US20200190618A1 - Steel member, hot-rolled steel sheet for steel member, and production method therefor - Google Patents

Steel member, hot-rolled steel sheet for steel member, and production method therefor Download PDF

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US20200190618A1
US20200190618A1 US16/500,613 US201816500613A US2020190618A1 US 20200190618 A1 US20200190618 A1 US 20200190618A1 US 201816500613 A US201816500613 A US 201816500613A US 2020190618 A1 US2020190618 A1 US 2020190618A1
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hot
steel
steel sheet
rolled steel
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Shunsuke Toyoda
Ichiro Sugimoto
Shuji Kawamura
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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
    • C22C38/14—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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • B21C37/08—Making tubes with welded or soldered seams
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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 by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C22C38/002—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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to steel members, hot-rolled steel sheets for the steel members, and production methods therefor. Specifically, the present invention relates to a steel member having good fatigue resistance properties in a plastic strain range, a hot-rolled steel sheet for the steel member, and production methods therefor.
  • the present invention relates to welded steel pipes for coiled tubing, welded steel pipes for line pipes, and welded steel pipes for automotive structural members, and in particular relates to welded steel pipes for coiled tubing. These welded steel pipes are required to have high strength and fatigue resistance properties in a plastic strain range.
  • the present invention more particularly relates to an improvement in the fatigue resistance properties of such steel members in the plastic strain range.
  • Patent Literature 1 discloses a method for producing a high-tensile-strength electric resistance welded steel pipe having a yield strength of 700 MPa or more, a tensile strength of 800 MPa or more, and ductility, i.e., an elongation of 15% or more after pipe making, the pipe being used for high-strength structural members and driving force transmission members for automobiles and as an electric resistance welded pipe for cleaning oil country tubular goods.
  • this method it is possible to provide a high-tensile-strength electric resistance welded steel pipe whose heat-affected zone is not softened because the pipe contains 0.09% to 0.18% C and predetermined amounts of alloying elements of Cu, Ni, Cr, and Mo.
  • the pipe disadvantageously has short durability life in repeated use as a steel pipe for fatigue applications, in particular, a steel pipe for coiled tubing required to have fatigue resistance properties in a plastic strain range.
  • Patent Literature 2 discloses a steel strip for coiled tubing, the steel strip having good uniformity in material quality, and a method for producing the steel strip. According to this method, a steel strip for coiled tubing, the steel strip having low variations in yield strength in the width and longitudinal directions of a coil, can be provided because the steel strip contains 0.10% to 0.16% C and predetermined amounts of alloying elements of Cr, Cu, Ni, Mo, Nb, and Ti. However, the steel strip disadvantageously has insufficient fatigue resistance properties and low durability life in repeated use.
  • Patent Literature 3 discloses a hardened and tempered steel pipe having good fatigue life as a steel pipe for machine structures such as automobiles, in particular, as a hollow stabilizer for automobiles. According to this method, it is possible to provide a steel pipe having long fatigue life because the steel pipe has a predetermined chemical composition, a precipitated carbide has an average particle size of 0.5 ⁇ m or less, and a central portion in the thickness direction has a hardness of 400 HV.
  • the level of the fatigue life of the steel pipe is a life of several tens of thousands cycles in a low stress-high cycle elastic region fatigue properties. Coiled tubing is used several hundred times while repeatedly inserted into and recovered from a well.
  • the phrase “good fatigue resistance properties in a plastic strain range” or “good in terms of fatigue resistance properties in a plastic strain range” indicates that when a tensile fatigue test is performed under conditions of a tensile mode, a strain control mode, a strain ratio of 0, and a total strain range of 2.0%, the number of cycles until fracture is 1,000 or more cycles.
  • a hot-rolled steel sheet serving as a material of a steel member according to aspects of the present invention also refers to a “material hot-rolled steel sheet”.
  • Examples of the steel member according to aspects of the present invention include steel pipes such as welded steel pipes and formed components such as automotive structural members.
  • Examples of the welded steel pipes include welded steel pipes for coiled tubing, welded steel pipes for line pipes, and welded steel pipes for automotive structural members.
  • the inventors have conducted systematic experiments and examinations using different chemical compositions under different production conditions of a hot-rolled steel sheet serving as a material in order to achieve a balance between strength and fatigue resistance properties, which are conflicting properties, at a high level, and have found that a steel member having both of high strength and good fatigue resistance properties in a plastic strain range is obtained by hot-rolling a steel having a specific chemical composition at specific temperature processing conditions or forming a steel having a specific chemical composition into a steel pipe and then performing heat treatment under specific conditions.
  • a steel member contains, on a percent by mass basis, 0.031% to 0.200% Ti, wherein 0.005% or more of Ti is precipitated as a precipitate having a particle size of 20 nm or less in a microstructure.
  • the steel member has a composition containing, on a percent by mass basis, C: 0.19% to 0.50%, Si: 0.002 to 1.5%, Mn: 0.4% to 2.5%, Al: 0.01% to 0.19%, Cr: 0.001% to 0.90%, B: 0.0001% to 0.0050%, Ti: 0.031% to 0.200%, P: 0.019% or less (including 0%), S: 0.015% or less (including 0%), N: 0.008% or less (including 0%), O: 0.003% or less (including 0%), and Sn: 0.10% or less (including 0%), the balance being Fe and incidental impurities.
