US3904447A - Method for producing steel materials for large heat-input welding - Google Patents

Method for producing steel materials for large heat-input welding Download PDF

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US3904447A
US3904447A US491483A US49148374A US3904447A US 3904447 A US3904447 A US 3904447A US 491483 A US491483 A US 491483A US 49148374 A US49148374 A US 49148374A US 3904447 A US3904447 A US 3904447A
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steel
tin
total
temperature
large heat
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Hisashi Gondo
Hajime Nakasugi
Hiroo Mazuda
Yasayuki Kawada
Rikio Chijiiwa
Shoichi Matsuda
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Nippon 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C21D6/02—Hardening by precipitation
    • 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

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  • Japan 57 ABSTRACT [22] Filed: July 1974 A method for producing steel materials suitable for [21] 1 ;491 4 3 large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al,
  • mIAT 0G IIAZ IMPAGT VALUE kgsnu mm 800 900 1000 n0uc FINISHING GUIILING TEMPERATURE (GI STEEL I PLATE THIGIIIIESS 25mm (IGGU G X GGG MINUTES GGGLING RATE 80 G NIIN.
  • an object of the present invention is to provide a method for producing high-toughness steel materials which satisfy the above demands.
  • Hardenability and cracking resistance are primarily depend on the chemical composition of the steel material to be welded and the heat-input for welding so far as the welding materials and welded structures are same, and thus generally determined by Ceq or Pc values as their parameters.
  • FIG. 1 is a graph showing the relation between the austenite grain size number and 2 mm V notch Charpy impact test values at 0C of the HAZ of hoint portions by electroslag welding of the steel materials according to the present invention and comparative steel materials.
  • FIG. 2 is a graph showing the relation between 2 mm V notch Charpy impact values at 0C of the HAZ of joint portions by electrogas welding and the amount of fine TiN up to 0.02; in the steel materials prior to welding in case of the steels containing 0.0015% N and 0.0036% N (Steels (2)-l0 and (2)-2 in Table 2) according to the present invention.
  • FIG. 3 is a graph showing the relation between the heat-inputs between 2 mm V notch Charpy impact val ues at 0C of HAZ of the steel (Steel (2)-l0 in Table 2) according to the present invention and a comparative steel (Steel (2)-9 in Table 2) welded by various welding methods.
  • FIG. 4 is a graph showing the relation between the ratio of NaS TiN/N (those marked by 0 and Q in the steels (Steel (2)-l0 and Steel (2)-2 in Table 2) of the present invention when they are heated at various tem peratures and held at the temperatures for l20 minutes and rapidly cooled in water and the amount (A and) of fine TiN up to 0.02 in the same steels when they are further held at 1 150C for minutes and quenched in water.
  • FIG. 5 is a graph showing the relation between the amount of fine TiN up to 002a in the steels (Steels (2)-l0 and (2)-2 according to the present invention when they are held at l350C for 600 minutes, subjected to breaking-down rolling, and cooled at a cooling rate of 60C/mm, and then reheated to various temperatures (holding time: 200 minutes).
  • FIG. 7 is a graph showing the relation between the finishing cooling temperatures and the HAZ toughness (2 mm V notch Charpy test) when the steel (Steel 1 l in Table 1) according to the present invention was heated and held at l350C for 600 minutes, broken down and water-cooled through the cooling course for stabilizing the HAZ toughness.
  • FIG. 8 shows the portion from which the 2mm V notch Charpy test pieces were taken for measuring the toughness values (vEo kg-m) of various welded joints as shown in Tables 1 to 6 (In the FIG. 1 is the deposited metal, I is the plate thickness).
  • the HAZ structure of conventional welding steel materials is not a lower-bainite structure, but mostly a mixture structure of martensite, lower-bainite, upperbainite ferrite and pearlite, and toughness of HAZ strongly depends on the austenite grain size. Thus it is most important to control the austenite grain size as small as possible for prevention of the toughness deterioration in HAZ. As shown in FIG. 1, it is necessary to maintain the austenite grain size in the HAZ equal or larger than ASTM No.
