EP2952601B1 - Widerstandsgeschweisstes stahlrohr - Google Patents

Widerstandsgeschweisstes stahlrohr Download PDF

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EP2952601B1
EP2952601B1 EP14746008.3A EP14746008A EP2952601B1 EP 2952601 B1 EP2952601 B1 EP 2952601B1 EP 14746008 A EP14746008 A EP 14746008A EP 2952601 B1 EP2952601 B1 EP 2952601B1
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steel pipe
content
case
pearlite
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French (fr)
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EP2952601A1 (de
EP2952601A4 (de
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Masatoshi Aratani
Takatoshi Okabe
Shunsuke Toyoda
Yoshikazu Kawabata
Hiromichi Hori
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to an electric resistance welded steel pipe excellent in terms of fatigue characteristic.
  • Patent Literature 1 discloses a hollow drive axis which is made from a seamless steel pipe as a raw material, having a steel chemical composition controlled to be within a specified range, which is excellent not only in terms of cold workability as indicated by an austenite grain size number of 9 or more after a quenching treatment has been performed but also in terms of hardenability, toughness, and torsion fatigue strength (hereinafter, also simply referred to as fatigue strength), and which realizes a stable fatigue life.
  • Patent Literature 2 discloses a technique for increasing the strength of a steel pipe by using an electric resistance welded steel pipe having a steel chemical composition controlled to be within a specified range as a raw material and by performing a quenching-tempering treatment on a weld of ERW and a portion around the weld as a hardening treatment.
  • JPH08295989 discloses an electric resistance welded tube wherein the austenite crystal grain are suppressed in the time of subsequent heat processing by annealing, wherein the steel composition includes (wt.%) 0.41 C, 0.23 Si, 1.05 Mn, 0.001 S, 0.010 P, Al 0.008 and at least one of 0.1 Cu 0.1 Ni, 0.1 Cr and 0.1 Mo.
  • an electric resistance welded steel pipe is superior to a seamless steel pipe in terms of dimension accuracy
  • normalizing is not performed, there is a risk in that, since an electric resistance welded steel pipe has low toughness, brittle failure may occur in a practical use environment.
  • a drive shaft since local stress concentration occurs in a weld of ERW and in the vicinity of the weld due to cyclic shearing stress and bending stress being applied, there is a risk in that fatigue breaking may occur in a short time. Therefore, normalizing is a treatment which is very important in order to use an electric resistance welded steel pipe for a drive shaft and which significantly influences the properties of a steel pipe as a final product.
  • An object of the present invention is, in order to solve the problems described above, to provide an electric resistance welded steel pipe whose metallic microstructure and tensile strength after normalizing has been performed are less likely to be influenced by a cooling rate when normalizing is performed even in the case where high-carbon steel is used as a raw material of an electric resistance welded steel pipe and with which stable fatigue strength can be achieved.
  • the present inventors diligently conducted investigations in order to solve the problems described above, and as a result, found that, by controlling Al content in steel to be within an appropriate range, the metallic microstructure and tensile strength after normalizing has been performed become less likely to be influenced by a cooling rate after normalizing has been performed and that stable fatigue strength can be achieved. Moreover, it was found that, by controlling the prior austenite grain size to be within an appropriate range, it is possible to increase (1) the strength of pearlite and (2) fatigue crack propagation resistance of ferrite-pearlite steel without changing the tensile strength, which results in an increase in fatigue strength.
  • the present inventors manufactured hot-reduced steel pipes (having an outer diameter of 45 mm and a wall thickness of 4.5 mm), by using a hot-rolled steel sheets (coiled at a coiling temperature of 650°C) having a basic chemical composition in accordance with the steel specification SAE1541 (containing 0.42%C,1.5%Mn,0.0035%N) and Al in various amounts as a raw material, by performing roll forming and high-frequency resistance welding on the raw material in order to manufacture electric resistance welded steel pipes (having an outer diameter of 89 mm and a wall thickness of 4.7 mm), and by thereafter performing hot reducing on the formed and welded pipes.