  • the steel member described in [2] further contains, on a percent by mass basis, one or two or more selected from Nb: 0.001% to 0.15%, V: 0.001% to 0.15%, W: 0.001% to 0.15%, Mo: 0.001% to 0.45%, Cu: 0.001% to 0.45%, Ni: 0.001% to 0.45%, Ca: 0.0001% to 0.005%, and Sb: 0.0001% to 0.10%, in addition to the composition.
  • the steel member described in any of [1] to [3] the steel member is a welded steel pipe.
  • a hot-rolled steel sheet for the steel member described in any of [1] to [4] contains, on a percent by mass basis, 0.031% to 0.200% Ti, in which 0.005% or more of Ti is present as dissolved Ti in the microstructure.
  • a leading end portion and a trailing end portion are both end portions in a longitudinal direction, and each of the leading end portion and the trailing end portion has a thickness 5% to 50% larger than a central portion in the longitudinal direction.
  • a method for producing the steel member described in any of [1] to [4] includes subjecting a hot-rolled steel sheet to forming processing, the hot-rolled steel sheet containing, on a percent by mass basis, 0.031% to 0.200% Ti, 0.005% or more of Ti being present as dissolved Ti in a microstructure, and then performing heat treatment including heating to a temperature of higher than 550° C. and 1,050° C. or lower and then cooling at an average cooling rate of 10° C./s or more in the temperature range of 550° C. to 400° C.
  • the hot-rolled steel sheet is produced by, after performing slab extraction of a steel slab containing, on a percent by mass basis, 0.031% to 0.200% Ti at a temperature higher than an equilibrium dissolution temperature T Ti calculated from formula (1) below, completing finish rolling at a temperature equal to or higher than T Ti —400° C., performing cooling at an average cooling rate of 10° C./s or more in the temperature range of T Ti —400° C. to T Ti —500° C., and performing coiling at a temperature equal to or lower than T Ti -500° C.,
  • a method for producing the hot-rolled steel sheet described in [5] or [6] includes after performing slab extraction of a steel slab containing, on a percent by mass basis, 0.031% to 0.200% Ti at a temperature higher than an equilibrium dissolution temperature T Ti calculated from formula (1) below, completing finish rolling at a temperature equal to or higher than T Ti —400° C., performing cooling at an average cooling rate of 10° C./s or more in the temperature range of T Ti -400° C. to T Ti —500° C., and performing coiling at a temperature equal to or lower than T Ti —500° C.,
  • Ti, N, and C in formula (1) indicate contents (% by mass) of respective elements in the steel slab.
  • the steel member having good fatigue resistance properties in the plastic strain range.
  • the hot-rolled steel sheet according to aspects of the present invention is particularly suitable as a material of the steel member.
  • the steel member that achieves a balance between strength and fatigue resistance properties, which are conflicting properties, at a high level.
  • welded steel pipes for coiled tubing in particular, welded steel pipes for line pipes, and welded steel pipes for automotive structural members, which are required to have high strength and fatigue resistance properties in the plastic strain range, are suitable.
  • welded steel pipes for coiled tubing are suitable.
  • the FIGURE illustrates the relationship between the amount of Ti precipitated as precipitates with a particle size of 20 nm or less by post-heat treatment and fatigue properties in a plastic strain range.
  • a steel member according to aspects of the present invention is obtained by subjecting a hot-rolled steel sheet to forming processing, the hot-rolled steel sheet (material hot-rolled steel sheet) having been produced by hot rolling under specific temperature processing conditions, and then performing heat treatment under specific conditions.
  • the heat treatment after the forming processing of the material hot-rolled steel sheet also referred to as “post-heat treatment”.
  • Ti precipitates as carbonitride in a hot-rolling step to inhibit grain growth due to recovery and recrystallization in the hot-rolling step.
  • the presence of Ti is effective in providing a fine ferrite phase having a desired grain size (1 to 50 ⁇ m) in the structure (microstructure) of the material hot-rolled steel sheet.
  • the refinement of the microstructure in the material hot-rolled steel sheet leads to the refinement of the microstructure after heat treatment subsequent to forming processing (cold working) such as pipe making or parts forming, thereby providing good fatigue resistance properties in a plastic strain range.
  • Tanaka et al. propose a model in which dislocations are irreversibly piled up on a slip plane due to fatigue cycles, and an initial crack is generated when a stress generated at this time exceeds a critical stress (literature: K. Tanaka and T. Mura: J Appl. Mech., Vol. 48, p. 97-103 (1981)).
  • the refined microstructure material according to aspects of the present invention will exhibit good fatigue resistance properties in the plastic strain range because of delayed fatigue crack initiation.