  • the present inventors have conducted extensive studies on methods for controlling the austenite grain size in the HAZ, and found that it is effective to disperse fine TiN more than a certain amount in the steel prior to welding for the purpose.
  • the present inventors have conducted further studies on methods for dispersing such fine TiN more than a certain amount, and developed a steel material which can give at least more than 4.2 kg-m 2 mm V notch Charpy impact valueat 0C to the HAZ by dispersing fine TiN more than a cer tain amount in the steel prior to welding by a method as described hereinafter other than the method disclosed in Japanese Patent Application Sho 45-25042, which comprises cooling rapidly the steel through the.
  • the present inventors have succeeded in adjusting the size and amount of TiN by refining the coarse TiN in the subsequent steps.
  • the adjustment has never been successful in the conventional arts.
  • the amounts of Ti and N in the steel are limited, and the steel is heated to a temperature commonly adopted in an ordinary steelmaking process to dissolve in solid solution TiN which was precipitated in the solidification and cooling in an amount not less than 0.004%, and this solid dissolved TiN is again reprecipitated as fine TiN of not larger than 0.02,u.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 1.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al, 0.004 to 0.03% Ti, 0.001 to 0.009% total N, with the balance being Fe and unavoidable impurities to a temperature between l250 and 1400C so as to dissolve into solid solution not less than 0.004% TiN, and then reprecipitating the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 1.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total A], 0.004 to 0.03% Ti, 0.001 to 0.009% total N, with the balance being Fe and unavoidable impurities to a temperature between l250 and 1400C so as to dissolve into solid solution not less than 0.004% TiN, rolling or forging the steel, forcedlycooling the steel to a temperature not higher than 800C, and then reheating the steel to a temperature not higher than 1 C so as to reprecipitate the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al, 0.004 to 0.03% Ti, 0.001 to 0.009% total N, with the balance being Fe and unavoidable impurities to a temperature between 1250 and 1400C so as to dissolve into solid solution not less than 0.004% TiN, rolling or forging the steel with a finishing temperature not lower than 1000C, and reheating the steel at a temperature not higher than 1 150C so as to reprecipitate the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al, 0.004 to 0.03% Ti, 0.001 to 0.009% total N, 0.001 to 0.03% REM with the balance being Fe and unavoidable impurities and satisfying the condition of REM/S 1.0 to 6.0 to a temperature between l250 and 1400C so as to dissolve into solid solution not less than 0.004% TiN, and reprecipitating the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C, 0.1 to 10% Si, 0.5 to 1.8% Mn, not more than 0.1% total A1, 0.004 to 0.03Ti, 0.001 to 0.009% total N, one or more of not more than 0.05% Nb, not more than 0.08% V, and not morethan 0.003% B with the balance being iron and unavoidable impurities to a temperature between l250 and 1400C so as to dissolve into solid solution not less than 0.004% TiN, and reprecipitating the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total A1, 0004 to 0.03% Ti, 0.001 to 0.009% total N, one or more of not more than 0.35% Cr, not more than 0.35% Mo, not more than 0.6% Cu, not more than 1.5% Ni, and not more than 1.0% W, with the balance being iron and unavoidable impurities and satisfying the condition of(Cu +Ni+W)/5+Cr+Mo 0.75% toa tempera ture between l250 and 1400C, and reprecipitating the dissolved TiN into fine TiN.
  • Ti is replaced by the same amount of one or more of Ti, Zr, and Hf so as to assure solid solution of nitrides in an amount of not less than 0.004% as one or more of TiN, ZrN and HfN during the heating step and reprecipitate fine TiN, ZrN and/or HfN.
