EP1533392B1 - Stahlprodukt zum schweissen mit hohem wärmeeintrag und verfahren zu seiner herstellung - Google Patents

Stahlprodukt zum schweissen mit hohem wärmeeintrag und verfahren zu seiner herstellung Download PDF

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Publication number
EP1533392B1
EP1533392B1 EP02763002.9A EP02763002A EP1533392B1 EP 1533392 B1 EP1533392 B1 EP 1533392B1 EP 02763002 A EP02763002 A EP 02763002A EP 1533392 B1 EP1533392 B1 EP 1533392B1
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Prior art keywords
mass
steel
toughness
weld
content
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French (fr)
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EP1533392A4 (de
EP1533392A1 (de
Inventor
Kenji c/o Intellectual Property Dept. OI
Katsuyuki c/o Intellectual Property Dpt ICHIMIYA
Mitsuhiro c/o Intellectual Property Dept. OKATSU
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • 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

Definitions

  • the present invention relates to steels used for various structures such as those in the fields of shipbuilding, construction, and civil engineering. More specifically, the present invention relates to steels suitably usable for high heat input welding with a heat input exceeding 400 kJ/cm.
  • steels used in the fields of shipbuilding, construction, and civil engineering are processed by welding to fabricate structures having desired shapes.
  • the individual steels are required not only to exhibit a high parent-metal toughness as a matter of course but also to exhibit high weld-zone toughness.
  • high-efficiency high heat input welding techniques such as a submerged arc welding, an electrogas welding, and an electroslag welding, are employed.
  • steels exhibiting high weld-zone toughness need to be used for the weld-fabrication using the high heat input welding.
  • the JP-A-2 267241 discloses a steel for a line pipe having excellent hydrogen induced cracking resistance and sulfide stress corrosion cracking resistance.
  • a technique that has already been put into practical use employs a method of suppressing the coarsening of austenite grains according to fine dispersion of TiN and actions of TiN serving as a ferrite transformation nucleus.
  • techniques have been developed for dispersing oxides of Ti ( Japanese Unexamined Patent Application Publication No. 57-51243 ) and for combining ferrite nucleation abilities BN ( Japanese Unexamined Patent Application Publication No. 62-170459 ).
  • known techniques include a technique in which a high toughness is obtained by adding Ca and controlling the sulfide form ( Japanese Unexamined Patent Application Publication No. 60-204863 ) and a technique in which a high toughness is obtained by adding REM and controlling the sulfide form ( Japanese Unexamined Patent Application Publication No. 62-260041 ).
  • JP 2002235114 discloses a method for producing a steel where ACR value is between 0 and 1 by which sufficient toughness can be obtained in a high heat input weld zone of >350 kJ/cm.
  • an object of the present invention is to solve the above-described problems experienced with the conventional arts and to thereby provide a steel that enables a high weld HAZ toughness at the same level as that of a parent metal of the steel even after welding is performed with a high heat input exceeding 400 kJ/cm.
  • the inventors carried out exhaustive researches. As a result, the inventors discovered that appropriate inclusion of Ca that is necessary for controlling the sulfide form is essential to improve the toughness of a weld heat affected zone (HAZ) even after welding performed with a high heat input exceeding 400 kJ/cm. More specifically, in order to improve the toughness of a high heat input weld HAZ, the inventors discovered that it is essential to suppress the coarsening of austenite grains in the high temperature region and to cause fine dispersion of the ferrite transformation nucleus that is necessary to accelerate ferrite transformation in the subsequent cooling stage. The conventional arts were insufficient in capability of achieving these essential factors.
  • CaS is crystallized in the stage of solidification during formation of a steel plate from molten steel.
  • CaS since CaS is crystallized at a lower temperature, CaS can be finely dispersed.
  • MnS is precipitated over the surface of CaS when a sufficient amount of solute S after crystallization of CaS is secured by controlling the contents of Ca and S and the amount of oxygen dissolved in the steel.
  • MnS itself has the ferrite nucleation ability and is effective to accelerate the ferrite transformation by forming Mn depleted zones.
  • the inventors discovered that the ferrite transformation is further accelerated by causing ferrite nucleation nuclei of TiN, AlN, and the like that are precipitated over MnS. These countermeasures described above enable fine dispersion of the ferrite-transformation generation nucleus that does not dissolve even at the high temperature during the high heat input welding. Consequently, the weld HAZ structure can be transformed into a ferrite and pearlite microstructure having a high toughness.
  • the present invention provides a steel for high heat input welding as defined in claim 1.
  • the lower limit of the C content is set to 0.03 mass% to secure a strength necessary for using the steel as a structural steel.