  • Ti is an essential element that improves strength after heat treatment subsequent to forming processing such as pipe making or parts forming and that significantly improves fatigue strength by enhancing the precipitation strengthening of a matrix in the form of carbide, solid-solution strengthening as a solid-solution element, and transformation structure strengthening as a hardenability-improving element. These effects are obtained when the Ti content is in the range of 0.031% to 0.200%. If the Ti content is lower than the lower limit of the above range, 0.005% or more of Ti is present as dissolved Ti in the stage of the material hot-rolled steel sheet described below.
  • the Ti content is more than the upper limit of the above range, coarse TiN is formed to degrade the fatigue resistance properties. Accordingly, the Ti content is in the range of 0.031% to 0.200%.
  • the Ti content is preferably more than 0.120%.
  • the Ti content is preferably 0.150% or less.
  • 0.005% or more of Ti is precipitated as precipitates having a particle size of 20 nm or less.
  • the inventors have found that in the case where a hot-rolled steel sheet is used as a material as in accordance with aspects of the present invention and where fatigue resistance properties in a plastic strain range are required after heat treatment (post-heat treatment) subsequent to forming processing such as pipe making or parts forming, 0.005% or more of Ti is precipitated as fine precipitates having a particle size of 20 nm or less by the post-heat treatment to provide excellent fatigue resistance properties in the plastic strain range.
  • the FIGURE illustrates the relationship between the amount (% by mass) of Ti precipitated as the fine precipitates having a particle size of 20 nm or less by the post-heat treatment and the fatigue resistance properties in the plastic strain range.
  • the amount of Ti precipitated as the fine precipitates having a particle size of 20 nm or less by the post-heat treatment is 0.005% or more
  • the number of cycles until fracture is 1,000 or more cycles. That is, good fatigue resistance properties in the plastic strain range are provided.
  • C is an element that ensures high strength by post-heat treatment under specific conditions and that binds to Ti during the post-heat treatment and is precipitated as fine precipitates particularly in a surface layer portion to improve the fatigue resistance properties in the plastic strain range.
  • desired strength YS 770 MPa
  • fatigue resistance properties in the plastic strain range are difficult to obtain.
  • the toughness and weldability of the steel member such as a steel pipe cannot be ensured; thus, the upper limit of the C content is set thereto. More preferably, the C content is more than 0.28%. More preferably, the C content is 0.30% or less.
  • Si is an element that improves the fatigue resistance properties in the plastic strain range while ensuring desired strength by solid-solution strengthening.
  • a Si content of less than 0.002% results in insufficient strength.
  • a Si content of more than 1.5% results in a decrease in weldability. Accordingly, the Si content is preferably limited to 0.002% to 1.5%. More preferably, the Si content is 0.05% or more. More preferably, the Si content is 0.35% or less.
  • Mn serves to ensure desired strength owing to low-temperature transformation strengthening during the post-heat treatment to improve the fatigue resistance properties in the plastic strain range. At a Mn content of less than 0.4%, the effect is not sufficiently provided. At a Mn content of more than 2.5%, the weldability deteriorates. Accordingly, the Mn content is preferably limited to 0.4% to 2.5%. More preferably, the Mn content is 1.09% or more. More preferably, the Mn content is 1.99% or less.
  • Al is a deoxidizing element during steel making and serves to inhibit the growth of austenite grains in the hot-rolling step, refine grains, provide desired ferrite grain size (1 to 50 ⁇ m) after the post-heat treatment, and improve the fatigue resistance properties in the plastic strain range.
  • An Al content of less than 0.01% does not result in these effects, thereby increasing the ferrite grain size.
  • An Al content of more than 0.19% results in the deterioration of the weldability. Additionally, oxide inclusions tend to be increased to decrease the fatigue resistance properties. More preferably, the Al content is 0.041% or more. More preferably, the Al content is 0.080% or less.
  • the Cr serves to ensure desired strength by low-temperature transformation strengthening during the post-heat treatment to improve the fatigue resistance properties in the plastic strain range. At a Cr content of less than 0.001%, the effect is not sufficiently provided. At a Cr content of more than 0.90%, the weldability deteriorates. Accordingly, the Cr content is preferably limited to 0.001% to 0.90%. More preferably, the Cr content is 0.001% to 0.19%.
  • the B serves to ensure desired strength by low-temperature transformation strengthening during the post-heat treatment to improve the fatigue resistance properties in the plastic strain range.
  • the B content is preferably limited to 0.0001% to 0.0050%. More preferably, the B content is 0.0005% or more. More preferably, the B content is 0.0035% or less.
  • P decreases the fatigue resistance properties in the plastic strain range and deteriorates the electric resistance weldability by solidification co-segregation with Mn.
  • the upper limit thereof is preferably 0.019%.
  • S is present as inclusions in steel in the form of, for example, MnS and acts as a starting point of a fatigue crack in the plastic strain range to deteriorate the fatigue resistance properties.
  • the adverse effect is markedly provided.
  • the upper limit thereof is preferably 0.015%. More preferably, the S content is 0.005% or less.
  • N forms TiN and precipitates as coarse precipitates, thereby consuming dissolved Ti.