  • the features of the present invention in respect of the production process lie in that a heating step for dissolving not less than 0.004% of TiN which has been precipitated during the solidification and cooling is combined with a rolling or forging step for reprecipitating the dissolved TiN with or without reheating after the rolling or forging in the process for producing steel products by rolling or forging a Ti-containing steel ingot or slab prepared by an ordinary steel-making method, and in that grain growth of the austenite in the HAZ is restricted by means of the reprecipitated fine TiN so as to prevent the lowering of toughness.
  • the amount of Ti for assuring the lower limit of 0.004% of the fine TiN is 0.004% for the commercial purpose in view of some Ti which forms oxides and sulfides, etc.
  • the content of Ti should be 0.004 to 0.03%.
  • Tin which has been dissolved in solid solution precipitates during the rolling or forging and the subsequent cooling step, but the amount of Ti which remains in solid solution increases in some cases depending on the rolling, forging or cooling conditions. If this remaining Ti in solid solution is reprecipitated as TiN finely enough in the subsequent reheating step, the refinement of TiN is effectively stabilized particularly in case of a smaller content of TiN.
  • the steel materials obtained according to the present invention must have low hardenability and good crack resistance in the HAZ and also must be less susceptible to the HAZ toughness deterioration even when welded with a large heat-input up to about 350 KJ/cm. Therefore, the method according to the present invention is characterized in that TiN which has been precipitated during the solidification and cooling of the molten steel is once dissolved in solid solution by heating and then reprecipitated into fine TiN so as to refine the austenite grains in the HAZ and to assure the HAZ toughness.
  • the upper limit of the reheating tempeature for reprecipitating Ti and N remaining in solid solution when the reheating temperature is above 1 C, both the TiN which has been already precipitated and the TiN which is precipitated by the reheating become coarse and the amount of TiN not larger than 0.02 1. decreases so that itis impossible to control the austenite grain size in the HAZ by the fine TiN.
  • the upper limit of the reheating temperature is defined to 1 150C.
  • the basic steel composition according to the present invention comprises 0.03 to 0.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al, 0.004 to 0.03% Ti, 0.00] to 0.009% total N with the balance being iron and unavoidable impurities.
  • Si is an element which is unavoidably contained in welding steels for reoxidation in steel making, but with less than 0. 1% Si, notch toughness of the steel material lowers and thus the lower limit is defined to 0.1%. On the other hand, with an excessive content of Si, not
  • the upper limit is defined to 1.0%.
  • the content of Mn with less than 0.5% Mn. softening of the HAZ is remarkable and strength and toughness of the steel material itself lower so that no satisfactory welding steel material is obtained. and thus the lower limit of Mn is defined to 0.5%.
  • the content of Mn is excessive, the HAZ toughness deteriorates sharply, and in case of the steel material as rolled the steel structure becomes upper bainite structure so that toughness lowers remarkably, and thus the upper limit of Mn is defined to 1.8%.
  • Al is an element which is unavoidably contained in Al-killed steels, but with more than 0. 1% total Al, not only the HAZ toughness but also the toughness of the weld metal lower remarkably, and thus the upper limit of total Al is defined to 0.1%.
  • the content of Ti is limited to from 0.004% to 0.03% and the content of total N is limited to from 0.001 to 0.009% for the reasons set forth hereinbefore.
  • the content of TiN never exceeds 0.04%.
  • the steel according to the present invention contains P and S as impurities and normally contains less than 0.04% P, but P is not added intentionally in the present invention.
  • S is normally contained in an amount less than 0.035%, and it is possible to lower the sulfur content down to about 0.0005% by the present level of technology, and in this case it is clear that both the HAZ toughness and the steel material toughness are improved. S is not added intentionally in the present invention.
  • the cooling conditions after the coarse TiN which has been precipitated during the solidification and cooling is dissolved by heating and the steel is rolled or forged are limited further.
  • the cooling is effected forcedly by water or a mixture of water and gas, and the finishing temperature of this cooling is limited not higher than 800C. so as to increase the amount of the fine TiN produced after the subsequent reheating at a temperature not higher than ll50C. Therefore, when the starting basic steel is treated by the first modification of the present invention, the HAZ toughness is further stabilized, while other properties required by a welding steel materials are not sacrificed at all.
