WO2022070873A1 - Tôle d'acier - Google Patents

Tôle d'acier Download PDF

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Publication number
WO2022070873A1
WO2022070873A1 PCT/JP2021/033646 JP2021033646W WO2022070873A1 WO 2022070873 A1 WO2022070873 A1 WO 2022070873A1 JP 2021033646 W JP2021033646 W JP 2021033646W WO 2022070873 A1 WO2022070873 A1 WO 2022070873A1
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WIPO (PCT)
Prior art keywords
less
content
toughness
steel sheet
affected zone
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PCT/JP2021/033646
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English (en)
Japanese (ja)
Inventor
亮 荒尾
圭治 植田
方成 友澤
孝一 中島
Original Assignee
Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to BR112023004211A priority Critical patent/BR112023004211A2/pt
Priority to KR1020237008995A priority patent/KR20230051276A/ko
Priority to CN202180062217.3A priority patent/CN116171335B/zh
Priority to JP2021576659A priority patent/JP7272471B2/ja
Publication of WO2022070873A1 publication Critical patent/WO2022070873A1/fr

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Classifications

    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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

  • the present invention relates to steel materials used for various steel structures in the fields of ships, construction, civil engineering, etc., and is particularly excellent in welding even when large heat input welding exceeding 20.0 kJ / mm is performed. Heat-affected zone Regarding steel sheets with toughness.
  • HAZ weld heat-affected zone
  • various steels for high heat input welding have been proposed. For example, a technique of finely dispersing TiN in steel to suppress the coarsening of austenite grains in the weld heat-affected zone and a technique of using it as a ferrite transformation nucleus in the weld heat-affected zone have been put into practical use.
  • Patent Document 1 among the Ti oxides that are difficult to dissolve even in the high temperature region of the weld heat affected zone, TiOx (however, x: 0.65 to 1.3) having a particle size of 5 ⁇ m or less is finely dispersed in the steel.
  • a technique has been proposed for improving the toughness of the weld heat-affected zone by using it as a core for forming acicular ferrite in the weld heat-affected zone.
  • B, N and sol. A technique has been proposed in which the amount of Al is adjusted to positively precipitate BN that miniaturizes the weld heat-affected zone to improve the toughness of the weld heat-affected zone.
  • Patent Document 3 the amount of Ti—B—N in the component composition is adjusted so that the HAZ toughness is in the high toughness region, and Ca or Ce is further added to impart the toughness improving effect by controlling the morphology of inclusions.
  • Patent Document 4 also proposes a technique for improving the toughness of a large heat input weld by adding REM that forms stable sulfur / oxide even in a weld bond portion with a low N-low Ti system as the component composition. Has been done.
  • Patent Document 5 Ca-based non-metal inclusions that become transformation nuclei and promote ferrite transformation in the weld heat-affected zone are finely dispersed in steel by appropriately controlling the Ca, O, and S contents.
  • a technique for improving the toughness of a weld heat-affected zone in a large heat-affected zone exceeding 20.0 kJ / mm is disclosed.
  • the present invention has been made in view of the above circumstances, and an object of the present invention is to provide a steel sheet having excellent toughness in a large heat-affected zone where the welding heat input is 20.0 kJ / mm or more.
  • the inventors conducted various studies to solve the above problems and obtained the following findings.
  • the present invention by controlling the amounts of S, Ca and O in addition to controlling the precipitate of TiN, the coarsening of the structure in the weld heat-affected zone is suppressed, and the excellent toughness in the weld heat-affected zone is suppressed. Can be obtained.
  • the present invention has been completed by further studying based on the above-mentioned findings, and the gist thereof is as follows.
  • the composition of the components is mass%. C: 0.030 to 0.120%, Si: 0.01-0.15%, Mn: 0.80 to 2.00%, P: 0.020% or less, S: 0.0005 to 0.0050%, Al: 0.005 to 0.100%, Ti: 0.005 to 0.030%, N: 0.0030-0.0080%, Ca: 0.0005-0.0030%, O: Contains 0.0040% or less, The rest are Fe and unavoidable impurities, Further, a steel sheet containing S, Ca, and O so as to satisfy the following formula (1), and the precipitate having a diameter equivalent to a circle exceeding 0.1 ⁇ m is 40% or more by mass ratio.