  • Fig. 1 illustrates the relationship between a cooling rate for normalizing and HV hardness (Vickers hardness). It is clarified that, in the case where the Al content is 0.005% or less, almost constant HV hardness is achieved for a wide cooling rate range, that, in the case where the Al content is 0.007% or more, HV hardness is strongly influenced by the cooling rate, and that, in the case where the cooling rate is low, there is a sharp decrease in HV hardness.
  • Fig. 2 illustrates the relationship between the Al content and a lamellar spacing
  • Fig. 3 illustrates the relationship between the Al content and a prior austenite grain size
  • Fig. 4 illustrates the relationship between the Al content and torsion fatigue strength.
  • the cooling rate for normalizing was 1°C/sec.
  • the prior austenite grain size increases with decreasing Al content, and the torsion fatigue strength increases along with the prior austenite grain size. It is clarified that, in the case where the Al content is 0.005% or less, such an effect becomes saturated and that the torsion fatigue strength also becomes stable.
  • Fig. 5 illustrates the results of the cross-section observation of the fracture portion after a fatigue test had been performed
  • Fig. 5(a) and Fig. 5(b) respectively illustrate the fatigue crack propagation situations for a material containing 0.03%-Al and a material containing 0.003%-Al.
  • the crack propagation route is indicated with a white line. It was found that fatigue crack starts from the outer surface side of a pipe and then propagates through a winding path made of soft pro-eutectoid ferrite.
  • the reason why hardness varies depending on the Al content in a low cooling rate region in Fig. 1 is because, in the case where the Al content is high, since the growth of austenite grains is suppressed in a normalizing process due to the pinning effect of aluminum nitride (AlN) which has been precipitated before normalizing is performed, and, at the same time, since there is an increase in the lamellar spacing of pearlite which is finally formed, there is a decrease in hardness.
  • a decrease in hardness is significant particularly in a low cooling rate region, in which quenching effect is less likely to be realized, and significantly depends on the Al content (the amount of AlN precipitated) in steel.
  • AlN aluminum nitride
  • the C content is set to be in a range of 0.35% or more and 0.55% or less, or preferably in a range of 0.40% or more and 0.45% or less.
  • Si 0.01% or more and 1.0% or less
  • Si is added for deoxidation, and it is not possible to realize a sufficient deoxidation effect in the case where the Si content is less than 0.01%.
  • Si is also a solute strengthening element, and it is necessary that the Si content be 0.01% or more in order to realize such an effect.
  • the Si content is more than 1.0%, there is a deterioration in the hardenability of a steel pipe.
  • the Si content is set to be in a range of 0.01% or more and 1.0% or less, or preferably 0.1% or more and 0.4% or less.
  • Mn 1.0% or more and 3.0% or less
  • Mn is a chemical element which promotes pearlite transformation and improves hardenability, it is necessary that the Mn content be 1.0% or more in order to realize such effects.
  • the Mn content is set to be in a range of 1.0% or more and 3.0% or less, or preferably in a range of 1.4% or more and 2.0% or less.
  • P is an inevitable impurity in the present invention
  • the upper limit of the P content is set to be 0.02% or less.
  • P is a tendency for P to be concentrated in a segregation part which is formed when continuous casting is performed and to remain in a hot-rolled steel sheet as a raw material of a pipe. Since the edges of a steel strip are abutted and subjected to upsetting when electric resistance welding is performed, the segregation part in which P is concentrated may be exposed on the outer surface and inner surface of a steel pipe, which results in there being a risk in that cracking occurs when secondary processing such as flattening forming is performed on this part. Therefore, it is preferable that the P content be 0.01% or less.
  • S is an inevitable impurity in the present invention, and the upper limit of the S content is set to be 0.01% or less.
  • the S content is high, there is a deterioration in toughness of raw material, and S combines with Mn in steel to form MnS. Since MnS is elongated in the longitudinal direction of a steel sheet to form a long inclusion in a hot rolling process, there is a deterioration in workability and toughness. Therefore, it is preferable that the S content be 0.005% or less, or more preferably 0.003% or less.
