US20090250146A1 - High Strength Thick-Gauge Electric-Resistance Welded Steel Pipe Excellent in Hardenability, Hot Workability and Fatigue Strength and Method of Production of the Same - Google Patents

High Strength Thick-Gauge Electric-Resistance Welded Steel Pipe Excellent in Hardenability, Hot Workability and Fatigue Strength and Method of Production of the Same Download PDF

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US20090250146A1
US20090250146A1 US11/990,477 US99047706A US2009250146A1 US 20090250146 A1 US20090250146 A1 US 20090250146A1 US 99047706 A US99047706 A US 99047706A US 2009250146 A1 US2009250146 A1 US 2009250146A1
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steel pipe
resistance welded
welded steel
hardenability
electric
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Tetsuo Ishitsuka
Hiroyuki Mimura
Motofumi Koyuba
Naoki Takasugi
Takahiro Ichiyama
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Nippon Steel Corp
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Assigned to NIPPON STEEL CORPORATION reassignment NIPPON STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: ICHIYAMA, TAKAHIRO, ISHITSUKA, TETSUO, KOYUBA, MOTOFUMI, MIMURA, HIROYUKI, TAKASUGI, NAOKI
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60G—VEHICLE SUSPENSION ARRANGEMENTS
    • B60G21/00—Interconnection systems for two or more resiliently-suspended wheels, e.g. for stabilising a vehicle body with respect to acceleration, deceleration or centrifugal forces
    • B60G21/02—Interconnection systems for two or more resiliently-suspended wheels, e.g. for stabilising a vehicle body with respect to acceleration, deceleration or centrifugal forces permanently interconnected
    • B60G21/04—Interconnection systems for two or more resiliently-suspended wheels, e.g. for stabilising a vehicle body with respect to acceleration, deceleration or centrifugal forces permanently interconnected mechanically
    • B60G21/05—Interconnection systems for two or more resiliently-suspended wheels, e.g. for stabilising a vehicle body with respect to acceleration, deceleration or centrifugal forces permanently interconnected mechanically between wheels on the same axle but on different sides of the vehicle, i.e. the left and right wheel suspensions being interconnected
    • B60G21/055—Stabiliser bars
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—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
    • C22C38/02—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/22—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
    • C22C38/26—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60G—VEHICLE SUSPENSION ARRANGEMENTS
    • B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
    • B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
    • B60G2206/40—Constructional features of dampers and/or springs
    • B60G2206/42—Springs
    • B60G2206/427—Stabiliser bars or tubes
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60G—VEHICLE SUSPENSION ARRANGEMENTS
    • B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
    • B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
    • B60G2206/80—Manufacturing procedures
    • B60G2206/82—Joining
    • B60G2206/8201—Joining by welding
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D9/14—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes wear-resistant or pressure-resistant pipes

Definitions

  • the present invention relates to high strength thick-gauge electric-resistance welded steel pipe excellent in hardenability, hot workability, and fatigue strength suitable for a hollow stabilizer for securing running stability of an automobile and method of production of the same.
  • the chasses of automobiles are being reduced in weight.
  • the stabilizer easing the rolling of the chassis at the time of cornering of the automobile and securing stability of the chassis at the time of high speed running may be mentioned as being part of this.
  • stabilizers have been produced by working a steel bar or other solid material into the required shape, but to lighten the weight, they are increasingly being produced using seamless steel pipe, electric-resistance welded steel pipe, or other hollow members.
  • WO2002/070767 discloses electric-resistance welded steel pipe for a stabilizer restricted in composition so as to obtain a uniform metal structure of the electric-resistance welded part and matrix material part, a small difference in hardness between the electric-resistance welded part and matrix material part, and excellent workability.
  • Japanese Unexamined Patent Publication No. 2004-011009 discloses electric-resistance welded steel pipe for a hollow stabilizer limiting the contents of Ti and N to secure hardenability.