  • N decreases the effect in which excellent fatigue resistance properties in the plastic strain range is obtained by the fact that the addition of Ti allows 0.005% or more of Ti to be present as dissolved Ti in the stage of the material hot-rolled steel sheet and that 0.005% or more of Ti is precipitated as fine precipitates having a particle size of 20 nm or less by heat treatment subsequent to forming processing.
  • a N content of more than 0.008% the adverse effect is markedly provided.
  • the upper limit thereof is preferably 0.008%. More preferably, the N content is 0.0049% or less.
  • O is present as oxide inclusions and decreases the fatigue resistance properties of steel. At an O content of more than 0.003%, the adverse effect is markedly provided. Thus, the upper limit thereof is preferably 0.003%. More preferably, the O content is 0.002% or less.
  • Sn is present as a dissolved element and decreases the hot ductility of steel. At a Sn content of more than 0.10%, the adverse effect is markedly provided. Thus, the upper limit thereof is preferably 0.10%. More preferably, the Sn content is 0.03% or less.
  • the balance is Fe and incidental impurities.
  • the following elements may be further added in order to improve the advantageous effects according to aspects of the present invention.
  • Nb precipitates as carbide is effective in inhibiting grain growth due to recovery and recrystallization in the hot-rolling step to provide desired ferrite grain size (1 to 50 ⁇ m), and may be contained as needed. At a Nb content of less than 0.001%, these effects are not provided. At a Nb content of more than 0.15%, coarse precipitates are precipitated in a surface layer portion by strain-induced precipitation during hot rolling to decrease fine precipitates in the surface layer portion, thereby decreasing the fatigue resistance properties in the plastic strain range. Thus, the upper limit thereof is 0.15%. Accordingly, when Nb is contained, the Nb content is 0.001% to 0.15%. More preferably, the Nb content is 0.001% to 0.009%.
  • V 0.001% to 0.15%
  • V precipitates as carbide is effective in inhibiting grain growth due to recovery and recrystallization in the hot-rolling step to provide desired ferrite grain size (1 to 50 ⁇ m), and may be contained as needed. At a V content of less than 0.001%, these effects are not provided. At a V content of more than 0.15%, coarse precipitates are precipitated in a surface layer portion by strain-induced precipitation during hot rolling to decrease fine precipitates in the surface layer portion, thereby decreasing the fatigue resistance properties in the plastic strain range. Thus, the upper limit thereof is 0.15%. Accordingly, when V is contained, the V content is 0.001% to 0.15%. More preferably, the V content is 0.001% to 0.049%.
  • W precipitates as carbide serves to complement the effect of inhibiting grain growth due to recovery and recrystallization in the hot-rolling step to provide desired ferrite grain size (1 to 50 ⁇ m), and may be contained as needed. At a W content of less than 0.001%, these effects are not provided. At a W content of more than 0.15%, coarse precipitates are precipitated in a surface layer portion by strain-induced precipitation during hot rolling to decrease fine precipitates in the surface layer portion, thereby decreasing the fatigue resistance properties in the plastic strain range. Thus, the upper limit thereof is 0.15%. Accordingly, when W is contained, the W content is 0.001% to 0.15%. More preferably, the W content is 0.001% to 0.049%.
  • Mo serves to ensure desired strength by low-temperature transformation strengthening or precipitation strengthening during the post-heat treatment and improving the fatigue resistance properties in the plastic strain range and may be contained as needed. At a Mo content of less than 0.001%, the effect is not provided. At a Mo content of more than 0.45%, the weldability deteriorates. Accordingly, when Mo is contained, the Mo content is 0.001% to 0.45%. More preferably, the Mo content is 0.001% to 0.30%.
  • Cu and Ni are elements serving to complement the effect of improving the fatigue strength of Mn and are effective in enhancing the corrosion resistance of a steel material.
  • Cu and Ni may each be contained as needed. These effects are provided when Cu and Ni is each contained in an amount of 0.001% or more.
  • Cu or Ni is contained in an amount of more than 0.45%, the weldability deteriorates.
  • the upper limit of each of Cu and Ni is 0.45%.
  • Cu is contained, the Cu content is 0.001% to 0.45%.
  • Ni the Ni content is 0.001% to 0.45%. More preferably, each element is contained in an amount of 0.35% or less.
  • Ca has what is called the shape control effect of forming elongated MnS into granular Ca(Al)S(O), is effective in inhibiting the fatigue crack initiation to improve the fatigue resistance properties, and may be contained as needed.
  • the effect is provided at a Ca content of 0.0001% or more.
  • a Ca content of more than 0.005% non-metal inclusions are increased to decrease the fatigue resistance properties.
  • the upper limit thereof is 0.005%. Accordingly, when Ca is contained, the Ca content is 0.0001% to 0.005%.
  • Sb preferentially segregates on a surface, serves to suppress the entry of N from an atmosphere in the hot-rolling step or post-heat treatment step and suppress the decrease of the addition effect of B due to the formation of BN, and may be contained as needed.