  • the upper limit of the C content is set to 0.15 mass% in consideration of deterioration in weld-crack resistance. More suitably, the C content is preferably limited to a range from 0.05 to 0.10 mass%.
  • the Si content is required to be at least 0.05 mass% for steelmaking. However, with an Si content exceeding 0.25 mass%, the parent-metal toughness is deteriorated, and M-A (Martensite-Austenite) constituent is formed in a high heat input weld HAZ, whereby the toughness of the HAZ is deteriorated.
  • M-A Martensite-Austenite
  • the Si content is preferably limited to a range of from 0.13 to 0.22 mass%.
  • Mn content of 0.5 mass% Mn or higher is required to secure a sufficient parent-metal strength.
  • Mn content is preferably limited to a range of from 0.8 to 1.6 mass%.
  • the P content is limited to 0.01 mass% or lower.
  • An S content exceeding 0.0030 mass% acts to deteriorate the parent-metal toughness.
  • the S content is limited to a range of from 0.0015 to 0.0025 mass% to generate CaS and MnS.
  • an Al content of 0.015 mass% or higher is required to generate CaS and MnS.
  • an Al content exceeding 0.1 mass% acts to deteriorate the parent-metal toughness and the weld metal toughness.
  • the S content is preferably limited to a range of from 0.02 to 0.06 mass%.
  • Ti is precipitated in the form of TiN upon solidification, thereby contributing to suppression of coarsening of austenite grains in the weld HAZ, and contributes, as a ferrite transformation nucleus, to improvement in the toughness of the weld HAZ.
  • Ti content lower than 0.004 mass%, the above-described effect is low; and with a Ti content exceeding 0.03 mass%, TiN grains are coarsened, and a desired effect cannot be obtained. More suitably, the Ti content is preferably limited to a range of from 0.008 to 0.02 mass%.
  • N is an element necessary to secure a required amount of TiN.
  • a sufficient amount of TiN cannot be secured.
  • an N content exceeding 0.0070 mass% the toughness is significantly deteriorated due to an increase in the amount of solute N in a region where TiN is dissolved by a weld-heating cycle. More suitably, the N content is preferably limited to a range of from 0.0030 to 0.0055 mass%.
  • Ca has a toughness-improving effect with S being fixed.
  • the Ca content is at least 0.0005 mass% to cause this effect to exhibit.
  • the effect is saturated eveb with a Ca content exceeding 0.0030 mass%.
  • the content is limited to the range of from 0.0005 to 0.0030 mass%. More suitably, the Ca content is preferably limited to a range of from 0.0010 to 0.0020 mass%.
  • Fig. 1 shows the results of synthetic HAZ tests performed under two simulated hea-input conditions in which Ca was diversely added into a fundamental composition of the steel of the present invention.
  • the toughness is significantly increased according to the relation 0.3 ⁇ ACR ⁇ 0.8 in either case where the time of 800-500°C cooling is 153 seconds or 270 seconds (improved by about 30°C in terms of vTrs).
  • the composition appears in the form of a compound sulfide with either MnS or MnS and TiN precipitated over CaS.
  • Fig. 3 is a schematic view showing the relationship between ACR and the sulfide to be precipitated.
  • products formed by simultaneous precipitation of the compound sulfides of CaS and MnS and TiN exist.
  • the quantity of the products is in a range of from 5 ⁇ 10 2 to 1 ⁇ 10 4 pieces/mm 2 , and the average grain size thereof is in a range of from 0.1 to 5 ⁇ m.
  • the present invention allows a steel of an embodiment to contain at least one or two selected elements from the elements V, Nb, Cu, Ni, Cr, and Mo that have a strength-improving function, as described hereunder.
  • B is effective in increasing hardenability during steel-plate manufacture. To secure this effect, the B content needs to be 0.0004 mass% or higher. However, addition of B exceeding 0.0010 mass% increases the hardenability, thereby decreasing the toughness of the weld HAZ.
  • V has the effect of improving the parent-metal strength and toughness. This effect can be secured with a V content of 0.01 mass% or higher. However, addition of V exceeding 0.2 mass% causes deterioration in the toughness.
  • Nb has the effect of enabling the parent-metal strength and toughness and the weld-joint strength to be secured. This effect can be secured with an Ni content of 0.007 mass% or higher. Addition Nb exceeding 0.05 mass% causes deterioration in the weld-HAZ toughness.
  • Ni has the effect of maintaining high parent-metal toughness and concurrently increasing the strength thereof. This effect can be secured with an Nb content of 0.10 mass% or higher. With a Ni content exceeding 1.5 mass%, since the effect is saturated, the content is specified to be the upper limit.
  • Cu exhibits an effect similar to that of Ni. This effect can be secured by including a Cu content of 0.10 mass% or higher. However, a Cu content exceeding 1.0 mass% causes hot embrittlement, thereby deteriorating the steel surface condition.
  • Cr has the effect of increasing the parent-metal strength. This effect is secured with a Cr content of 0.05 mass% or higher. However, since addition of an excessive amount causes adverse effects on the toughness, the upper limit is set to 0.7 mass%.
  • Mo Mo (Molybdenum): 0.7 Mass% Maximum
  • Mo has the effect of increasing the parent-metal strength. This effect is secured with a Cr content of 0.05 mass% or higher. However, since addition of an excessive amount causes adverse effects on the toughness, the upper limit is set to 0.7 mass%.
