EP2239343A1 - Hohlkörper und verfahren zu seiner herstellung - Google Patents

Hohlkörper und verfahren zu seiner herstellung Download PDF

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Publication number
EP2239343A1
EP2239343A1 EP09703762A EP09703762A EP2239343A1 EP 2239343 A1 EP2239343 A1 EP 2239343A1 EP 09703762 A EP09703762 A EP 09703762A EP 09703762 A EP09703762 A EP 09703762A EP 2239343 A1 EP2239343 A1 EP 2239343A1
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Prior art keywords
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electric resistance
resistance welded
content
quenching
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EP09703762A
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English (en)
French (fr)
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EP2239343A4 (de
EP2239343B1 (de
Inventor
Yoshikazu Kawabata
Masayuki Sakaguchi
Kei Sakata
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C22C1/00—Making non-ferrous alloys
    • C22C1/11—Making amorphous 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
    • C22C38/04—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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

Definitions

  • the present invention relates to a hollow article made from an electric resistance welded steel pipe suitable for applications such as stabilizers and a method for manufacturing the same and particularly relates to the enhancement of the strength of an electric resistance-welded portion heat-treated by rapid heating for a short time or the like.
  • Such hollow parts are usually manufactured in such a manner that seamless steel pipes or electric resistance welded steel pipes are cold-worked so as to have a desired shape and then subjected to thermal refining such as quenching or quenching and tempering. Since the electric resistance welded steel pipes are relatively inexpensive and are excellent in accuracy of dimension, the electric resistance welded steel pipes are widely used as materials for are hollow stabilizers.
  • Japanese Examined Patent Application Publication No. 1-58264 discloses a steel for electric resistance welded steel pipes for hollow stabilizers.
  • the steel contains 0.35% or less C, 0.25% or less Si, 0.30% to 1.20% Mn, less than 0.50% Cr, N, O, Ti, and 0.0005% to 0.009% B and further contains 200 ppm or less Ca and/or Nb, the sum of the content of N and that of O being 0.0200% or less, the content of Ti being four to 12 times the sum of the content of N and that of O in the steel, the content of Nb being not greater than to four-tenths of the content of C.
  • the C, Si, Mn, and Cr content is adjusted such that the ideal critical diameter D 1 is 1.0 in. or more.
  • the C, Si, Mn, and Cr content is adjusted such that the carbon equivalent Ceq is 0.60% or less.
  • Japanese Examined Patent Application Publication No. 61-45688 discloses a method for producing a steel for electric resistance welded steel pipes for hollow stabilizers.
  • the steel contains 0.35% or less C, 0.25% or less Si, 0.30% to 1.20% Mn, less than 0.50% Cr, N, O, Ti, and 0.0005% to 0.009% B and further contains 200 ppm or less Ca, the sum of the content of N and that of O being 0.0200% or less, the content of Ti being four to 12 times the sum of the content of N and that of O in the steel.
  • the following slab is subjected to hot rolling and then coiled at a coiling temperature of 570°C to 690°C: a slab of the steel in which the C, Si, Mn, and Cr content is adjusted such that the D 1 value is 1.0 in. or more and furthermore, the C, Si, Mn, and Cr content is adjusted such that Ceq is 0.60% or less.
  • Japanese Unexamined Patent Application Publication No. 6-93339 discloses a method for manufacturing a high-strength, high-ductility electric resistance welded steel pipe usable for stabilizers.
  • a technique disclosed in Japanese Unexamined Patent Application Publication No. 6-93339 is as follows: an electric resistance welded steel pipe made of a steel which contains 0.18% to 0.28% C, 0.10% to 0.50% Si, 0.60% to 1.80% Mn, 0.020% to 0.050% Ti, 0.0005% to 0.0050% B, and at least one of 0.20% to 0.50% Cr, 0.5% or less Mo, and 0.015% to 0.050% Nb and which further contains 0.0050% or less Ca is subjected to a normalizing treatment at a temperature of 850°C to 950°C and is then quenched, whereby the high-strength, high-ductility electric resistance welded steel pipe is manufactured.