  • Japanese Unexamined Patent Publication No. 2004-009126 proposes electric-resistance welded steel pipe for a hollow stabilizer having a ratio t/D of the thickness t and outside diameter D of the steel pipe of 20% or more and a tensile strength of 400 to 755 N/mm 2 and discloses to increase the thickness by stretch reducing rolling.
  • Japanese Unexamined Patent Publication No. 2003-201543 proposes high strength steel pipe for an automobile structural member obtained by stretch rolling a material pipe, having a tensile strength of over 580 MPa, having a yield ratio of 70% or less, and excellent in workability to withstand hydroforming
  • Japanese Unexamined Patent Publication No. 2004-292922 proposes a method of production of high tension steel pipe specifying the heating temperature, diameter reduction rate, etc. at the time of stretch rolling to obtain superior bending, stretching, pipe end flattening, and other composite secondary workability.
  • Japanese Unexamined Patent Publication No. 2005-076047 discloses a method of production of a hollow stabilizer forming a material pipe into a stabilizer shape by cold bending, quenching this shaped steel pipe, and heat treating it for tempering, which method of production of a hollow stabilizer rolls said material pipe at a rolling temperature 600 to 850° C. and a cumulative diameter reduction rate of 40% or more after heat treating the master steel pipe so as to improve the fatigue resistance characteristics.
  • Japanese Patent No. 3,653,871 discloses electric-resistance welded steel pipe for quenching use containing, by mass %, C: 0.15 to 0.3%, Mn: 0.5 to 2.0%, and Cu: 0.05 to 0.30%, one or more elements selected from Si ⁇ 0.41%, P ⁇ 0.02%, Al ⁇ 0.03%, Nb ⁇ 0.020%, B ⁇ 0.001%, Ti ⁇ 0.01%, and Cr ⁇ 0.42%, unavoidable impurities limited to 0 ⁇ Ni+Mo ⁇ 0.15% and S ⁇ 0.003%, and the balance of Fe to give excellent workability and a high residual strength rate after penetration of water due to corrosion.
  • a stabilizer is produced by further stretch rolling electric-resistance welded steel pipe to obtain thick-gauge electric-resistance welded steel pipe having the required thickness/outside diameter ratio and then 1) forming it into the required shape by bending or other cold forming, heating and water cooling this for quenching, then tempering it or 2) heating the thick-gauge electric-resistance welded steel pipe, forming it to the required shape by pressing or other hot forming, then water cooling it for quenching, then tempering it.
  • the latter method of hot forming is superior compared with the former cold forming in that the forming work is easier and even complicated shapes can be handled, so this is advantageous as a production process.
  • the material is shaped after heating, so the time until quenching becomes long—leading to a drop in the temperature of the formed member, contact between the press die and the master steel pipe (electric-resistance welded steel pipe) causes a drop in temperature, and the formation of heating scale causes uneven temperature, so it becomes difficult to secure a sufficient hardened state overall and insufficient hardening is liable to occur.
  • a steel material for steel pipe better in hardenability is therefore necessary.
  • the general practice is to use B-containing steel having a high hardenability for the stabilizer steel, but B-containing steel has the major problems that it is poor in hot workability and is susceptible to cracking and flaws at the time of hot forming. Further, B-containing steel sometimes falls in fatigue strength—an important characteristic for a stabilizer.
  • the stabilizer use electric-resistance welded steel pipes and high strength steel pipes described in WO2002/070767, Japanese Unexamined Patent Publication No. 2004-011009, Japanese Unexamined Patent Publication No. 2004-009126, Japanese Unexamined Patent Publication No. 2003-201543, Japanese Unexamined Patent Publication No. 2004-292922, Japanese Unexamined Patent Publication No. 2005-076047, Japanese Unexamined Patent Publication No. 2005-076047, Japanese Patent No. 3653871, etc. are useful as steel pipe for automobile structural members, but, as explained above, cannot sufficiently handle the problems arising from changes in the process in the method of production of automobile structural members. Further, they cannot be said to be sufficient in terms of fatigue characteristics either.