  • the effect is provided at an Sb content of 0.0001% or more. At an Sb content of more than 0.10%, the effect is saturated. Thus, the upper limit is 0.10%. Accordingly, when Sb is contained, the Sb content is 0.0001% to 0.10%. More preferably, the Sb content is 0.0001% to 0.030%.
  • the steel member according to aspects of the present invention has a microstructure in which a ferrite phase extending from a surface to a depth of 200 ⁇ m in the thickness direction after the post-heat treatment has an average grain size of 1 to 50 ⁇ m and Ti carbide having a particle size of 1.0 to 20 nm is precipitated in the ferrite phase extending from a surface to a depth of 200 ⁇ m in the thickness direction, in which a difference (absolute value) between the average hardness of a portion extending from the surface to a depth of 200 ⁇ m in the thickness direction and the average hardness in the vicinity of the center in the thickness direction, excluding a center segregation portion, is ⁇ HV 50 points or less in terms of Vickers hardness (HV).
  • HV Vickers hardness
  • the microstructure of the steel member, the precipitation state of precipitates, and the cross-sectional hardness are important in achieving good fatigue resistance properties in the plastic strain range.
  • the ferrite phase extending from the surface to a depth of 200 ⁇ m in the thickness direction after the post-heat treatment has an average grain size of more than 50 ⁇ m, a large initial fatigue crack is formed early, thus making it difficult to ensure desired fatigue resistance properties in the plastic strain range.
  • the lower limit thereof is set thereto.
  • the ferrite phase used here refers to matrix iron phase with a body-centered cubic lattice and includes polygonal ferrite, acicular ferrite, Widmanstatten ferrite, bainitic ferrite, bainite, and low-carbon (C content: 1% or less) martensite structure.
  • Examples of a secondary phase other than the ferrite phase include austenite, carbide, pearlite, and high-carbon martensite (C content: more than 1%).
  • the main phase of the microstructure of the steel member according to aspects of the present invention is preferably the ferrite phase.
  • the “main phase” used here refers to a phase that constitutes, on a percent by volume basis, 51% or more, preferably 80% or more, and may be 100%.
  • the dimensions of Ti carbide in the ferrite phase extending from the surface to a depth of 200 ⁇ m in the thickness direction are important in achieving high surface hardness and good fatigue resistance properties in the plastic strain range.
  • the precipitation of Ti carbide having a particle size of 1.0 to 20 nm in the ferrite phase extending from the surface to a depth of 200 ⁇ m in the thickness direction inhibits the generation of an initial fatigue crack and reduces the size of the initial fatigue crack, thereby further improving the fatigue resistance properties in the plastic strain range.
  • the amount of Ti carbide precipitated with a particle size of 1.0 to 20 nm is not particularly specified. In addition to Ti carbide having a particle size of 1.0 to 20 nm, the precipitation of Ti carbide having different dimensions is acceptable.
  • the fact that the difference between the average hardness of the portion extending from the surface to a depth of 200 ⁇ m in the thickness direction and the average hardness in the vicinity of the center in the thickness direction, excluding the center segregation portion, is ⁇ HV 50 points or less is important in achieving good fatigue resistance properties in the plastic strain range.
  • the difference between the average hardness of the portion extending from the surface to a depth of 200 ⁇ m in the thickness direction and the average hardness in the vicinity of the center in the thickness direction, excluding the center segregation portion is more than ⁇ HV 50 points, a large initial fatigue crack is formed early, thereby making it difficult to ensure desired fatigue resistance properties in the plastic strain range.
  • the difference between the average hardness of the portion extending from the surface to a depth of 200 ⁇ m in the thickness direction and the average hardness in the vicinity of the center in the thickness direction, excluding the center segregation portion, is preferably ⁇ HV 50 points or less.
  • the micro-Vickers hardness values (HV(0.1)) at seven points located 25 ⁇ m apart from each other in the thickness direction in a portion extending from a depth of 50 ⁇ m to a depth of 200 ⁇ m were measured at a load of 0.1 kgf, and the average HV(0.1) s of the values was calculated.
  • micro-Vickers hardness values HV(0.1)
  • HV(0.1) c The micro-Vickers hardness values (HV(0.1)) at seven points located 25 ⁇ m apart from each other in the thickness direction in a central portion, excluding the center segregation portion, were measured, and the average HV(0.1) c thereof was calculated. Then the difference between the average HV(0.1) s and the average HV(0.1) c , i.e., HV(0.1) c —HV(0.1) s , was calculated.
  • the hot-rolled steel sheet (material hot-rolled steel sheet) for the steel member according to aspects of the present invention is particularly preferred in order to provide the steel member according to aspects of the present invention.
  • the material hot-rolled steel sheet according to aspects of the present invention contains, on a percent by mass basis, 0.031% to 0.200% Ti, in which 0.005% or more of Ti is present as dissolved Ti in the microstructure.
  • 0.005% or more of Ti can be precipitated as fine precipitates having a particle size of 20 nm or less in the microstructure of a steel member. This makes it possible to provide the steel member having good fatigue resistance properties in the plastic strain range and good strength properties.
  • the material hot-rolled steel sheet according to aspects of the present invention has the same composition as the steel member.