  • the compositions are each regulated in the content to the limited range. Therefore, the steel exhibiting a high toughness in the weld HAZ in the high heat input welding can be provided.
  • the steel of the present invention is manufactured in, for example, a procedure as described hereunder.
  • molten steel is refined using a convertor into steel.
  • an RH (Ruhrstahl-Heraeus) degassing process is performed, and the steel is formed into slabs through continuous casting or ingot-casting-blooming steps.
  • each of the slabs is reheated to a temperature of 1, 250°C or lower, and is then hot-rolled to a predetermined thickness in a temperature range of from a heating temperature to 650°C.
  • the hot-rolled steel is subjected to either an air-cooling process or an accelerated cooling process at a cooling rate of from 1 to 40°C/sec.
  • the cooling process is terminated at a temperature range of from 200 to 600°C, and air cooling is performed.
  • the hot-rolled steel is directly hardened from a temperature range of 650°C or higher, and is then tempered to a temperature of 500°C ⁇ 150°C.
  • the steel can be also manufactured according to a method selected from the steps wherein the hot-rolled steel is subjected to quenching after reheating in a temperature range of 850°C to 950°C and then, tempering to a temperature of 500°C ⁇ 150°C; the hot-rolled steel is reheated to a temperature of 1,000°C or lower and normalized; or the hot-rolled steel is reheated to a temperature of 1,000°C or lower and normalized and subsequently, tempered to a temperature of 650°C or lower.
  • the manufacture can be achieved even under manufacturing conditions ordinarily used in hot rolling with a tandem roller being used.
  • the steel plate according to the present invention is either a thick steel plate having a thickness of 6 mm or larger or a hot-rolled steel plate.
  • a welding method to be used for the steel plate of the present invention is not limited to a specific one.
  • the welding method may be an arc welding method, a submerged arc welding method, an electroslag welding method, an electrogas welding method, or any one of other heating-source welding techniques.
  • test specimens having a size of 80 mm (width) x 80 mm (length) x 15 mm (thickness) were prepared to measure properties after being subjected to welding thermal cycles. These test specimens were subjected to a welding thermal cycle set such that the rate of cooling from 800°C to 500°C after heating to 1,400°C was set to 1°C/sec (equivalent to a weld HAZ in electrogas welding with a heat input of 450 kJ/cm). Then, the test specimens were each evaluated for the weld-HAZ toughness according to the result of a 2-mm V-notch Charpy impact test.
  • Table 3 shows thus-obtained weld-HAZ toughnesses together with parent-metal strengths and toughnesses.
  • the parent-metal strengths were each obtained such that two JIS-Z2201 based test specimens were prepared from 1/2t-thick portions in the rolled direction of each of the rolled plates. The two test specimens were each tested in conformity with
  • the toughnesses were each measured such that three JIS-Z2201 based V-notch test specimens were prepared from 1/2t thick portions in the direction perpendicular to the rolled direction of the rolled plate. The three test specimens were each tested in conformity to JIS-Z2242 to measure a brittle-ductile fracture transition temperature (vTrs). The toughness (represented by the fracture transition temperature) of each of the parent metals and the weld HAZs was determined to be excellent in accordance with a criterion set to a vTrs of -40°C or lower.
  • any one of inventive examples a high weld-HAZ toughness satisfying vTrs ⁇ -40°C was obtained.
  • comparative examples were found to include those individually having low weld-HAZ toughnesses and even those individually having low parent-metal toughnesses.
  • at least one of the value of (Ca - (0.18 + 130 x Ca) x O)/1.25/S and the contents of the compositions such as Ca, Ti, C, Mn, Si, S, N, Cu, Cr, Mo, V, and B was found to be out of the range specified in the present invention.
  • a steel plate having a thickness of 60 mm was produced by hot rolling.
  • a weld joint was produced by electrogas welding with a heat input of 450 kJ/cm, and a microstructure of a representative weld HAZ of a 1/4t thick portion was observed.
  • Fig. 4 shows a microstructure taken of the inventive example steel 16
  • Fig. 5 shows a microstructure taken of the comparative example steel 23. From these microstructures, grain-coarsening in the weld HAZ was found to appear conspicuously in the comparative example steel 23 shown in Fig. 5 . In comparison, however, the microstructure of the weld HAZ in the inventive example steel 16 shown in Fig. 4 was found to have been refined to the same level as that of the microstructure of the parent metal.
  • a steel having a weld-HAZ toughness even after welding is performed with a high heat input of 400 kJ/cm or higher can be obtained.
  • the present invention greatly contributes to improvement in the quality of a large structure that is fabricated by high heat input welding, such as submerged arc welding, electrogas welding, and/or electroslag welding.
  • the steel has a high weld-HAZ toughness in a heat-input range of 400 kJ/cm or lower.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (1)