  • each element symbol indicates the content (mass%) of each element.
  • the composition of the components is further increased by mass%.
  • the composition of the components is further increased by mass%.
  • a steel sheet having excellent toughness in a large heat-affected zone where the welding heat input is 20.0 kJ / mm or more can be obtained, which is extremely useful in industry.
  • C 0.030-0.120%
  • the C content is preferably 0.040% or more, more preferably 0.050% or more, and further preferably 0.060% or more.
  • MA island-shaped martensite
  • the C content is preferably 0.100% or less, more preferably 0.090% or less, and further preferably 0.085% or less.
  • Si 0.01-0.15%
  • Si is an element added as a deoxidizing agent when melting steel, and must be contained in an amount of 0.01% or more. Therefore, the Si content is 0.01% or more.
  • the Si content is preferably 0.02% or more, more preferably 0.03% or more, still more preferably 0.04% or more, and most preferably 0.06% or more.
  • the Si content is set to 0.15% or less.
  • the Si content is preferably 0.13% or less, more preferably 0.10% or less, still more preferably 0.09% or less.
  • Mn 0.80 to 2.00%
  • the Mn content of Mn is 0.80% or more in order to secure the strength of the base material.
  • the Mn content is preferably 1.00% or more, more preferably 1.20% or more, still more preferably 1.40% or more, and most preferably 1.50% or more.
  • the Mn content exceeds 2.00%, the toughness of HAZ is significantly deteriorated, so the Mn content is set to 2.00% or less.
  • the Mn content is preferably 1.90% or less, more preferably 1.85% or less, still more preferably 1.80% or less, and most preferably 1.70% or less.
  • P 0.020% or less P promotes MA formation in HAZ near the bond portion and greatly reduces toughness, so the P content was set to 0.020% or less.
  • the P content is preferably 0.015% or less, more preferably 0.012% or less.
  • the lower limit of the P content is not particularly limited. However, since excessive de-P causes an increase in cost, the P content is preferably 0.002% or more.
  • S 0.0005 to 0.0050%
  • S is an element required to form MnS or CaS, which acts as a nucleation site for ferrite. Therefore, the S content is set to 0.0005% or more.
  • the S content is preferably 0.0010% or more, more preferably 0.0015% or more.
  • the toughness of the base metal is lowered, so the S content is set to 0.0050% or less.
  • the S content is preferably 0.0040% or less, more preferably 0.0035% or less, still more preferably 0.0030% or less.
  • Al 0.005 to 0.100%
  • Al is an element contained for deoxidizing steel, and the Al content is 0.005% or more.
  • the Al content is preferably 0.010% or more, more preferably 0.020% or more, and further preferably 0.030% or more. However, if it is contained in an amount of more than 0.100%, not only the toughness of the base metal but also the toughness of the weld metal is lowered. Therefore, the Al content is set to 0.100% or less.
  • the Al content is preferably 0.085% or less, more preferably 0.070% or less, and further preferably 0.065% or less.
  • Ti 0.005 to 0.030%
  • TiN becomes TiN during solidification of the molten steel and precipitates in the base metal, and contributes to the improvement of the toughness of the base metal by suppressing the coarsening of austenite grains.
  • TiN suppresses the coarseness of the structure in the heat-affected zone of the weld and becomes a transformation nucleus of ferrite, which contributes to high toughness.
  • the content of 0.005% or more is required. Therefore, the Ti content is set to 0.005% or more.
  • the Ti content is preferably 0.008% or more, more preferably 0.011% or more, and further preferably 0.015% or more.
  • the Ti content is set to 0.030% or less.
  • the Ti content is preferably 0.027% or less, more preferably 0.024% or less, still more preferably 0.020% or less.
  • N 0.0030-0.0080% Since N produces TiN and contributes to the improvement of toughness, the N content is set to 0.0030% or more.
  • the N content is preferably 0.0035% or more, more preferably 0.0040% or more.
  • the N content is set to 0.0080% or less.
  • the N content is preferably 0.0070% or less, more preferably 0.0065% or less, still more preferably 0.0070% or less.
  • Ca 0.0005-0.0030%
  • Ca has the effect of fixing S and improving toughness.
  • the Ca content is 0.0005% or more.
  • the Ca content is preferably 0.0010% or more, more preferably 0.0015% or more.
  • the Ca content is set to 0.0030% or less.
  • the Ca content is preferably 0.0025% or less, more preferably 0.0020% or less.
  • the O content is 0.0040% or less.
  • the O content is preferably 0.0030% or less, more preferably 0.0025% or less.