  • Electric resistance welded steel pipes are widely used as materials for hollow parts because the electric resistance welded steel pipes are relatively inexpensive and are excellent in dimensional accuracy. Since further weight saving is recently aided and stresses applied to hollow parts are large, the techniques disclosed in Japanese Examined Patent Application Publication No. 1-58264 , Japanese Examined Patent Application Publication No. 61-45688 , and Japanese Unexamined Patent Application Publication No. 6-93339 are insufficient to secure the fatigue durability of electric resistance welded portions in some cases. This is because the hardenability of the electric resistance welded portions is insufficient.
  • electrical heating is a technique used in a step of quenching a stabilizer and is characterized in that electrical heating is capable of preventing decarburization even during heating in air because heating to 900°C or higher, at which decarburization occurs in air, can be achieved in a short time of one minute or less. If decarburization occurs, a desired surface hardness is not obtained, which leads to a reduction in fatigue durability. Electrical heating, as used herein, refers to a heating technique in which the average heating rate from room temperature to a maximum heating temperature of 900°C or higher is 10 °C/s or more and the time to hold 900°C or higher is one minute or less.
  • the hardness as quenching of an electric resistance welded portion can be prevented from being reduced and a hollow article, having excellent durability, suitable for applications such as such as stabilizers can be readily and stably manufactured. This is particularly industrially advantageous.
  • electric resistance welded steel pipes include electric resistance welded portions including layers (low carbon layers) having a reduced amount of carbon as shown in the C concentration distribution, determined by EPMA (Electron Probe Micro-Analysis), shown in Fig.
  • the electric resistance welded portions cannot be recarburized to a carbon level not less than a desired level by rapid heating for a short time like electrical heating when the low carbon layers have an increased width; and therefore the electric resistance welded portions therefore have reduced hardenability and cannot be sufficiently secured in hardenability.
  • the low carbon layers are unavoidable for electric resistance welding. The inventors have supposed that a low carbon layer is formed as described below.
  • the inventors have further performed investigations and have found that the hardness of a quenched electric resistance welded portion can be adjusted to a desired value and the fatigue durability of an article can be enhanced in such a manner that the heating rate, the attained maximum temperature, the soaking temperature, and the primary cooling rate to the quenching start temperature, which are among quenching conditions, are adjusted so as to satisfy a specific correlation relating to the width of a low carbon layer in an electric resistance welded portion and an amount of carbon sufficient to secure the hardness as quenching is thereby diffused from a base material to the electric resistance welded portion.
  • Hot-rolled Steel Sheet A having a composition shown in Table 1 was processed into steel pipe materials.
  • the steel pipe materials were formed into open pipes with substantially a cylindrical shape. End portions of each of the open pipes were brought into contact with each other and then electrically welded by high-frequency resistance welding or further subjected to reducing rolling, whereby electric resistance welded steel pipes including low carbon layers with various widths (2h: 7 to 54 ⁇ m) were manufactured.
  • the electric resistance welded steel pipes were subjected to a quenching treatment including a thermal cycle shown in Fig.
  • the electric resistance welded steel pipes were measured for hardness, whereby the hardness as quenching thereof was determined.
  • the measurement of hardness was performed in such a manner that a base material portion and an electric resistance welded portion were measured for Vickers hardness HV0.5 with a load of 500 g (a test force of 4.9 N) in the thickness direction thereof and the measurements were averaged, whereby the hardness as quenching of each portion was determined.
  • the heating rate V h , the attained maximum temperature T, and the primary cooling rate V c were varied and the rate of secondary cooling (quenching) was constant (80 °C/s).
  • Equation (a) An integral term following the term (C 0 - 0.09) in Equation (a) shows how, when a location which is spaced from the center of a low carbon layer at a distance y in the width direction of the low carbon layer and which has a width dy has a certain initial C concentration and C is diffused from a base material portion to the low carbon layer after a time t elapsed, the C concentration of the location x varies.
  • the initial C concentration of the low carbon layer formed during electric resistance welding was set such that the C content is constantly 0.09% from -h to +h in the width direction and follows a rectangular pattern.
  • Equation (a) the C content of a location spaced from the center of a low carbon layer at a distance x in the width direction of the low carbon layer is determined from Equation (a) by integrating the integral term following the term (C 0 - 0.09) from -h to +h with respect to y in the integral term.