  1. Stahl zum Schweißen mit hohem Wärmeeintrag, dadurch gekennzeichnet, dass eine Zusammensetzung des Stalles umfasst: C (Kohlenstoff) 0,03 bis 0,15 Masseprozent (Masse-%); Si (Silizium) 0,05 bis 0,25 Masse-%; Mn (Mangan) 0,5 bis 2,0 Masse-%; P (Phosphor) s 0,01 Masse-%; S (Schwefel) 0,0015 bis 0,0030 Masse-%; Al (Aluminium) 0,015 bis 0,1 Masse-%; Ti (Titan) 0,004 bis 0,03 Masse-%; N (Stickstoff) 0,0020 bis 0,0070 Masse-%; Ca (Calcium) 0,0005 bis 0,0030 Masse-%, B (Bor) 0,0004 bis 0,0010 Masse-%; und O (Sauerstoff) ≤ 0,0045 Masse-%;
    wobei:
    die Einzelgehalte von Ca, O (Sauerstoff) und S den folgenden Ausdruck (1) erfüllen und der Rest der Zusammensetzung Fe (Eisen) und unvermeidbare Verunreinigungen umfasst: 0 , 3 ≤ ACR ≤ 0 , 8
    Figure imgb0003
     wobei ACR = (Ca - (0,18 + 130 x Ca) x O)/1,25/S, wobei Ca, O und S jeweils den Gehalt (Masse-Prozent) dieser darstellen; und optional umfassend ein oder zwei oder mehr gewählt aus: V (Vanadium) maximal 0,2 Masse-%; Cu (Kupfer) maximal 1,0 Masse-%; Ni (Nickel) maximal 1,5 Masse-%; Cr (Chrom) maximal 0,7 Masse-%; Nb (Niob) maximal 0,05 Masse-% und Mo (Molybdän) maximal 0,7 Masse-%.
EP02763002.9A 2002-09-04 2002-09-04 Stahlprodukt zum schweissen mit hohem wärmeeintrag und verfahren zu seiner herstellung Expired - Lifetime EP1533392B1 (de)