  • leading end portion and the trailing end portion of the material hot-rolled steel sheet according to aspects of the present invention are both end portions in the longitudinal direction, and preferably, each of the leading end portion and the trailing end portion has a thickness 5% to 50% larger than an intermediate portion (central portion in the longitudinal direction) other than the both end portions in the longitudinal direction.
  • a method for producing a steel member according to aspects of the present invention and a method for producing a hot-rolled steel sheet serving as a material of the steel member will be described below.
  • a temperature used in the following description is a surface temperature of a steel slab, unless otherwise specified.
  • a steel slab produced by casting a steel having the composition described above is used as a starting material.
  • a method for producing the starting material is not particularly limited. An example thereof is a method in which a molten steel having the composition described above is made by a common method with a converter or the like and then formed into a steel slab by a common casting method such as a continuous casting process.
  • a method for producing a hot-rolled steel sheet (material hot-rolled steel sheet) serving as a material of a steel member according to aspects of the present invention will first be described.
  • the material hot-rolled steel sheet according to aspects of the present invention can be produced by hot-rolling a steel slab containing 0.031% to 0.200% Ti under predetermined conditions.
  • a slab extraction temperature in a hot-rolling step affects the size of precipitates and the amount of dissolved Ti after the hot rolling in accordance with the state of re-dissolution or precipitation of Ti in steel and thus is important in ensuring good fatigue resistance properties after post-heat treatment.
  • T Ti equilibrium dissolution temperature
  • the slab extraction temperature is preferably 1,620 K or lower from the viewpoint of preventing an increase in grain size
  • a slab soaking time time to hold the slab at a temperature higher than the equilibrium dissolution temperature T Ti ) is preferably 10 minutes or more from the viewpoint of ensuring a uniform dissolution state of Ti and a sufficient dissolution time.
  • the finish rolling temperature in the hot rolling is lower than T Ti —400° C.
  • additional shear strain due to upper and lower rolls in portions near surfaces or strain-induced precipitation due to heat removal by rolls and cooling water is induced.
  • the amount of dissolved Ti present in portions (extending from the front and back surfaces to a depth of 200 ⁇ m) near the surfaces is lower than 0.005% in the stage of the material hot-rolled steel sheet, thereby failing to provide excellent fatigue resistance properties in the plastic strain range after the post-heat treatment.
  • the finish rolling temperature in the hot rolling is equal to or higher than T Ti 400° C.
  • 0.005% or more of Ti is present as dissolved Ti in the portions near the surfaces in the stage of the material hot-rolled steel sheet.
  • the heat treatment subsequent to the forming processing enables 0.005% or more of Ti to be precipitated as fine precipitates having a particle size of 20 nm or less, thereby providing excellent fatigue resistance properties in the plastic strain range.
  • the coiling temperature When the coiling temperature is higher than T Ti —500° C., the precipitation of Ti precipitates is promoted until coil is cooled.
  • the amount of dissolved Ti present in the stage of the material hot-rolled steel sheet is less than 0.005%, thereby failing to provide excellent fatigue crack growth resistance properties in the plastic strain range.
  • the coiling temperature is equal to or lower than T Ti —500° C., 0.005% or more of Ti is present as dissolved Ti in the portions near the surfaces in the stage of the material hot-rolled steel sheet.
  • the heat treatment subsequent to the forming processing enables 0.005% or more of Ti to be precipitated as fine precipitates having a particle size of 20 nm or less, thereby providing excellent fatigue crack growth resistance properties in the plastic strain range.
  • the finish rolling temperature and the coiling temperature are a surface temperature in the central portion of the coil in the width direction.
  • the average cooling rate is determined from the surface temperature.
  • a hot-rolled steel sheet (material hot-rolled steel sheet) in which 0.005% or more Ti is present as dissolved Ti in the microstructure is obtained.
  • the steel member according to aspects of the present invention is produced by subjecting the material hot-rolled steel sheet to forming processing and then performing predetermined heat treatment.
  • the forming processing is not particularly limited.
  • the steel member is a steel pipe
  • pipe making is exemplified.
  • the steel member is a welded steel pipe
  • welding may be performed after the pipe making.
  • the steel member is a formed component such as automotive structural member, press working and so forth are exemplified.
  • heat treatment is performed under conditions described below.
  • the material hot-rolled steel sheet is subjected to forming processing and then heat treatment including heating to a temperature higher than 550° C. and 1,050° C. or lower and then cooling at an average cooling rate of 10° C./s or more in the temperature range of 550° C. to 400° C., so that 0.005% or more of Ti precipitates as fine precipitates having a particle size of 20 nm or less, thereby providing excellent fatigue resistance properties in the plastic strain range.
  • the heating temperature is 550° C. or lower, dissolved Ti does not precipitate as fine precipitates having a particle size of 20 nm or less, thereby failing to provide excellent fatigue resistance properties in the plastic strain range.
  • the ferrite phase When the heating temperature is higher than 1,050° C., the ferrite phase has a grain size of more than 50 ⁇ m, thus making it difficult to provide excellent fatigue resistance properties in the plastic strain range.