  • the first modification of the present invention has been made for overcoming the above defect. and comprises heating the basic steel as defined above to a high temperature between l250 and l4()0C, rolling or forging the thus heated steel, forcedly cooling the rolled or forged steel with water or a mixture of water and gas so as to render the size of TiN precipitating during the cooling as small as possible and to suppress the precipitation amount, and reheating the steel to precipitate fine TiN not larger than 0.02,u as much as possible so as to further stabilize the HAZ toughness.
  • the finishing cooling temperature should be not higher than 800C for the reason that it is a temperature range above 800C which contributes substantially to the TiN precipitationand growth in case of a continuous cooling.
  • the amount of the precipitates is small and the size is also small so that the precipitates do not coarsen during the subsequent reheating step at a temperature below ll50C and do not effectthe amount of the fine TiN of 002p. or smaller. It is effective for stabilizing the HAZ toughness if the cooling after the working is forced effected according to the first modification of the present invention to suppress the coarsening of TiN when the steel is worked, and further the steel slab is heated between l250 and 1400C when it is worked into a final steel product, because the dissolution of TiN during the second heating promoted by the first heating and the forced cooling in combination, and thus the amount of the fine TiN in thc final steel product is increased.
  • the conditions of the rolling or forging the steel after the coarse TiN which has been precipitated during the solidification and cooling is dissolved are further limited.
  • the finishing working temperature to 1000C or higher, the amount of the fine TiN produced after the reheating at a temperature not higher than 1 C can be increased, and the HAZ toughness can be still further stabilized.
  • the technical means of the second modifi' cation is different from that of the first modification but the both modifications are metallurgically same in that the production conditions after the dissolving heating are particularly limited to suppress the precipitation of the coarse TiN before the reheating as much as possible to precipitate the fine TiN of 002p. or smaller as much as possible after the reheating.
  • the finishing working temperature is not lower than l000C so that the formation of TiN precipitation nuclei during the rolling or forging is reduced and thus TiN precipitation during the subsequent cooling is reduced and also the precipitation of the coarse TiN is suppressed. Therefore, the second modification brings forth the same results as the first modification and stabilizes still further the HAZ toughness. It is very natural that if the second modification is combined with the first modification, the HAZ toughness is still further stabilized.
  • rare earth metals chiefly Ce, La and Pr. are added to the basic steel composition, in an amount between 0.001 to 0.03%, and the ratio of REM/S is defined to from 1.0 to 6.0.
  • Table 4 the HAZ toughness of the steel treated according to the third modification is further stabilized.
  • more than 0.08% V and not more than 0.003% B is further added to the basic steel composition.
  • These elements are added for the purpose of further improving the strength and toughness of the steel produced by the present invention as well as widening the plate thickness range which can be commercially produced and assuring the strength of the joints welded with a large heat-input. If these elements are added in an excessive amount, the HAZ toughness is remarkably deteriorated even in case of a steel in which the l-lAZ toughness has been improved by the fine TiN as in the steel produced according to the present invention. Therefore, their upper limits are defined.
  • Nb contents up to 0.05% improves the above various properties without substantially deteriorating the HAZ toughness, but Nb contents beyond 0.05% remarkably deteriorate the HAZ toughness. Therefore, the upper limit is defined to 0.05%.
  • V has similar effects as Nb, but its upper limit is allowed to 0.08%.
  • B is a useful element when the steel produced by the present invention is quenched and tempered, but when it is added in an amount beyond 0.003% B-constituent is formed in the HAZ at the time of a large heat-input welding, and the HAZ toughness is remarkably deteriorated.
  • the upper limit of B is defined to 0.003%.
  • one or more of not more than 0.35% Cr, not more than 0.35% Mo, not more than 1.5% Ni, not more than 0.6% Cu and not more than 1.0% W is further added to the basic steel composition so as to satisfy the condition: (Cu Ni W)/5 Cr Mo 0.75%.