  • the lower limit of the O content is not particularly limited. However, since excessive reduction of oxygen content leads to an increase in cost, the O content is preferably 0.0003% or more.
  • the A value is set to more than 0.
  • the A value is preferably 0.1 or more, more preferably 0.2 or more, and further preferably 0.3 or more.
  • S is mostly fixed by Ca
  • MnS which is a ferrite-forming nucleus
  • the A value is set to less than 1.
  • the A value is preferably 0.8 or less, more preferably 0.7 or less.
  • the above is the basic composition of the present invention, and the balance is Fe and unavoidable impurities.
  • At least one selected from Cu, Ni, Cr, Mo, V and Nb is contained as a selective element in the following range for the purpose of further improving the strength. Can be done.
  • Cu 1.00% or less
  • Cu is an element effective for increasing the strength of steel sheets, but if added in excess, it may promote cracking of cast steel ingots and reduce the toughness of steel sheets. Therefore, when Cu is contained, the Cu content is set to 1.00% or less.
  • the Cu content is preferably 0.50% or less, more preferably 0.30% or less.
  • the Cu content is preferably 0.03% or more.
  • the Cu content is more preferably 0.04% or more.
  • Ni 1.50% or less Ni improves the toughness of the steel sheet and also increases the strength, but excessive addition reduces the toughness of the base metal and HAZ, and also puts pressure on the manufacturing cost. Therefore, when Ni is contained, the Ni content is 1.50% or less.
  • the Ni content is preferably 1.0% or less, more preferably 0.50% or less, still more preferably 0.30% or less.
  • the Ni content is preferably 0.03% or more.
  • the Ni content is more preferably 0.04% or more.
  • Cr 1.00% or less Cr is an element advantageous for increasing the strength of the steel sheet, but excessive content reduces the toughness of the base material and HAZ. Therefore, when Cr is contained, the Cr content is set to 1.00% or less.
  • the Cr content is preferably 0.80% or less, more preferably 0.50% or less, still more preferably 0.30% or less.
  • the Cr content is preferably 0.02% or more.
  • the Cr content is more preferably 0.03% or more.
  • Mo 0.50% or less
  • Mo is an element advantageous for increasing the strength of the steel sheet, but excessive content reduces the toughness of the base material and HAZ. Therefore, when Mo is contained, the Mo content is 0.50% or less.
  • the Mo content is preferably 0.40% or less, more preferably 0.30% or less, and further preferably 0.20% or less.
  • the Mo content is preferably 0.003% or more.
  • the Mo content is more preferably 0.004% or more.
  • V 0.50% or less
  • V is an element advantageous for increasing the strength of the steel sheet, but excessive content reduces the toughness of the base material and HAZ. Therefore, when V is contained, the V content is set to 0.50% or less.
  • the V content is preferably 0.40% or less, more preferably 0.30% or less, still more preferably 0.20% or less.
  • the V content is preferably 0.003% or more.
  • the V content is more preferably 0.004% or more.
  • Nb 0.05% or less
  • the Nb content is set to 0.05% or less.
  • the Nb content is preferably 0.04% or less, more preferably 0.03% or less, and further preferably 0.02% or less.
  • the Nb content is preferably 0.002% or more.
  • the Nb content is more preferably 0.003% or more.
  • the steel material of the present invention can further contain at least one selected from B, Mg, Zr and REM as a selective element in the following range in addition to the above components.
  • B 0.0025% or less B produces BN in the weld heat affected zone to reduce the solid solution N, and also becomes a ferrite transformation nucleus to generate ferrite to improve toughness.
  • the B content is 0.0003% or more.
  • the B content is preferably 0.0005% or more, more preferably 0.0008% or more.
  • the toughness of the base metal and HAZ is lowered. Therefore, when B is contained, the B content is 0.0025% or less.
  • the B content is preferably 0.0020% or less, more preferably 0.0018% or less.
  • Mg, Zr and REM are all elements having a toughness improving effect by dispersing oxides.
  • the Mg content should be 0.0005% or more, and the Zr content and REM content should be 0.0010% or more, respectively.
  • the Mg content is 0.0010% or more, and the Zr content and the REM content are 0.0015% or more, respectively.
  • the Mg content is 0.0050% or less, and the Zr content and the REM content are 0.0200% or less, respectively.
  • the Mg content is 0.0030% or less, and the Zr content and the REM content are 0.01% or less, respectively.
  • TiN precipitates those having a diameter equivalent to a circle and exceeding 0.1 ⁇ m are 40% or more by mass.