  • the present invention in consideration of the above problems, has as its object the provision of high strength thick-gauge electric-resistance welded steel pipe having sufficient hardenability and excellent in hot workability and fatigue strength and a method of production of the same.
  • the thick-gauge electric-resistance welded steel pipe of the present invention was devised to achieve this object. It increases the C as much as possible to improve the strength (hardness) to an extent not impairing the weldability and toughness, strictly limits the range of the N content to improve the hot workability and fatigue strength, and adjusts the composition of the steel material so that the critical cooling rate V c becomes a specific range so as to thereby secure the hardenability. Further, in the production of the thick-gauge electric-resistance welded steel pipe of the present invention, the heating temperature and the cross-section reduction rate are set to specific ranges for the stretch reducing rolling of the electric-resistance welded steel pipe.
  • the gist of this is as follows:
  • a method of production of high strength thick-gauge electric-resistance welded steel pipe excellent in hardenability, hot workability, and fatigue strength characterized by heating electric-resistance welded steel pipe having the ingredients as set forth in any one of (1) to (4) to 800 to 1200° C. and stretch reducing rolling it by a cross-section-reduction rate of 40 to 80% in range.
  • the thick-gauge electric-resistance welded steel pipe of the present invention is extremely excellent in hardenability, so in the production of a stabilizer or other automobile structural member, for example, it is possible to obtain a sufficient hardening effect immediately after hot forming.
  • the quenching means is not limited to water cooling. It is also possible to obtain a sufficient hardening effect by oil quenching which has a smaller cooling rate than water cooling.
  • the hot workability is excellent, cracks or flaws are difficult to occur even with hot forming when producing automobile members.
  • the fatigue strength is excellent, so there is high durability against repeated load. Further, the strength is high, so the stabilizers and other automobile structural members may be lightened in weight more.
  • FIG. 1 is a view of the relationship between hardness of a steel material for thick-gauge electric-resistance welded steel pipe after quenching and tempering and the amount of C.
  • FIG. 2 is a view of the relationship between the reduction in area at 850° C. and the N content.
  • FIG. 3 is view for explaining the method of the fatigue test.
  • the inventors investigated to improve the hardenability, hot workability, and fatigue strength of thick-gauge electric-resistance welded steel pipe for a stabilizer and further to increase the strength thereof.
  • FIG. 1 shows the relationship between the change in hardness after water-cooled quenching and tempering and the amount of C.
  • FIG. 1 simultaneously shows the relationship between the hardnesses of 100% and 90% martensite structures and the amount of C. From Test Materials A, B, and C, it is learned that if hardening to at least a 90% martensite structure, a hardness of 10% or more of the conventional material can be secured. Therefore, as an indicator of the hardenability, for example, it is sufficient to use the critical cooling rate Vc (° C./sec) giving a 90% martensite structure known in the past from Tetsu to Hagane, 74 (1988), p. 1073. This is usually expressed by the following equation ⁇ 1>:
  • the amount of C is increased and the ingredients are selected so that the critical cooling rate Vc shown in ⁇ 1> becomes less than 30° C./sec.
  • the inventors investigated the causes for the poor workability of the B-containing steel in the 600 to 900° C. temperature region where hot forming is performed and as a result found the fact that the amount of N in the steel has a major effect on the hot deformation resistance. That is, the inventors fabricated test materials comprised of 0.3C-1.1Mn-0.020Ti-0.0013B steel changed in N content from 0.01% to 0.001% in range, conducted single-axis tensile tests at 850° C. within the temperature range of hot forming, and measured the reduction in area at that time.
  • FIG. 2 shows the relationship between the reduction of area at 850° C. and the N content.