  • an excessive chromium content will increase hardenability of the HAZ and lower the HAZ toughness and crack resistance.
  • the upper limit is defined to 0.35%.
  • M0 is similar to Cr and effective to improve various properties of the steel material, but its upper limit is defined to 0.35% because of its adverse effect on the HAZ.
  • Ni is effective to increase the strength and toughness of the steel material without adverse effect on the HAZ hardenability and toughness, but a nickel content beyond 1.5% will cause adverse effect on the HAZ hardenability and toughness, and thus its upper limit is defined to 1.5%.
  • Ti is replaced by 0.004 to 0.03% of one or more than two of Ti, Zr and Hf.
  • Zr and Hf are elements belonging to the same group as Ti and form stable nitridesjust as Ti, prevent coarsening of the austenite grain size in the HAZ and improve the HAZ toughness. Therefore, if one or more than two of Ti, Zr and Hf is added in an amount from 0.04 to 0.03% so as to dissolve into solid solution not less than 0.004% of one or more than two of TiN, ZrN and HfN and then reprecipitates them, the same effects as obtained by Ti can be obtained.
  • the elements other than Ti, Zr and Hf are limited to the same ranges as defined in the previous modifications for the same reasons.
  • SAW Submerged arc welding
  • EU Elcctrogas welding
  • ES Electroslng Welding.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18%, C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al, 0.004 to 0.03% Ti, and 0.001 to 0.009% total N, with the balance being Fe and unavoidable impurities to a temperature between 1250 and 1400C so as to dissolve not less than 0.004% of the TiN into solid solution and then reprecipitating the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C. 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al, 0.004 to 0.03% Ti, and 0.001 to 0.009% total N, with the balance being Fe and unavoidable impurities to a temperature between 1250 and 1400C so as to dissolve not less than 0.004% of the TiN into solid solution, rolling or forging the steel. forcedly cooling the steel to a temperature not higher than 800C, and then reheating the steel to a temperature not higher than 1 l- 50C so as to reprecipitate the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total A], 0.004 to 0.03% Ti, and 0.001 to 0.009% total N, with the balance being Fe and unavoidable impurities to a temperature between l250 and 1400C so as to dissolve not less than 0.004% C of the TiN into solid solution.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C. 1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al, 0.004 to 0.03% Ti, 0.001 to 0.009% total N. and 0.001 to 0.03%- REM with the balance being Fe and unavoidable impurities and satisfying the condition of REM/S 1.0 to 6.0, to a temperature between l250 and 1400C so as to dissolve not less than 0.004% of the TiN into solid solution, and reprecipitating the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding in which i the reprecipitation of the dissolved TiN is done by reheating the steel to a temperature not higher than 1 150C after the heatingv 10.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C, 0.1 to 1.0% Si, 0.5 to 1.8% Mn, not more than 0.1% total Al,
  • 0.004 to 0.03% Ti 0.001 to 0.009% total N, one or more of not more than 0.05 Nb, not more than 0.08% V and not more than 0.003% B with the balance being iron and unavoidable impurities to a temperature between l250 and 1400C so as to dissolve not less than 0.004% of the T iN into solid solution, and reprecipitating the dissolved TiN into fine TiN.
  • a method for producing steel materials suitable for large heat-input welding which comprises heating a steel ingot or slab containing 0.03 to 0.18% C, 0.1 to
  • a method for producing steel materials suitable for large heat-input welding according to any of the preceeding claims in which 0.004 to 0.03% Ti is replaced by the same amount of one or more of Ti, Zr and Hf so as to assure a solid solution of nitrides in an amount of not less than 0.004% as one or more of TiN, ZrN and HfN during the heating step and reprecipitate fine TiN, ZrN or HfN.