  • the TiN precipitates in the steel sheet 20.0 kJ / mm by setting the mass ratio (hereinafter, also referred to as P value) of the precipitates having a diameter equivalent to a circle exceeding 0.1 ⁇ m to 40% or more of the total amount of precipitates.
  • P value the mass ratio of the precipitates having a diameter equivalent to a circle exceeding 0.1 ⁇ m to 40% or more of the total amount of precipitates.
  • the mass ratio of the precipitates having a diameter equivalent to a circle of more than 0.1 ⁇ m out of the total amount of the precipitates of TiN is 40% or more.
  • those having a circle-equivalent diameter of more than 0.1 ⁇ m have a mass ratio of preferably 45% or more, more preferably 50% or more.
  • the mass ratio of the precipitate having a large size (diameter equivalent to a circle) is excessively increased, the precipitate may become coarse and become a starting point of fracture.
  • Precipitates having a diameter of more than 0.1 ⁇ m are preferably 98% or less in terms of mass ratio.
  • those having a diameter equivalent to a circle and exceeding 0.1 ⁇ m are more preferably 98% or less, and further preferably 95% or less in terms of mass ratio. Further, it is desirable to reduce the amount of precipitates having a diameter equivalent to a circle exceeding 2.0 ⁇ m as much as possible because they may be the starting point of brittle fracture.
  • the proportion of precipitates exceeding 0.1 ⁇ m in the equivalent circle diameter for example, by adjusting the average cooling rate from 1450 ° C to 1300 ° C at the time of casting to 0.5 ° C / sec or less. Due to the Ostwald growth after precipitation, the mass ratio of the precipitate having a diameter equivalent to a circle and exceeding 0.1 ⁇ m can be set to 40% or more.
  • the cooling rate is higher than 0.5 ° C./sec, the proportion of precipitates with a diameter equivalent to a circle of 0.1 ⁇ m or less increases, and TiN is added during large heat input welding exceeding 20.0 kJ / mm. Most of it is dissolved and the subsequent grain growth cannot be sufficiently suppressed.
  • the steel sheet of the present invention can be manufactured by a conventionally known method for a manufacturing method other than the above-mentioned average cooling rate at the time of casting.
  • steel smelted in a converter or electric furnace is secondarily refined by RH degassing, etc. to adjust the steel composition to the above-mentioned appropriate range, and then continuously cast or ingot-lumped to make steel such as slabs. Use as a material.
  • the average cooling rate may be controlled during continuous casting or ingot formation.
  • the steel material is reheated and hot-rolled to obtain a steel plate of a desired size, and then allowed to cool, or after the hot-rolling, accelerated cooling, direct quenching-tempering, and reheating quenching.
  • -It can be manufactured through processes such as tempering and reheating quenching-tempering.
  • the plate thickness range obtained by the present invention is 9 mm to 50 mm.
  • the steel sheet of the present invention has excellent toughness in a large heat-affected zone where the welding heat input is 20.0 kJ / mm or more. Specifically, when a Charpy impact test at -40 ° C is performed in a large heat-affected zone where the welding heat input is 20.0 kJ / mm or more, the impact absorption value (vE- 40 ° C ) exceeds 100 J. Is obtained.
  • Steels 1 to 18 were melted and cast at the average cooling rate shown in Table 2 to form a steel ingot, which was then hot rolled to obtain a steel sheet having a thickness of 50 mm.
  • the obtained steel sheet was quantified for TiN precipitates by using the QUANPASS method (see JP-A-2010-12778). Specifically, a 10 mm square plate-shaped metal sample is cut out from the 1/4 position of the plate thickness of the steel plate, the metal sample is electrolyzed in an electrolytic solution, precipitates and the like are extracted, and filtering and quantitative analysis are performed by size. A test was conducted to repeat what was done. From the quantitative results, the mass ratio of TiN precipitates having a diameter equivalent to a circle and having a size exceeding 0.1 ⁇ m among all TiN precipitates was defined as the P value.
  • the reproducible heat cycle condition corresponds to the heat history of the bond portion in the case of electrogas welding with an input heat amount of 30.0 kJ / mm simulating 1-pass welding with a plate thickness of 50 mm.
  • Table 2 also shows the test results of the average cooling rate from 1450 ° C to 1300 ° C, the P value, and the toughness of the weld heat-affected zone during casting.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Polishing Bodies And Polishing Tools (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