  • the smaller the content of N the larger the reduction of area, that is, the better the hot workability. If the content of N falls to 0.005%, the reduction of area rises to 40%, the line where hot forming generally becomes possible, while if the content of N is less than 0.004%, the reduction of area reaches 50% or more where hot forming can be performed without problem.
  • the inventors discovered that the reason was that due to the N content falling, the amount of TiN precipitating in the temperature region for hot forming falls. That is, in general, B-containing steel must contain Ti with its high effect of immobilizing N so as to suppress the precipitation of BN reducing the effect of B in improving the hardenability. Due to this, with B-containing steel, the inventors found that the hot workability was poor since TiN precipitated in the hot forming temperature region.
  • massive precipitation of TiN causes a drop in the fatigue strength—an important characteristic of a stabilizer. Further, massive precipitation of TiN is also disadvantageous for toughness. On the other hand, due to the suitable presence of TiN, the growth of ⁇ grains is suppressed and improvement of toughness is contributed to. Therefore, by strictly controlling the N content, which had not been that strictly controlled in the past, it becomes possible to obtain B-containing steel with desirable hot workability, fatigue strength, and toughness.
  • the thick-gauge electric-resistance welded steel pipe of the present invention is raised in C content and suppressed in N content to a small amount so as to improve the strength and improve the hot workability and fatigue strength and is suitably controlled in other ingredients so as to lower the critical cooling rate Vc and improve the hardenability.
  • C is an element entering into solid solution or precipitating in a base material and increasing the strength of the steel.
  • Si is an alloy element contributing to solution strengthening. To obtain this effect, 0.01% or more must be contained. Further, there is the effect of increasing the tempering softening resistance. To obtain this effect, 0.25% or more must be added. On the one hand, if added over 0.5%, the toughness falls. Therefore, the content is made 0.01 to 0.50% in range. Note that preferably the content is 0.25 to 0.35%.
  • Mn is an element for increasing the hardenability. If the content is less than 0.8%, the effect of increasing the hardenability cannot be sufficiently secured, while if over 1.5%, the weldability and weld zone soundness are detrimentally affected, so the content is made 0.8 to 1.5% in range.
  • Al is an element required as a deoxidation material for molten steel. Further, it is an element for immobilizing N. Therefore, the amount has a major effect on the crystal grain size or the mechanical properties. If the content is over 0.05%, the crystal grain size coarsens and the toughness drops, the nonmetallic inclusions increase, and flaws easily occur on the product surface, so the content is made 0.05% or less. Note that preferably the content is 0.03% or less.
  • B is an element which, when added in a fine amount, greatly improves the hardenability of the steel material. Further, there is the effect of grain boundary strengthening. If the content is less than 0.0005%, it is not possible to expect the effect of improving the hardenability. On the one hand, if over 0.01%, coarse B-containing phases tend to be produced and embrittlement easily occurs. Therefore, the content is made 0.0005% to 0.01%. Note that preferably the content is over 0.0010 to 0.0020%.
  • N is an element having the effects of causing the precipitation of nitrides or carbonitrides and increasing the strength.
  • the drop in hardenability due to the precipitation of BN as explained above, the drop in the hot workability and fatigue strength due to the precipitation of TiN due to the Ti added to prevent the precipitation of BN, and further the drop in toughness become problems.
  • TiN has the effect of suppressing coarsening of the ⁇ grains at the time of high temperature and increasing the toughness. For this reason, to optimize the balance of the hot workability, fatigue strength, and toughness, the content is made 0.001 to 0.005% in range. Note that preferably the content is 0.002 to less than 0.004%.
  • Ti acts to immobilize the N in the steel as TiN and suppress the precipitation of BN so as to stably and effectively improve the hardenability by the addition of B. Therefore, addition in an amount of 3.42 times the N content is necessary at the minimum as in the stoichiochemical level of TiN.
  • the range of the Ti content is automatically determined from the above range of N content.