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US4125416A (en) * 1976-09-10 1978-11-14 Nippon Steel Corporation Method for producing steel strip or steel sheet containing carbide and nitride forming elements
US4219371A (en) * 1978-04-05 1980-08-26 Nippon Steel Corporation Process for producing high-tension bainitic steel having high-toughness and excellent weldability
USRE31251E (en) * 1976-04-12 1983-05-24 Nippon Steel Corporation Process for producing a high tension steel sheet product having an excellent low-temperature toughness with a yield point of 40 kg/mm2 or higher
EP1006209A1 (de) * 1998-03-13 2000-06-07 Nippon Steel Corporation Bn-auscheidungsverstärkter, ferritischer hitzebeständiger stahl mit niedrigem kohlenstoffgehalt und hohen schweisseigenschaften
EP1254275A1 (de) * 2000-12-14 2002-11-06 Posco Tin- und zrn-ausscheidendes stahlblech für schweisstrukturen, hetsellungsverfahren dafür und diese verwendende schweissgefüge
US20030106623A1 (en) * 2000-12-01 2003-06-12 Hong-Chul Jeong Steel plate to be precipitating tinfor welded structures, method for manufacturing the same and welding fabric using the same
US20040144454A1 (en) * 2001-11-16 2004-07-29 Hong-Chul Jeong Steel plate having superior toughness in weld heat-affected zone and method for manufacturing the same, and welded structure made therefrom
EP1719821A1 (de) * 2004-02-04 2006-11-08 Sumitomo Metal Industries, Ltd. Stahlprodukt für ein leitungsrohr mit hervorragender hic-beständigkeit und damit hergestelltes leitungsrohr
CN102555351A (zh) * 2010-12-20 2012-07-11 顾伟 高抗磨双金属复合材料
CN116043132A (zh) * 2021-10-28 2023-05-02 江苏新华合金有限公司 一种314耐热钢丝及其制备方法

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GB2099016B (en) * 1981-02-26 1985-04-17 Nippon Kokan Kk Steel for welding with high heat input
JPS581012A (ja) * 1981-06-25 1983-01-06 Nippon Steel Corp 均質な鋼の製造方法
JPS59162223A (ja) * 1983-03-07 1984-09-13 Japan Steel Works Ltd:The 非調質高強度高靭性鋼を母材としたクラツド鋼の製造方法
GB8603500D0 (en) * 1986-02-13 1986-03-19 Hunting Oilfield Services Ltd Steel alloys
JPH02479U (de) * 1988-06-10 1990-01-05
FR2668169B1 (fr) * 1990-10-18 1993-01-22 Lorraine Laminage Acier a soudabilite amelioree.
JP5418662B2 (ja) 2012-01-30 2014-02-19 Ｊｆｅスチール株式会社 溶接部靭性に優れた高靭性クラッド鋼板の母材及びそのクラッド鋼板の製造方法

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US3625780A (en) * 1968-04-29 1971-12-07 Youngstown Sheet And Tube Co Process for preparation of high-strength alloy of titanium and ferritic structure
US3673009A (en) * 1969-12-17 1972-06-27 Inland Steel Co Method for producing a part from steel sheet
US3787250A (en) * 1971-03-11 1974-01-22 Jones & Laughlin Steel Corp Corrosion-resistant high-strength low-alloy steels

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US3625780A (en) * 1968-04-29 1971-12-07 Youngstown Sheet And Tube Co Process for preparation of high-strength alloy of titanium and ferritic structure
US3673009A (en) * 1969-12-17 1972-06-27 Inland Steel Co Method for producing a part from steel sheet
US3787250A (en) * 1971-03-11 1974-01-22 Jones & Laughlin Steel Corp Corrosion-resistant high-strength low-alloy steels

Cited By (21)

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USRE31251E (en) * 1976-04-12 1983-05-24 Nippon Steel Corporation Process for producing a high tension steel sheet product having an excellent low-temperature toughness with a yield point of 40 kg/mm2 or higher