  • the cooling rate in the temperature range of 550° C. to 400° C. is less than 10° C./s, sufficient strength (YS ⁇ 770 MPa) is not obtained.
  • the heating temperature is more preferably in the range of 700° C. to 1,000° C.
  • the welded steel pipe is produced by, but not particularly limited to, the following procedure: A material hot-rolled steel sheet is slit into a predetermined width as rolled or after one or more treatments selected from pickling, cold rolling, annealing, and coating, as needed. One or more coils are joined in the longitudinal direction by welding and formed into a shape with a substantially circular cross section by roll forming or press forming. End portions are joined by, for example, high-frequency electric resistance welding or laser welding. The resulting article is heated on- or off-line to a temperature higher than 550° C. and 1,050° C. or lower, cooled at an average cooling rate of 10° C./s or more in the temperature range of 550° C. to 400° C., and coiled to provide a coiled steel pipe.
  • the formed component is produced by the following procedure: A material hot-rolled steel sheet is subjected to blanking into a predetermined size as rolled or after one or more treatments selected from pickling, cold rolling, annealing, and coating, as needed, and is subjected to forming processing into a component.
  • the component is heated to a temperature higher than 550° C. and 1,050° C. or lower and cooled at an average cooling rate of 10° C./s or more in the temperature range of 550° C. to 400° C.
  • 0.0.05% or more of Ti precipitates as fine precipitates having a particle size of 20 nm or less, thus providing excellent fatigue resistance properties in the plastic strain range.
  • Steel slabs having compositions (types of steels: C to L) presented in Table 1 were extracted from a heating furnace at a slab surface temperature of about 1,220° C. and a slab center temperature of about 1,210° C.
  • the steel slabs were subjected to hot rolling including a finish rolling reduction of 91%, a finish rolling temperature of about 860° C. in the central portion of the coil in the width direction, a minimum finish rolling temperature of about 850° C. in the central portion of the coil in the width direction, cooling at an average cooling rate of about 20° C./s in the temperature range of T Ti —400° C. to T Ti —500° C., and a coiling temperature of about 560° C., thereby providing material hot-rolled steel sheets (Nos. 3 to 12) (thickness: about 5 mm, the leading and trailing end portions having a thickness about 10% larger than the central portion in the longitudinal direction).
  • a material hot-rolled steel sheet (No. 1) was produced in the same manner as above, except that a steel slab having a composition (type of steel: A) presented in Table 1 was extracted from the heating furnace at a slab surface temperature of about 1,250° C. and a slab center temperature of about 1,245° C.
  • Material hot-rolled steel sheets (Nos. 2 and 13) were produced in the same manner as above, except that steel slabs having compositions (types of steels: B and M) presented in Table 1 were extracted from the heating furnace at a slab surface temperature of about 1,335° C. and a slab center temperature of about 1,335° C. and the finish rolling temperature of the central portion of the coil in the width direction was about 940° C.
  • These material hot-rolled steel sheets were pickled, slit into a predetermined width dimension, and continuously formed into open pipes.
  • the open pipes were subjected to electric resistance welding by high-frequency resistance welding to form welded steel pipes having an outside diameter of 50.8 mm and a thickness of about 5 mm at a width drawing rate of 4%.
  • the entirety of each of the welded steel pipes were subjected to heat treatment including continuous high-frequency heating to a heating temperature of 920° C. for a holding time of about 5 seconds and then mist cooling with water from the outer surface at an average cooling rate of about 50° C./s in the temperature range of 550° C. to 400° C.
  • Test pieces were collected from these welded steel pipes. A microstructure observation test, quantitative tests for precipitates and the amount dissolved, a tensile test, a fatigue test in a plastic strain range, and a low-temperature toughness test were performed. Test methods were described below.
  • Test pieces for microstructure observation were collected in such a manner that sections of the welded steel pipes in the circumferential direction served as observation surfaces.
  • the test pieces were polished and etched with nital.
  • the microstructures were observed with a scanning electron microscope ( ⁇ 3,000). A boundary when the tilt angle between adjacent grains was 15° or more was defined as a grain boundary, and the average grain size of a ferrite phase was determined by an electron backscatter diffraction (EBSD) technique.
  • EBSD electron backscatter diffraction
  • a value was determined by measuring grain sizes at three points located 50 ⁇ m apart from each other in the thickness direction in a portion extending from a depth of 50 to a depth of 200 ⁇ m and averaging the resulting grain sizes, and a value was determined by measuring grain sizes at three points located 50 ⁇ m apart from each other in the thickness direction in a central portion, excluding the center segregation portion, and averaging the resulting grain sizes.
  • Test pieces having a size of 20 mm ⁇ 30 mm were cut from these welded steel pipes. Each of the test pieces was subjected to constant-current electrolysis at a current density of 20 mA/cm 2 in a 10% AA-containing electrolytic solution (10% by volume of acetylacetone-1% by mass of tetramethylammonium chloride-methanol) so as to be reduced in weight by about 0.2 g. After the electrolysis, the test piece having surfaces to which precipitates adhere was taken out of the electrolytic solution and immersed in an aqueous solution of sodium hexametaphosphate (500 mg/l) (hereinafter, referred to as an “aqueous solution of SHMP”).