  • C 0 is the C content (mass percent) of a steel sheet
  • D is the diffusion coefficient (m 2 /s)
  • D D 0 exp(-Q / RT)
  • D 0 is 4.7 ⁇ 10 -5 (m 2 /s)
  • Q 155 (kJ/mol ⁇ K)
  • R 8.31 (J/mol ⁇ K)
  • T is the attained maximum temperature (maximum heating temperature) (K)
  • t the diffusion time (s)
  • t 50 / V h + 50 / V c + k
  • V h is the heating rate (K/s)
  • V c is the primary cooling rate (K/s)
  • k is the soaking time (s).
  • Fig. 1 shows the relationship between the measured average hardness HV0.5 and the ratio C 1 /C 0 of the calculated minimum C content C 1 of each electric resistance welded portion to the C content C 0 of a corresponding one of steel sheets.
  • Fig. 1 illustrates that the hardness (hardness as quenching) of the electric resistance welded portion can be regulated with the ratio C 1 /C 0 and the reduction of the hardness as quenching thereof can be prevented by adjusting the ratio C 1 /C 0 to 0.83 or more.
  • Fig. 5 shows the relationship between the fatigue durability and the ratio of the hardness of each quenched and tempered electric resistance welded portion to the hardness of a corresponding one of base material portions.
  • the fatigue durability is the fatigue strength determined by a fatigue test according to JIS Z 2273 under completely reversed torsion at a number of cycles of 10 6 .
  • Fig. 5 illustrates that an electric resistance welded portion with a hardness that is 86% or more of the hardness of the corresponding base material portion is not significantly reduced in fatigue strength.
  • the adjustment of the ratio C 1 /C 0 to 0.83 or more can prevent the fatigue durability of an electric resistance welded portion from being reduced due to a reduction in hardness as quenching.
  • the ratio C 1 /C 0 is less than 0.83, the hardness as quenching is significantly reduced.
  • the present invention has been completed on the basis of these findings in addition to further investigations.
  • an electric resistance welded steel pipe made from a steel sheet, including a low carbon layer with a width 2h (m) is used.
  • the electric resistance welded steel pipe is manufactured in such a manner that the steel sheet is processed into materials; one of the materials is formed, preferably continuously formed, into an open pipe with substantially a cylindrical shape; and edge portions of the open pipe are brought into contact with each other and then electrically welded by high-frequency resistance welding.
  • the electric resistance welded steel pipe includes an electric resistance welded portion that includes the low carbon layer, which has a width 2h (m).
  • the width of the low carbon layer can be measured by various methods such as the analysis of C by EPMA (Electron Probe Micro-Analysis) as shown in the top of Fig.
  • quenching conditions are adjusted depending on the measured bond width (low carbon layer width) 2h so as to satisfy Inequality (1).
  • the electric resistance welded steel pipe used is preferably cold-worked so as to have a desired shape and then subjected to a heat treatment which includes a quenching treatment and which may further include a tempering treatment, whereby an article with a desired strength is obtained.
  • quenching treatment refers to a rapid heating treatment for a short time as shown in Fig. 2 , that is, a treatment in which the electric resistance welded steel pipe is heated to an attained maximum temperature (maximum heating temperature) T at a heating rate V h , held for a soaking time k, immediately cooled to a quenching start temperature Tq at a primary cooling rate V c , and then secondarily cooled (quenched).
  • rapid heating treatment for a short time refers to a heating process the average heating rate from room temperature to an attained maximum temperature of 900°C or higher is 10 °C/s or more and the time to hold 900°C or higher is one minute or less.
  • a particular heating technique is preferably electrical heating.