  • Al is an important chemical element in the present invention in order to achieve the desired prior austenite grain size accompanied by satisfactory torsion fatigue strength, since, in the case where the Al content is more than 0.005%, a pinning effect is realized in a normalizing process due to an increase in the amount of AlN precipitated, which results in the desired austenite grain size not being achieved due to the growth of austenite grains being suppressed. Therefore, the Al content is set to be 0.003% or less.
  • N is a chemical element which contributes to suppressing the growth of austenite grains in a normalizing process as a result of combining with Al to form AlN, it is necessary that the N content be 0.0050% or less in order to suppress such an effect, or preferably 0.0035% or less.
  • the Cr content is set to be in a range of 0.1% or more and 0.5% or less, or preferably in a range of 0.15% or more and 0.30% or less.
  • the basic chemical composition according to the present invention is as described above, and one or more of Ti, B, Mo, W, Nb, V, Ni, Cu, Ca, and REM, which will be described below, may further be added in order to increase strength and fatigue strength.
  • Ti is effective for fixing N in steel in the form of TiN.
  • the Ti content is less than 0.005%, there is insufficient effect of fixing N, and, in the case where the Ti content is more than 0.1%, there is a deterioration in the workability and toughness of steel.
  • the Ti content it is preferable that the Ti content be in a range of 0.005% or more and 0.1% or less, or more preferably in a range of 0.01% or more and 0.04% or less.
  • B is a chemical element which improves hardenability.
  • the B content is less than 0.0003%, there is insufficient effect of increasing hardenability.
  • the B content is more than 0.0050%, such an effect becomes saturated and there is a deterioration in fatigue resistance due to intergranular fracture being more likely to occur as a result of B being precipitated at the grain boundaries.
  • the B content be in a range of 0.0003% or more and 0.0050% or less, or more preferably in a range of 0.0010% or more and 0.0040% or less.
  • Mo is a chemical element which improves hardenability
  • Mo is effective for increasing fatigue strength by increasing the strength of steel. It is preferable that the Mo content be 0.001% or more in order to realize such an effect. However, in the case where the Mo content is more than 2%, there is a significant deterioration in workability. In the case where Mo is added, it is preferable that the Mo content be 2% or less, or more preferably in a range of 0.001% or more and 0.5% or less.
  • W is effective for increasing the strength of steel by forming carbides. It is preferable that the W content be 0.001% or more in order to realize such an effect. However, in the case where the W content is more than 2%, since unnecessary carbides are precipitated, there is a deterioration in fatigue resistance and there is a deterioration in workability. In the case where W is added, it is preferable that the W content be 2% or less, or more preferably in a range of 0.001% or more and 0.5% or less.
  • Nb is a chemical element which improves hardenability and which contributes to an increase in strength by forming carbides. It is preferable that the Nb content be 0.001% or more in order to realize such effects. However, in the case where the Nb content is more than 0.1%, the effects become saturated and there is a deterioration in workability. In the case where Nb is added, it is preferable that the Nb content be 0.1% or less, or more preferably in a range of 0.001% or more and 0.04% or less.
  • V is a chemical element which is effective for increasing the strength of steel by forming carbides and which has temper softening resistance. It is preferable that the V content be 0.001% or more in order to realize such effects. However, in the case where the V content is more than 0.1%, the effects become saturated and there is a deterioration in workability. In the case where V is added, it is preferable that the V content be 0.1% or less, or more preferably in a range of 0.001% or more and 0.1% or less
  • Ni is a chemical element which improves hardenability
  • Ni is effective for increasing fatigue strength by increasing the strength of steel. It is preferable that the Ni content be 0.001% or more in order to realize such an effect. However, in the case where the Ni content is more than 2%, there is a significant deterioration in workability. In the case where Ni is added, it is preferable that the Ni content be 2% or less, or more preferably in a range of 0.001% or more and 0.5% or less.