  • the content is made higher than the theoretical value of 0.005 or more, while if over 0.05%, the toughness tends to deteriorate, so the content is made 0.005 to 0.05% in range. Note that preferably the content is 0.01 to 0.02%.
  • P is an element having a detrimental effect on the weld crack resistance and toughness, so is limited to not more than 0.05%. Note that preferably the content is 0.03% or less.
  • the content is limited to 0.05% or less. Note that preferably the content is 0.01% or less.
  • the thick-gauge electric-resistance welded steel pipe of the present invention may contain, in accordance with need, one or more of Cr, Mo, V, and Ni and/or at least one of Ca and Nb.
  • Cr is an element improving the hardenability. Further, it has the effect of causing the precipitation of M 23 C 6 type carbides in the base material and has the action of increasing the strength and increasing the fineness of the carbides. If the content is less than 0.1%, these actions and effects cannot be sufficiently expected. Further, if over 1%, defects easily occur at the time of electric-resistance welding. Therefore, the content is made 0.1 to 1% in range. Note that preferably the content is 0.1 to 0.6%.
  • Mo is an element having the effect of improving the hardenability and has the effect of causing solution strengthening. If the content is less than 0.05%, these effects cannot be sufficiently expected. On the one hand, if over 1%, coarse carbides easily precipitate and the toughness is deteriorated, so the content is made 0.05 to 1% in range. Note that preferably the content is 0.1 to 0.5%.
  • Ni is an element having the effect of improving the hardenability and toughness. If the content is less than 0.1%, this effect cannot be expected, while if over 1%, there is a possibility of residual ⁇ even after quenching and the fatigue durability is degraded. Therefore, the content is made 0.1 to 1% in range. Note that preferably the content is 0.015 to 0.5%.
  • V is an element having the effect of improving the hardenability and has the effect of precipitation strengthening by the V carbonitrides. If the content is less than 0.01%, these effects cannot be sufficiently expected, while if over 0.5%, coarse carbides easily precipitate and the toughness is degraded, so the content is made 0.01 to 0.5% in range. Note that preferably the content is 0.02 to 0.05%.
  • Nb has the effect of precipitation strengthening by Nb carbonitrides and further has the effect of increasing the fineness of the former austenite grains and increasing the toughness. Further, there is the effect of suppression of the decarbrization of the surface.
  • the content is less than 0.01%, the effect of improvement of the strength and toughness is not sufficient, while if contained over 0.1%, the carbides increase and the toughness drops. Therefore, the content is made 0.01 to 0.1% in range. Note that preferably the content is 0.02 to 0.04%.
  • Ca is an element having the effect of making the oxides and sulfides spherical in shape and improving the workability. If the content is less than 0.0002%, these effects cannot be sufficiently expected, while if over 0.005%, the oxides in the steel increase and the toughness is degraded, so the content is made 0.0002 to 0.005% in range. Note that preferably the content is 0.0002 to 0.004%.
  • the lower limit of t/D is set to over 0.15, while from the viewpoint of the producibility and reduction of weight, the upper limit is set to 0.30.
  • Molten steel produced to have the required chemical composition is cast to a slab or is formed into an ingot once, then is hot rolled to a slab. This cast or rolled (slab is then hot rolled to obtain a hot rolled steel sheet.
  • This hot rolled steel sheet is formed into an electric-resistance welded steel pipe by the method of production of ordinary electric-resistance welded steel pipe, for example, hot or cold electric-resistance welding.
  • the thick-gauge electric-resistance welded steel pipe of the present invention has a ratio of thickness/outside diameter of the steel pipe explained above, that is, t/D, of over 0.15 to 0.30.
  • t/D thickness/outside diameter of the steel pipe explained above
  • the electric-resistance welded steel pipe making machine has the ability to produce electric-resistance welded steel pipe having such a range of thickness/outside diameter ratio, it is possible to use the hot rolled steel sheet to directly produce the thick-gauge electric-resistance welded steel pipe of the present invention.