  • the heating rate V h , the maximum heating temperature T, the soaking time k, and the primary cooling rate V c are adjusted so as to satisfy the following inequality and the quenching start temperature Tq is adjusted to a temperature higher than the Ar 3 transformation temperature: 0.83 ⁇ 1 - 1 - 0.09 / C 0 ⁇ - h h exp - y 2 / 4 ⁇ Dt / 4 ⁇ ⁇ Dt ⁇ dy
  • C 0 (mass percent) is the C content (mass percent) of a steel sheet
  • t the diffusion time (s)
  • t 50 / V h + 50 / V c + k
  • V h is the heating rate (K/s)
  • V c the primary cooling rate (K/s)
  • k is the soaking time (s)
  • D is the diffusion coefficient (m 2 /s)
  • D D 0 exp(-Q / RT)
  • Do 4.7 ⁇ 10 -5 (m 2 /s)
  • the right side of Inequality (1) was obtained in such a manner that 0 was substituted for x in Equation (a) and both sides of Equation (a) were divided by C 0 representing the C content of the steel sheet. That is, the right side of Inequality (1) means that the ratio of the minimum C content C 1 (0) of an electric resistance welded portion to the C content C 0 of the steel sheet is 0.83 or more.
  • the C content of the electric resistance welded portion cannot be increased to a level sufficient to achieve a hardness as quenching substantially equal to the hardness of a base material portion; hence, the hardness of the electric resistance welded portion cannot be increased to a desired hardness as quenching and therefore a manufactured article has reduced durability.
  • the soaking time k includes 0 s (no holding).
  • the quenching start temperature Tq in the quenching treatment is adjusted to a temperature higher than the Ar 3 transformation temperature of the electric resistance welded portion.
  • the quenching start temperature Tq is equal to or lower than the Ar 3 transformation temperature, the transformation of ferrite, bainite, and/or the like occurs prior to the start of secondary cooling (quenching) hence, the electric resistance welded portion cannot be transformed into a 100% martensite structure and a desired hardness as quenching or desired fatigue durability cannot be achieved.
  • a value (Ac 3 transformation temperature) determined using a calculation formula below is used in place of the Ar 3 transformation temperature of the electric resistance welded portion.
  • the Ac 3 transformation temperature shifts to a temperature higher than the Ar 3 transformation temperature upon the determination of the quenching start temperature Tq and is a safe-side value.
  • a ⁇ c 3 ⁇ t ⁇ r ⁇ a ⁇ n ⁇ s ⁇ f ⁇ o ⁇ r ⁇ m ⁇ a ⁇ t ⁇ i ⁇ o ⁇ n t ⁇ e ⁇ m ⁇ p ⁇ e ⁇ r ⁇ a ⁇ t ⁇ u ⁇ r ⁇ e °C 910 ⁇ 203 C ⁇ 15.2 ⁇ N ⁇ i + 44.7 ⁇ S ⁇ i + 104 ⁇ V + 31.5 ⁇ M ⁇ o + 13.1 ⁇ W ⁇ 30 ⁇ M ⁇ n + 11 ⁇ C ⁇ r + 20 ⁇ C ⁇ u ⁇ 700 ⁇ P ⁇ 400 ⁇ A ⁇ 1 ⁇ 120 ⁇ A ⁇ s ⁇ 400
  • the calculation formula defining the Ac 3 transformation temperature is one quoted from Koda, Leslie Tekkou Zairyougaku, Maruzen, 1985, p. 273 .
  • Secondary cooling may be performed under cooling conditions capable of producing a 100% martensitic structure and depends on the composition of the steel sheet.
  • the steel sheet which has a composition below, is preferably cooled from the quenching start temperature Tq to room temperature at an average cooling rate of 30 °C/s or more and more preferably 80 °C/s or more.
  • secondary cooling is preferably water cooling, oil cooling, or the like.
  • the width of the low carbon layer which is included in the electric resistance welded portion of the electric resistance welded steel pipe, needs to be adjusted to be equal to or less than the low carbon layer width 2h such that Inequality (1) is satisfied.
  • the low carbon layer width 2h is determined from set quenching conditions and Inequality (1) so as to satisfy Inequality (1) for the set quenching conditions.
  • An electric resistance welding condition, particularly the heat input, is preferably adjusted such that the low carbon layer width of the electric resistance welded portion is equal to or less than a determined value.
  • the electric resistance welded portion is checked for workability by a bending test or the like.
  • the low carbon layer width 2h is too small to satisfy Inequality (1) and the untreated electric resistance welded portion has reduced workability, it is effective that after electric resistance welding is performed such that the bond width is greater than an appropriate value, the electric resistance welded steel pipe is subjected to diameter reducing such that the bond width is mechanically reduced.