  • Cu is a chemical element which improves hardenability
  • Cu is effective for increasing fatigue strength by increasing the strength of steel. It is preferable that the Cu content be 0.001% or more in order to realize such an effect. However, in the case where the Cu content is more than 2%, there is a significant deterioration in workability. In the case where Cu is added, it is preferable that the Cu content be 2% or less, or more preferably in a range of 0.001% or more and 0.5% or less.
  • Ca and REM are both chemical elements which are effective for suppressing the formation of the origins of cracks which induce a fatigue breaking in a use environment in which cyclic stress is applied by making the shape of non-metal inclusions spherical, these chemical elements may be selectively added as needed. Such an effect is recognized in the case where the content of each of Ca and REM is 0.0020% or more. On the other hand, in the case where the content is more than 0.02%, there is a decrease in cleaning level due to an increase in the amount of inclusions. Therefore, in the case where Ca or REM is added, it is preferable that the content of each of Ca and REM be 0.02% or less. In the case where Ca and REM are added in combination, it is preferable that the total content be 0.03% or less.
  • the remainder of the chemical composition of the steel according to the present invention other than the constituents described above consists of Fe and inevitable impurities.
  • the metallic microstructure according to the present invention is a microstructure in which the area ratio of pearlite is 85% or more and in which the total of the area ratios of ferrite and bainite (including 0) is 15% or less.
  • the metallic microstructure include mainly pearlite and that the area ratio of pearlite be 85% or more to realize such an effect.
  • the area ratio of pearlite is set to be 85% or more, and the total of the area ratios (including 0) of ferrite and bainite is set to be 15% or less.
  • Prior austenite grain size 25 ⁇ m or more
  • the strength of pearlite increases with decreasing lamellar spacing of pearlite.
  • the lamellar spacing be 170 nm or less, or more preferably 150 nm or less.
  • Hot-reduced steel pipes (having an outer diameter of 45 mm and a wall thickness of 4.5 mm) were manufactured, by performing hot rolling on steel slabs having steel chemical compositions (mass%) given in Table 1 in order to obtain hot-rolled steel strips, by performing roll forming and high-frequency resistance welding on the hot-rolled steel strips in order to manufacture electric resistance welded steel pipes (having an outer diameter of 89 mm and a wall thickness of 4.7 mm), and by thereafter performing hot reducing on the formed and welded pipes.
  • product steel pipes were manufactured, by performing cold drawing in order to obtain cold drawn steel tubes (having an outer diameter of 40 mm and a thickness of 4.0 mm), and thereafter performing normalizing (at a temperature of 920°C for a duration of 10 minutes and with a cooling rate of 0.5°C/sec. to 3.0°C/sec. after soaking had been performed).
  • Examples C and G of Table 1 are comparative examples and not inventive examples according to this invention.
  • a tensile specimen JIS No. 12 specimen
  • etching was performed so that austenite grain boundaries were exposed in a cross-section in the circumferential direction of the steel pipe in order to determine the austenite grain size.
  • the grain size was determined based on a method of section by taking photographs of 10 microscopic fields using an optical microscope at a beautiful of 400 times, and the average value of the determined values was used as a representative value.
  • a lamellar spacing of the pearlite was determined using a method of section, by performing a nital corrosion treatment on a cross-section in the circumferential direction of the steel pipe in the similar way as described above, and by taking photographs of 10 microscopic fields in which cementite layers were arranged as much at a right angle as possible to the paper plane using an electron scanning microscope of 20,000 times power, and the average value of the determined values was used as a representative value.
  • the fatigue strength ⁇ w of the steel pipe was determined by performing a torsion fatigue test under conditions that the frequency was 3 Hz, the wave shape was a sine wave, and the stress ratio R was -1 (reversed vibration).
  • ⁇ w was defined as the stress with which a fracture did not occur even after the number of the cycles reaches 2 million.
  • Examples C and G of Tables 2 and 3 are comparative examples and not inventive examples according to this invention.