  • an aqueous solution of SHMP aqueous solution of sodium hexametaphosphate
  • the absolute amounts of Ti in the residues on the filters and in the filtrate were measured to determine Tilp, which was the absolute amount of Ti in the precipitates having a particle size of more than 100 nm, Timp, which was the absolute amount of Ti in the precipitates having a particle size of 100 nm or less and more than 20 nm, and Tisp, which was the absolute amount of Ti in the precipitates having a particle size of 20 nm or less.
  • the mass reduced by the electrolysis was determined by measuring the mass of the test piece after the separation of the precipitates and subtracting the resulting mass from the mass of the test piece before electrolysis.
  • the content of Ti in a dissolved state was determined as follows: The electrolytic solution after the electrolysis was used as a solution for analysis. The concentrations of Ti and Fe serving as a reference element in the solution were measured by ICP mass spectrometry. The concentration ratio of Ti to Fe was calculated on the basis of the resulting concentrations. The ratio was multiplied by the Fe content of the test piece to determine the dissolved Ti content. The Fe content of the test piece can be determined by subtracting the total content of elements other than Fe from 100%. The quantitative tests for the precipitates and the amount dissolved were also performed on the welded steel pipes before the post-heat treatment in addition to the welded steel pipes after the post-heat treatment.
  • JIS No. 12 test pieces were cut from these welded steel pipes in accordance with JIS Z 2201 in such a manner that the L-direction coincided with a tensile direction.
  • the tensile test was performed in accordance with JIS Z 2241 to determine tensile properties (tensile strength TS, yield strength YS, and total elongation El).
  • Each of the welded steel pipes was uncoiled in such a manner that the longitudinal direction of the pipe (L-direction) coincided with the length of a specimen.
  • a Charpy specimen (2 mm V-notch, 1 ⁇ 2 size) was cut out in accordance with JIS Z 2202.
  • a Charpy impact test was performed in accordance with JIS Z 2242. The fracture appearance transition temperature was determined to evaluate the low-temperature toughness.
  • the average hardness (HV(0.1) s ) of a portion extending from a surface to a depth of 200 ⁇ m in the thickness direction and the average hardness (HV(0.1) c ) in the vicinity of the center in the thickness direction, excluding a center segregation portion, were measured by the foregoing method.
  • a difference between the average hardness of the portion extending from the surface to a depth of 200 ⁇ m in the thickness direction and the average hardness in the vicinity of the center in the thickness direction, excluding the center segregation portion, i.e., ⁇ HV (HV(0.1) c -HV(0.1) s ) was calculated.
  • the number of cycles in the fatigue test in the plastic strain range is 1,000 or more cycles, which indicates good fatigue resistance properties in the plastic strain range.
  • YS is 770 MPa or more, which indicates good strength properties.
  • the Charpy fracture appearance transition temperature is ⁇ 30° C. or lower, which indicates good low-temperature toughness.
  • No. 12 in which the component composition of the steel does not satisfy the range of the present invention and less than 0.005% of Ti is precipitated as precipitates having a particle size of 20 nm or less
  • No. 13 in which the component composition of the steel does not satisfy the range of the present invention, desired fatigue resistance properties in the plastic strain range are not provided.
  • Steel slabs having component compositions of the types of steels A, B, and C presented in Table 1 were hot-rolled under conditions presented in Table 3 to form material hot-rolled steel sheets (thickness: about 5 mm, the leading and trailing end portions having a thickness about 10% larger than the central portion in the longitudinal direction).
  • These material hot-rolled steel sheets were pickled, slit into a predetermined width dimension, and continuously formed into open pipes.
  • the open pipes were subjected to electric resistance welding by high-frequency resistance welding to form welded steel pipes having an outside diameter of 50.8 mm and a thickness of about 5 mm at a width drawing rate of 4%.
  • the entirety of each of the welded steel pipes was subjected to heat treatment including continuous high-frequency heating under conditions presented in Table 3.
  • Test pieces were collected from these welded steel pipes. A microstructure observation test, quantitative tests for precipitates and the amount dissolved, a tensile test, a fatigue test in a plastic strain range, a low-temperature toughness test, and Vickers hardness measurement were performed.
  • a material hot-rolled steel sheet was subjected to pickling, blanking into a predetermined size, and press working to form a formed component.
  • the formed component was heat-treated under conditions presented in Table 3. Test pieces were collected from the formed component, and the tests described above were performed.
  • Table 4 presents the results. Table 3 and 4 also present the results of Nos. 1 to 3.
  • the number of cycles in the fatigue test in the plastic strain range is 1,000 or more cycles, which indicates good fatigue resistance properties in the plastic strain range.
  • YS is 770 MPa or more, which indicates good strength properties.
  • the Charpy fracture appearance transition temperature is ⁇ 30° C. or lower, which indicates good low-temperature toughness.
  • desired fatigue resistance properties in the plastic strain range are not provided.

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