  • Diameter reducing is preferably performed by a drawing or punching process using a dice, a caliber rolling process, or the like.
  • the temperature of diameter reducing may be cold, warm, or hot.
  • Diameter reducing is preferably performed in such a manner that the electric resistance welded steel pipe is heated to a temperature of 950°C to 1000°C by induction heating and then subjected to reducing rolling at a reduction of diameter of 50% to 70% at a finish temperature of about 800°C.
  • the bond width (low carbon layer width) 2h can be reduced by increasing the diameter-reducing rolling reduction during reducing rolling.
  • the bond width 2h is used as the low carbon layer width.
  • the low carbon layer width 2h is herein preferably 25 ⁇ m or less and more preferably 16 ⁇ m or less because the temperature achieved by conventional electrical heating is probably increased to 1000°C and then reduced to 900°C or lower in up to one minute for the purpose of preventing decarburization.
  • the low carbon layer width as electric resistance welding is preferably 10 ⁇ m or more and more preferably 30 ⁇ m or more.
  • the low carbon layer width as electric resistance welding is greater than 30 ⁇ m, it is effective that the low carbon layer width is mechanically reduced to 25 ⁇ m or less and more preferably 16 ⁇ m or less in such a manner that the rolling reduction for diameter reducing is increased by reducing rolling or the like.
  • the tempering treatment may be performed subsequently to the quenching treatment for the purpose of increasing the toughness.
  • the heating temperature in the tempering treatment is preferably within a range from 150°C to 450°C. When the heating temperature for tempering is lower than 150°C, desired toughness cannot be achieved. When the heating temperature is higher than 450°C, desired fatigue durability cannot be achieved because of a reduction in hardness.
  • the steel sheet which is a material suitable for the electric resistance welded steel pipe, contains 0.15% to 0.40% C, 0.05% to 0.50% Si, 0.30% to 2.00% Mn, 0.01% to 0.10% Al, 0.001% to 0.04% Ti, 0.0005% to 0.0050% B, and 0.0010% to 0.0100% N and further contains one or more selected from the group consisting of 1.0% or less Cr, 1.0% or less Mo, 1.0% or less W, 1.0% or less Ni, and 1.0% or less Cu; and/or one or more selected from the group consisting of 0.2% or less Nb and 0.2% or less V; and/or 0.0050% or less Ca on a mass basis, the remainder being Fe and unavoidable impurities, and Ti and N satisfy the inequality (N / 14) ⁇ (Ti / 47.9).
  • the steel sheet is preferably a hot-rolled steel sheet.
  • the term "steel sheet" as used herein covers any steel strip.
  • Mass percent is hereinafter simply represented by %.
  • C is a useful element that forms a solid solution to increase the strength of steel and precipitates in the form of a carbide or a carbonitride to increase the strength of tempered steel.
  • the content of C needs to be 0.15% or more.
  • the content thereof is greater than 0.40%, the toughness is reduced after the quenching treatment. Therefore, the content of C is limited to a range from 0.15% to 0.40% and is preferably within a range from 0.20% to 0.35%.
  • Si is an element acting as a deoxidizing agent.
  • the content thereof needs to be 0.05% or more.
  • the content is greater than 0.50%, the effect of deoxidation is saturated; hence, an advantage appropriate to the content cannot be expected, which is economically disadvantageous.
  • inclusions are formed during electric resistance welding, which negatively affects the soundness of the electric resistance welded portion. Therefore, the content of S is limited to a range from 0.05% to 0.50% and is preferably within a range from 0.10% to 0.30%.
  • Mn is an element that forms a solid solution to increase the strength and hardenability of steel.
  • the content thereof needs to be 0.30% or more.
  • the content of Mn is limited to a range from 0.30% to 2.00% and is preferably within a range from 0.30% to 1.60%.
  • Al is a useful element that acts as a deoxidizing agent and has an effect of fixing N and an effect of securing the amount of solid solution B effective in increasing the hardenability.
  • the content thereof needs to be 0.01% or more.
  • the content of Al is limited to a range from 0.01% to 0.10% and is preferably within a range from 0.02% to 0.05%.
  • B is an element effective in increasing the hardenability of steel.