  • strength stability a case where the deviation (the difference between the maximum value and the minimum value) of tensile strength TS when the cooling rate for normalizing was changed in the range of 0.5°C/sec. to 3.0°C/sec. was 50 MPa or less was judged as satisfactory ( ⁇ ), and a case where the deviation was more than 50 MPa was judged as unsatisfactory ( ⁇ ).
  • the tensile strength was low in the case where the cooling rate for normalizing was in the lower range, and the torsion fatigue strength was low.
  • the cooling rate was in the higher range, although the difference from the examples of the present invention in tensile strength was small, the torsion fatigue strength was lower than that of the examples of the present invention. The reason for that is thought to be because of the difference in the prior austenite grain size and because of the difference in the strength of pearlite.
  • a hot-rolled steel sheet was used as a raw material of an electric resistance welded steel pipe in the present examples, the present invention is not limited to the examples, and a cold-rolled steel strip may be used as the raw material of a steel pipe.
  • an ordinary electric resistance welded steel pipe which has not been subjected to hot reducing, may be used as a steel pipe which is subjected to cold drawing.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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Claims (2)

  1. Widerstandsgeschweißtes Stahlrohr, wobei
    das Stahlrohr eine chemische Zusammensetzung, die in Massen-% C: 0,35% oder mehr und 0,55% oder weniger, Si: 0,01% oder mehr und 1,0% oder weniger, Mn: 1,0% oder mehr und 3,0% oder weniger, P: 0,02% oder weniger, S: 0,01% oder weniger, Al: 0,003% oder weniger, N: 0,0050% oder weniger, Cr: 0,1% oder mehr und 0,5% oder weniger, optional eines oder mehrere ausgewählt aus Ti: 0,005% oder mehr und 0,1% oder weniger, B: 0,0003% oder mehr und 0,0050% oder weniger, Mo: 2% oder weniger, W: 2% oder weniger, Nb: 0,1% oder weniger, V: 0,1% oder weniger, Ni: 2% oder weniger, Cu: 2% oder weniger, Ca: 0,02% oder weniger, und REM: 0,02% oder weniger und als Rest Fe und unvermeidliche Verunreinigungen enthält und eine metallische Mikrostruktur einschließlich Perlit, Ferrit und Bainit aufweist, wobei das Flächenverhältnis des Perlits 85% oder mehr beträgt, die Gesamtheit der Flächenverhältnisse (einschließlich 0) des Ferrits und des Bainits 15% oder weniger beträgt und wobei eine Voraustenitkorngröße 25 µm oder mehr beträgt.
  2. Widerstandsgeschweißtes Stahlrohr nach Anspruch 1, wobei
    das Stahlrohr die chemische Zusammensetzung aufweist, die in Massen-% eines oder mehrere ausgewählt aus Ti: 0,01% oder mehr und 0,04% oder weniger, B: 0,0010% oder mehr und 0,0040% oder weniger, Mo: 0,001% oder mehr und 0,5% oder weniger, W: 0,001% oder mehr und 0,5% oder weniger, Nb: 0,001% oder mehr und 0,04% oder weniger, V: 0,001% oder mehr und 0,1% oder weniger, Ni: 0,001% oder mehr und 0,5% oder weniger, Cu: 0,001% oder mehr und 0,5% oder weniger, Ca: 0,0020 % oder mehr und 0,02% oder weniger und REM: 0,0020% oder mehr und 0,02% oder weniger enthält.
EP14746008.3A 2013-01-31 2014-01-30 Widerstandsgeschweisstes stahlrohr Active EP2952601B1 (de)

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KR20150099831A (ko) 2015-09-01
CN104968821B (zh) 2017-03-08
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CN104968821A (zh) 2015-10-07
KR101710816B1 (ko) 2017-02-27
US20150368768A1 (en) 2015-12-24
EP2952601A1 (de) 2015-12-09
WO2014119802A1 (ja) 2014-08-07
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