US4125416A (en) * 1976-09-10 1978-11-14 Nippon Steel Corporation Method for producing steel strip or steel sheet containing carbide and nitride forming elements
US4219371A (en) * 1978-04-05 1980-08-26 Nippon Steel Corporation Process for producing high-tension bainitic steel having high-toughness and excellent weldability
EP1006209A1 (de) * 1998-03-13 2000-06-07 Nippon Steel Corporation Bn-auscheidungsverstärkter, ferritischer hitzebeständiger stahl mit niedrigem kohlenstoffgehalt und hohen schweisseigenschaften
EP1006209A4 (de) * 1998-03-13 2002-08-07 Nippon Steel Corp Bn-auscheidungsverstärkter, ferritischer hitzebeständiger stahl mit niedrigem kohlenstoffgehalt und hohen schweisseigenschaften
US6946038B2 (en) * 2000-12-01 2005-09-20 Posco Steel plate having Tin+MnS precipitates for welded structures, method for manufacturing same and welded structure
US20030106623A1 (en) * 2000-12-01 2003-06-12 Hong-Chul Jeong Steel plate to be precipitating tinfor welded structures, method for manufacturing the same and welding fabric using the same
EP1254275A1 (de) * 2000-12-14 2002-11-06 Posco Tin- und zrn-ausscheidendes stahlblech für schweisstrukturen, hetsellungsverfahren dafür und diese verwendende schweissgefüge
US20030121577A1 (en) * 2000-12-14 2003-07-03 Hae-Chang Choi Steel plate to be precipitating tinfor welded structures,method for manufacturing the same and welding fabric using the same
US6966955B2 (en) * 2000-12-14 2005-11-22 Posco Steel plate having TiN+ZrN precipitates for welded structures, method for manufacturing same and welded structure made therefrom
EP1254275A4 (de) * 2000-12-14 2004-11-10 Posco Tin- und zrn-ausscheidendes stahlblech für schweisstrukturen, hetsellungsverfahren dafür und diese verwendende schweissgefüge
US20050173030A1 (en) * 2001-11-16 2005-08-11 Strapack Corporation Method for manufacturing steel plate having superior toughness in weld heat-affected zone
US20040144454A1 (en) * 2001-11-16 2004-07-29 Hong-Chul Jeong Steel plate having superior toughness in weld heat-affected zone and method for manufacturing the same, and welded structure made therefrom
US7105066B2 (en) * 2001-11-16 2006-09-12 Posco Steel plate having superior toughness in weld heat-affected zone and welded structure made therefrom
US7396423B2 (en) 2001-11-16 2008-07-08 Posco Method for manufacturing steel plate having superior toughness in weld heat-affected zone
EP1719821A1 (de) * 2004-02-04 2006-11-08 Sumitomo Metal Industries, Ltd. Stahlprodukt für ein leitungsrohr mit hervorragender hic-beständigkeit und damit hergestelltes leitungsrohr
US20070217942A1 (en) * 2004-02-04 2007-09-20 Sumitomo Metal Industries, Ltd. Steel Product for Use as Line Pipe Having High Hic Resistance and Line Pipe Produced Using Such Steel Product
EP1719821A4 (de) * 2004-02-04 2008-06-25 Sumitomo Metal Ind Stahlprodukt für ein leitungsrohr mit hervorragender hic-beständigkeit und damit hergestelltes leitungsrohr
US7648587B2 (en) 2004-02-04 2010-01-19 Sumitomo Metal Industries, Ltd. Steel product for use as line pipe having high HIC resistance and line pipe produced using such steel product
CN102555351A (zh) * 2010-12-20 2012-07-11 顾伟 高抗磨双金属复合材料
CN116043132A (zh) * 2021-10-28 2023-05-02 江苏新华合金有限公司 一种314耐热钢丝及其制备方法

Also Published As

Publication number Publication date
GB1473934A (en) 1977-05-18
SE417984B (sv) 1981-04-27
DE2436419B2 (de) 1978-04-06
JPS5526164B2 (de) 1980-07-11
SE7409807L (sv) 1975-02-03
DE2436419A1 (de) 1975-02-20
JPS5033920A (de) 1975-04-02

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