  • B has the ability to strengthen grain boundaries and also has an effect of preventing quenching cracks.
  • the content thereof needs to be 0.0005% or more.
  • the content is greater than 0.0050%, the effect is saturated, which is economically disadvantageous.
  • the content of B is limited to a range from 0.0005% to 0.0050% and is preferably within a range from 0.0010% to 0.0025%.
  • Ti is an element that has an effect of fixing N and an effect of securing the amount of solid solution B effective in increasing the hardenability. Ti precipitates in the form of a fine carbide, prevents grains from being coarsened during welding or heat treating, and contributes to an increase in toughness. In order to obtain such effects, the content thereof needs to be 0.001% or more. When the content is greater than 0.04%, a large amount of inclusions are formed to cause a reduction in toughness. Therefore, the content of Ti is limited to a range from 0.001% to 0.04% and is preferably within a range from 0.02% to 0.03%.
  • N is an element that combines with alloy elements in steel to produce nitrides and carbonitrides and contributes to secure the strength after tempering.
  • the content thereof needs to be 0.0010% or more.
  • the content of N is limited to a range from 0.0010% to 0.0100%.
  • the content of Ti and that of N are within the above ranges and Ti and N satisfy the inequality (N / 14) ⁇ (Ti / 47.9).
  • Ti and N do not satisfy this inequality, the amount of solid solution B is unstable during quenching, which is not preferred.
  • the above components are preferred fundamental components.
  • one or more selected from an A Group, B Group, and C Group below may be contained in addition to the fundamental components.
  • the following element or elements may be selectively contained as required:
  • the content thereof is preferably 0.05% or more.
  • the content of Cr is preferably limited to 1.0% or less and is more preferably within a range from 0.10% to 0.30%.
  • Mo has the ability to enhance the hardenability and the ability to form a fine carbide to increase the strength and contributes to secure desired strength.
  • the content thereof is preferably 0.05% or more.
  • the content of Mo is preferably limited to 1.0% or less and is more preferably within a range from 0.10% to 0.30%.
  • W is an element that has the ability to enhance the hardenability and the ability to well balance the hardness and toughness as thermal refining.
  • the content thereof is preferably 0.05% or more.
  • the content of W is preferably limited to 1.0% or less and is more preferably within a range from 0.10% to 0.30%.
  • Ni is an element that contributes to enhance the hardenability and the toughness.
  • the content thereof is preferably 0.05% or more.
  • the content of Ni is preferably limited to 1.0% or less and is more preferably within a range from 0.10% to 0.50%.
  • Cu is an element that is effective in enhancing the hardness and is effective in preventing delayed fracture.
  • the content thereof is preferably 0.05% or more.
  • the content of Cu is preferably limited to 1.0% or less and is more preferably within a range from 0.10% to 0.30%.
  • the remainder other than the above components are Fe and unavoidable impurities.
  • the unavoidable impurities are P, S, and O.
  • a P content of 0.020% or less, an S content of 0.010% or less, and an O content of 0.005% or less are allowable.
  • P is an element that negatively affects the weld cracking resistance and the toughness.
  • the content thereof is preferably adjusted to 0.020% or less and more preferably 0.015% or less.
  • S is present in steel in the form of a sulfide inclusion and is an element that reduces the workability, toughness, fatigue life of steel pipes and enhances the reheat crack sensitivity thereof.
  • the content thereof is preferably adjusted to 0.010% or less and more preferably 0.005% or less for hollow stabilizer use.
  • O is present in steel in the form of an oxide inclusion and reduces the workability, toughness, fatigue life of steel pipes. Therefore, the content thereof is preferably adjusted to 0.005% or less and more preferably 0.002% or less for hollow stabilizer use.
  • a hollow article obtained by the above manufacturing method is manufactured in such a manner that an electric resistance welded steel pipe, made of a steel sheet, including an electric resistance welded portion having a low carbon layer with a width of 2h (m) is subjected to at least a quenching treatment.
  • a base material portion (steel sheet) other than the electric resistance welded portion preferably satisfies the above composition.
  • the hollow article according to the present invention has excellent durability and is characterized in that the ratio C 1 /C 0 of the minimum C content C 1 of the electric resistance welded portion to the C content C 0 of the base material portion (steel sheet) is 0.83 or more.
