mill.
  • a reduction rate per pass in the hot rolling is preferably 5-30%.
  • the hot rolled steel plate may be heated at 800-950°C and then water cooled at a cooling rate of 2.5-30°C/sec.
  • a heating temperature is less than 800°C, an alloy component may be difficult to be sufficiently solid-solutionized, and when the heating temperature is more than 950°C, crystal grains may be coarsened, such that the toughness may be deteriorated.
  • the cooling rate is less than 2.5°C/sec, the martensite structure may not be obtained.
  • the cooling rate is more than 30°C/sec, since a large amount of cooling water may be required, there is an economic burden of requiring additional cooling equipment, such that the cooling rate is preferably limited to 2.5-30°C/sec.
  • the water cooled steel plate may be tempered.
  • the water cooled steel plate may be tempered at 550-660°C for ⁇ 1.5 ⁇ t + (10-30) ⁇ minutes [wherein t is a thickness (mm) of the steel material] .
  • a tempering temperature is less than 550°C, the toughness may be deteriorated by excessive strength.
  • the tempering temperature is more than 660°C, strength may be excessively deteriorated.
  • a tempering time may be determined to ⁇ 1.5 ⁇ t + (10-30) ⁇ minutes [wherein t is a thickness (mm) of the steel material], and a specific reason for the limitation is as follows.
  • the tempering time when the tempering time is shorter than the above criteria, the tempered martensite structure may be difficult to be obtained. On the other hand, when the tempering time is longer than the above criteria, overall productivity may be damaged.
  • the steel microstructure including 25-80 area% of tempered bainite and a balance of tempered martensite may be obtained.
  • the microstructure may include 30-70 area fraction% of tempered bainite and a balance of tempered martensite.
  • PWHT heat treatment may be performed on the tempered steel plate to remove stress of a welded portion after welding for manufacturing a pressure vessel.
  • a PWHT process for a maximum of 20 hours at 580-640°C may be further included.
  • a PWHT temperature is less than 580°C, it may be difficult to remove residual stress from the welded portion, or the like, and when the PWHT temperature is more than 640°C, strength of the steel material may be significantly lowered. Further, when the PWHT time is more than 20 hours, strength may be excessively deteriorated.
  • the hot rolled steel plates were heated at an austenitization temperature and water cooled under conditions shown in Table 2 below, and subsequently, tempered at temperature and time shown in Table 2 below.
  • the tempered steel plates were also subjected to PWHT treatment under the conditions shown in Table 2 below.
  • the PWHT-treated steel plates were evaluated for yield strength, tensile strength and low temperature toughness, and results thereof are also shown in Table 2 below. Meanwhile, in Table 2 below, the low temperature toughness is a result of evaluating a specimen having V notch at -110°C with the Charpy impact energy value obtained by performing the Charpy impact test.

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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)
  • Heat Treatment Of Articles (AREA)
EP16879157.2A 2015-12-22 2016-11-03 Stahlblech mit ausgezeichneter pwht-beständigkeit für niedertemperaturdruckbehälter und verfahren zur herstellung Active EP3395984B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020150183528A KR101758497B1 (ko) 2015-12-22 2015-12-22 Pwht 저항성이 우수한 저온 압력용기용 강판 및 그 제조 방법
PCT/KR2016/012566 WO2017111290A1 (ko) 2015-12-22 2016-11-03 Pwht 저항성이 우수한 저온 압력용기용 강판 및 그 제조 방법

Publications (3)

Publication Number Publication Date
EP3395984A1 true EP3395984A1 (de) 2018-10-31
EP3395984A4 EP3395984A4 (de) 2018-12-26
EP3395984B1 EP3395984B1 (de) 2020-01-29

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EP16879157.2A Active EP3395984B1 (de) 2015-12-22 2016-11-03 Stahlblech mit ausgezeichneter pwht-beständigkeit für niedertemperaturdruckbehälter und verfahren zur herstellung

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Country Link
US (1) US20180371568A1 (de)
EP (1) EP3395984B1 (de)
JP (1) JP6700400B2 (de)
KR (1) KR101758497B1 (de)
CN (1) CN108431272B (de)
WO (1) WO2017111290A1 (de)

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KR102280641B1 (ko) * 2019-10-22 2021-07-22 주식회사 포스코 고온 용접후열처리 저항성이 우수한 압력용기용 강판 및 그 제조방법
CN112626417A (zh) * 2020-12-14 2021-04-09 南阳汉冶特钢有限公司 一种低成本690MPa级低温抗震钢的生产方法
KR102443670B1 (ko) * 2020-12-16 2022-09-20 주식회사 포스코 고온 pwht 저항성이 우수한 압력용기용 강판 및 그 제조방법
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
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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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WO2017111290A1 (ko) 2017-06-29
US20180371568A1 (en) 2018-12-27
CN108431272A (zh) 2018-08-21
EP3395984B1 (de) 2020-01-29
CN108431272B (zh) 2020-07-28
WO2017111290A8 (ko) 2017-12-21
JP2019505672A (ja) 2019-02-28
EP3395984A4 (de) 2018-12-26
KR101758497B1 (ko) 2017-07-27
JP6700400B2 (ja) 2020-05-27
KR20170075050A (ko) 2017-07-03

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