  • an electric-resistance welded steel pipe having a thickness/outside diameter ratio t/D of 0.15 or less can be produced by an ordinary electric-resistance welded steel pipe making machine, but if the t/D is over 0.15, the production capacity is exceeded, so with an ordinary electric-resistance welded steel pipe making machine, it is often difficult to directly produce a thick-gauge electric-resistance welded steel pipe of the present invention having a t/D of over 0.15 to 0.30.
  • an ordinary electric-resistance welded steel pipe making machine is used to produce electric-resistance welded steel pipe having a thickness/outside diameter ratio of 0.15 or less (also called a “master pipe” here), then this is hot stretch rolled to produce thick-gauge electric-resistance welded steel pipe having a thickness/outside diameter ratio of over 0.15 to 0.30.
  • the stretch reducing rolling may be performed using a stretch reducer etc.
  • a stretch reducer is a rolling mill provided with a plurality of rolling stands having three or four rolls around a rolling axis in series along the rolling axis.
  • the steel pipe in the stretch reducing rolling, the steel pipe is reduced in outside diameter by the reduction force on the outside diameter, while the thickness is increased.
  • the thickness is reduced due to the tension acting on the axial direction of the steel pipe.
  • the final thickness is determined by the balance of the two.
  • the thickness of the thus stretch reducing rolled steel pipe is mainly determined by the tension between the rolling stands, so it is necessary to find the tension between rolling stands for obtaining the target thickness from rolling theory etc. and set the roll speeds of the rolling stands on which this tension acts.
  • the present invention heats said electric-resistance welded steel pipe (master pipe) to 800 to 1200° C. and cross-section reduction rate 40 to 80% and hot stretch rolls it to obtain thick-gauge electric-resistance welded steel pipe having a thickness/outside diameter ratio of over 0.15 to 0.30.
  • cross-section reduction rate is the (outside diameter of the steel pipe before stretch reducing ⁇ outside diameter of the steel pipe after stretch reducing)/outside diameter of steel pipe before stretch reducing ⁇ 100 (%).
  • the heating temperature of the electric-resistance welded steel pipe at the time of stretch reducing rolling is less than 800° C., the deformation resistance is large, while if over 1200° C., there is remarkable formation of heat scale and the surface properties deteriorate. Therefore, the heating temperature is made 800 to 1200° C. in range.
  • the cross-section reduction rate at the time of stretch reducing rolling is less than 40%, the compression force is insufficient. It is therefore difficult to make thick-gauge electric-resistance welded steel pipe having a thickness/outside diameter ratio of over 0.15 to 0.30 from electric-resistance welded steel pipe (master pipe) having a thickness/outside diameter ratio of 0.15 or less.
  • the cross-section reduction rate is over 80%, there is remarkable formation of surface defects on the steel pipe due to stretch reducing rolling and securing a uniform surface becomes difficult. Therefore, the cross-section reduction rate in the stretch reducing rolling is made 40 to 80%.
  • the stretch reducer used for the stretch reducing rolling is a rolling mill provided with a plurality of rolling stands having three rolls or four rolls around the rolling axis in series along the rolling axis.
  • the rolls of the adjoining rolling stands for example, the N and N+1 rolling stands
  • the rolls of the adjoining rolling stands are offset in phase.
  • the rolls are arranged offset in phase by exactly 60° while in the case of four-roll rolling stands, the rolls are arranged offset in phase by exactly 45°.
  • the inside shape of the cross-section vertical to the axial direction of the thick-gauge electric-resistance welded steel pipe produced by stretch reducing rolling is hexagonal when the stretch reducer is provided with three-roll rolling stands and is octagonal when it is provided with four-roll rolling stands.