  • the following value is used: a value obtained in such a manner that the electric resistance welded portion of the hollow article is analyzed for C in the circumferential direction of the pipe by EPMA or chemical analysis.
  • Hot-rolled steel sheets having compositions shown in Table 1 were processed into materials.
  • the materials were subjected to continuous cold forming, whereby open pipes with substantially a cylindrical shape were prepared. Edge portions of the open pipe were brought into contact with each other and then electrically welded by high-frequency resistance welding, whereby an electric resistance welded steel pipe (an outer diameter of 30 mm ⁇ and a thickness of 6 mm) was prepared.
  • Some of the hot-rolled steel sheets were processed into materials. These materials were subjected to continuous cold forming, whereby open pipes were prepared. These open pipes electrically welded, whereby base pipes having an outer diameter of 89 mm ⁇ and a thickness of 6.2 mm were prepared.
  • the base pipes were heated to 950°C and then subjected to reducing rolling at a finish temperature of 800°C, whereby steel pipes having an outer diameter of 30 mm ⁇ and a thickness of 6 mm were prepared.
  • welding conditions were varied, whereby the width of bond (width of each low carbon layer) 2h was adjusted to various values as shown in Tables 2 and 3.
  • the bond width (low carbon layer width) 2h was determined in such a manner that a specimen for microstructure observation was taken from each electric resistance welded steel pipe so as to include an electric resistance welded portion and then observed for microstructure.
  • the untreated electric resistance welded steel pipes were subjected to a quenching treatment in a heat cycle pattern shown in Fig. 2 under conditions shown in Tables 2 and 3.
  • Specimens for hardness measurement were taken from the untreated electric resistance welded steel pipes so as to include electric resistance welded portions and then subjected to hardness measurement, whereby base material portions and the electric resistance welded portions were measured for hardness as quenching.
  • the electric resistance welded portion of each obtained electric resistance welded steel pipe was analyzed for C concentration in the circumferential direction of the pipe by EPMA at a position 100 ⁇ m away from the outer surface of the pipe, whereby the measured minimum C content C 1 (measured) was determined.
  • the minimum C content C 1 of each electric resistance welded steel pipe subjected to the quenching treatment was calculated by substituting 0 for x in Equation (a) and then divided by the C content C 0 of the base material portion (steel sheet), whereby the ratio C 1 /C 0 of calculated values and the ratio C 1 /C 0 of measured values were calculated.
  • the quenched steel pipes were tempered at 350°C for 20 minutes, subjected to a torsion fatigue test, and then checked whether irregular cracks were present along the electric resistance welded portions. Such cracks along the electric resistance welded portions were represented by B ⁇ and other cracks were represented by A O.
  • Specimens including the electric resistance welded portions were cut out of the obtained electric resistance welded steel pipes so as to have a cross section perpendicular to the axial direction of the pipes, polished, corroded with a metal flow etching solution (5% picric acid and a surface acting agent), and then observed for sectional structure with a light microscope (a magnification ratio of 400 times). The maximum width of a region (layer) in which no segregation line was observed in the sectional structure was measured, whereby the bond width (low carbon layer width) 2h was determined.
  • Specimens for hardness measurement were taken from the obtained electric resistance welded steel pipes.
  • the electric resistance welded portions and the base material portions were measured for Vickers hardness HV0.5 in the thickness direction thereof with a Vickers hardness meter (a load of 4.9 N).
  • the outer surfaces were measured at a pitch of 0.2 mm. Obtained measurements were arithmetically averaged, whereby the hardness of the electric resistance welded portion and that of the base material portion of each steel pipe were determined.
  • Specimens (a length of 250 mm in the axial direction of the pipes) for fatigue measurement were taken from the obtained electric resistance welded steel pipes having an outer diameter of 30 mm ⁇ and a thickness of 6 mm and then subjected to a fatigue test according to JIS Z 2273 under completely reversed torsion.