La présente invention a pour but de fournir une tôle d'acier présentant une excellente ténacité dans les parties affectées par la chaleur où il existe une importante entrée de chaleur pendant le soudage jusqu'à 20,0 kJ/mm ou plus de l'apport de chaleur de soudage.　La présente tôle d'acier a une composition comprenant, en pourcentage en masse, de 0,030 à 0,120 % de C, 0,01 à 0,15 % de Si, de 0,80 à 2,00 % de Mn, pas plus de 0,020 % de P, de 0,0005 à 0,0050 % de S, de 0,005 à 0,100 % de Al, de 0,005 à 0,030 % de Ti, de 0,0030 à 0,0080 % de N, de 0,0005 à 0,0030 % de Ca, et pas plus de 0,0040 % de O, le reste comprenant Fe et des impuretés inévitables. Les quantités contenues de S, Ca et O satisfont la formule (1). Parmi les précipités de TiN, la proportion massique de précipités ayant un diamètre de cercle équivalent supérieur à 0,1 μm est de 40 % ou plus. (1) : 0 < (Ca - (0,18 + 130 × Ca) × O) / 1,25 / S < 1 (les symboles d'éléments indiquant les quantités contenues d'éléments respectifs).
PCT/JP2021/033646 2020-09-30 2021-09-14 Tôle d'acier WO2022070873A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
BR112023004211A BR112023004211A2 (pt) 2020-09-30 2021-09-14 Placa de aço
KR1020237008995A KR20230051276A (ko) 2020-09-30 2021-09-14 강판
CN202180062217.3A CN116171335B (zh) 2020-09-30 2021-09-14 钢板
JP2021576659A JP7272471B2 (ja) 2020-09-30 2021-09-14 鋼板

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JP2020165378 2020-09-30
JP2020-165378 2020-09-30

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KR (1) KR20230051276A (fr)
CN (1) CN116171335B (fr)
BR (1) BR112023004211A2 (fr)
TW (1) TWI806170B (fr)
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JPH05279789A (ja) * 1992-04-03 1993-10-26 Nippon Steel Corp 低温靱性の優れた超大入熱溶接構造用鋼板
JP2010111924A (ja) * 2008-11-07 2010-05-20 Jfe Steel Corp 大入熱溶接部靭性に優れた建築用低降伏比鋼板およびその製造方法
JP2010174314A (ja) * 2009-01-28 2010-08-12 Kobe Steel Ltd 溶接熱影響部の靭性に優れた鋼材
JP2013060631A (ja) * 2011-09-13 2013-04-04 Kobe Steel Ltd 母材および溶接熱影響部の靭性に優れた鋼材、およびその製造方法
JP2014029019A (ja) * 2012-07-03 2014-02-13 Jfe Steel Corp 脆性亀裂伝播停止特性に優れた大入熱溶接用鋼板の製造方法

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