  • the phase of the rolls in four continuous rolling stands of a stretch reducer (for example, N, N+1, N+2, and N+3 rolling stands) are offset by 30°, 60°, and 90° in the case of three-roll rolling stands and offset by 22.5°, 45°, and 67.5° in the case of four-roll rolling stands
  • the inner shape of the cross-section vertical to the axial direction of the thick-gauge electric-resistance welded steel pipe after stretch rolling (C section) is dodecagonal in the case of provision of three-roll rolling stands and hexadecagonal in the case of four-roll rolling stands.
  • the electric-resistance welded steel pipe produced by the Steel No. 1 of Table 2 was changed in cross-section reduction rate in the stretch reducing rolling to produce thick-gauge electric-resistance welded steel pipe having a thickness of 5 to 7.5 mm and an outside diameter 30 to 35 mm.
  • the obtained thick-gauge electric-resistance welded steel pipe was heated to 960° C., water cooled, quenched, and tempered at 300° C. ⁇ 1 hr and 350° C. ⁇ 1 hr. Test pieces were taken from this steel pipe and subjected to various types of tests so as to confirm the chararacteristics of the thick-gauge electric-resistance welded steel pipe of the present invention.
  • the hardness was obtained by measuring the center of thickness by Hv9.8N at five points and finding the average.
  • the hot workability was evaluated using a single-axis tensile test piece having a diameter of the parallel part of 6 mm, applying tension at 850° C., and finding the rate of reduction of the cross-sectional area of the broken part.
  • Steel No. 12 had a large critical cooling rate Vc, so was not sufficiently hardened and had an amount of C of a low 0.22%, so did not give sufficient hardness.
  • Steel No. 13 had too high an amount of N, so was poor in hot workability and also somewhat low in fatigue characteristics.
  • Steel No. 14 had an insufficient amount of C, so even with tempering at 300° C., the minimum necessary hardness required for an automobile structural member could not be obtained.
  • the present invention Steel Pipe Nos. a to e shown in Table 3 had sufficient fatigue strengths having sufficient cycles until break of over 50 ⁇ 10 3 .

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US20100047609A1 (en) * 2007-02-26 2010-02-25 Jfe Steel Corporation Electric resistance welded steel tube for heat treatment and method for manufacturing the same
US20140202600A1 (en) * 2010-04-15 2014-07-24 Nisshin Steel Co., Ltd. Method of making quenched and tempered steel pipe with high fatigue life
JP2015168845A (ja) * 2014-03-06 2015-09-28 新日鐵住金株式会社 疲労特性に優れた中空材とその製造方法
US10987714B2 (en) * 2019-05-28 2021-04-27 Hyundai Motor Company Method for forming vehicle body member
US20210310091A1 (en) * 2018-12-19 2021-10-07 Jfe Steel Corporation Electric resistance welded steel pipe or tube

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KR101271781B1 (ko) 2010-12-23 2013-06-07 주식회사 포스코 내마모성, 내식성 및 저온인성이 우수한 오일샌드 슬러리 파이프용 강판 및 그 제조방법
ES2691085T3 (es) * 2012-05-25 2018-11-23 Nippon Steel & Sumitomo Metal Corporation Estabilizador hueco, y tubo de acero para estabilizadores huecos y método para producir el mismo
US20150368768A1 (en) * 2013-01-31 2015-12-24 Jfe Steel Corporation Electric Resistance Welded Steel Pipe
CN103938098A (zh) * 2014-04-21 2014-07-23 河北钢铁股份有限公司唐山分公司 一种超高强度钢管及其连续生产方法
KR102232097B1 (ko) 2016-10-24 2021-03-24 제이에프이 스틸 가부시키가이샤 고강도 박육 중공 스태빌라이저용 전봉 강관 및 그 제조 방법
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US20210310091A1 (en) * 2018-12-19 2021-10-07 Jfe Steel Corporation Electric resistance welded steel pipe or tube
US10987714B2 (en) * 2019-05-28 2021-04-27 Hyundai Motor Company Method for forming vehicle body member

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