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PCT/JP2002/008977 WO2004022807A1 (ja) 2002-09-04 2002-09-04 大入熱溶接用鋼材およびその製造方法

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KR (1) KR100622888B1 (de)
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JP5439887B2 (ja) * 2008-03-31 2014-03-12 Ｊｆｅスチール株式会社 高張力鋼およびその製造方法
CN101736194B (zh) * 2008-11-19 2012-11-28 攀钢集团研究院有限公司 一种车轮钢及其制备方法和车轮
KR101333307B1 (ko) * 2009-03-25 2013-11-27 신닛테츠스미킨 카부시키카이샤 가공성 및 담금질 후의 피로 특성이 우수한 전봉 강관
CN101899614B (zh) * 2010-08-27 2012-07-04 攀钢集团钢铁钒钛股份有限公司 一种含V、Nb复合微合金化的热轧钢板及其制备方法
JP5480215B2 (ja) * 2011-09-08 2014-04-23 株式会社神戸製鋼所 引張強さ７８０ＭＰａ以上の低降伏比厚肉円形鋼管用鋼板およびその製造方法、並びに引張強さ７８０ＭＰａ以上の低降伏比厚肉円形鋼管
JP5857693B2 (ja) * 2011-12-05 2016-02-10 Ｊｆｅスチール株式会社 大入熱用鋼板およびその製造方法
KR20160121712A (ko) 2015-04-10 2016-10-20 동국제강주식회사 초대입열 용접용 강판의 제조 방법과 이에 의해 제조된 초대입열 용접용 강판
WO2017135179A1 (ja) * 2016-02-03 2017-08-10 Ｊｆｅスチール株式会社 大入熱溶接用鋼材
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CN107385353B (zh) * 2017-06-19 2019-06-25 江阴兴澄特种钢铁有限公司 一种海洋平台用250mm 特厚EH36钢板及其制备方法
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KR20210105418A (ko) * 2019-03-19 2021-08-26 제이에프이 스틸 가부시키가이샤 고망간강 주편의 제조 방법, 고망간강 강편 및 고망간강 강판의 제조 방법
CN111519098B (zh) * 2020-05-12 2021-06-15 首钢集团有限公司 一种低碳钢及控制低碳钢中夹杂物的脱氧方法

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CN100402688C (zh) 2008-07-16
EP1533392A4 (de) 2005-12-07
EP1533392A1 (de) 2005-05-25
CN1561403A (zh) 2005-01-05
KR20040040485A (ko) 2004-05-12

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