  • a stress ⁇ of 380 MPa was applied to each of component A, B, and E materials and a stress ⁇ of 470 MPa was applied to each of C and D materials.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
EP09703762.6A 2008-01-21 2009-01-20 Hohlkörper und verfahren zu seiner herstellung Not-in-force EP2239343B1 (de)

Applications Claiming Priority (2)

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JP2008010018 2008-01-21
PCT/JP2009/051148 WO2009093728A1 (ja) 2008-01-21 2009-01-20 中空部材およびその製造方法

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EP2778239A1 (de) * 2013-03-14 2014-09-17 Tenaris Coiled Tubes, LLC Hochleistungsmaterial für gewickelte Rohrwendelanwendungen und Verfahren zu ihrer Herstellung
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
US9163296B2 (en) 2011-01-25 2015-10-20 Tenaris Coiled Tubes, Llc Coiled tube with varying mechanical properties for superior performance and methods to produce the same by a continuous heat treatment
EP2857537A4 (de) * 2012-05-25 2016-04-13 Nippon Steel & Sumitomo Metal Corp Hohlstabilisator und stahlrohr für hohle stabilisatoren und verfahren zur herstellung davon
US9598746B2 (en) 2011-02-07 2017-03-21 Dalmine S.P.A. High strength steel pipes with excellent toughness at low temperature and sulfide stress corrosion cracking resistance
US9644248B2 (en) 2013-04-08 2017-05-09 Dalmine S.P.A. Heavy wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes
US9657365B2 (en) 2013-04-08 2017-05-23 Dalmine S.P.A. High strength medium wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes
US9970242B2 (en) 2013-01-11 2018-05-15 Tenaris Connections B.V. Galling resistant drill pipe tool joint and corresponding drill pipe
EP3358028A4 (de) * 2015-09-29 2018-08-15 JFE Steel Corporation Widerstandsgeschweisstes stahlrohr für hochfesten hohlstabilisator, verfahren zur herstellung eines widerstandsgeschweissten stahlrohrs für hochfesten hohlstabilisator, hochfester hohlstabilisator und verfahren zur herstellung eines hochfesten hohlstabilisators
WO2020127555A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur herstellung von thermo-mechanisch hergestellten profilierten warmbanderzeugnissen
WO2020127561A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur herstellung von konventionell warmgewalzten, profilierten warmbanderzeugnissen
WO2020127557A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur herstellung von thermo-mechanisch hergestellten warmbanderzeugnissen
WO2020127558A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur herstellung von konventionell warmgewalzten warmbanderzeugnissen
US10844669B2 (en) 2009-11-24 2020-11-24 Tenaris Connections B.V. Threaded joint sealed to internal and external pressures
US11105501B2 (en) 2013-06-25 2021-08-31 Tenaris Connections B.V. High-chromium heat-resistant steel
US11124852B2 (en) 2016-08-12 2021-09-21 Tenaris Coiled Tubes, Llc Method and system for manufacturing coiled tubing
US11512361B2 (en) 2017-12-27 2022-11-29 Jfe Steel Corporation Electric resistance welded steel pipe or tube and production method for electric resistance welded steel pipe or tube
US11833561B2 (en) 2017-01-17 2023-12-05 Forum Us, Inc. Method of manufacturing a coiled tubing string

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US10844669B2 (en) 2009-11-24 2020-11-24 Tenaris Connections B.V. Threaded joint sealed to internal and external pressures
US11952648B2 (en) 2011-01-25 2024-04-09 Tenaris Coiled Tubes, Llc Method of forming and heat treating coiled tubing
US9163296B2 (en) 2011-01-25 2015-10-20 Tenaris Coiled Tubes, Llc Coiled tube with varying mechanical properties for superior performance and methods to produce the same by a continuous heat treatment
US10480054B2 (en) 2011-01-25 2019-11-19 Tenaris Coiled Tubes, Llc Coiled tube with varying mechanical properties for superior performance and methods to produce the same by a continuous heat treatment
US9598746B2 (en) 2011-02-07 2017-03-21 Dalmine S.P.A. High strength steel pipes with excellent toughness at low temperature and sulfide stress corrosion cracking resistance
EP2857537A4 (de) * 2012-05-25 2016-04-13 Nippon Steel & Sumitomo Metal Corp Hohlstabilisator und stahlrohr für hohle stabilisatoren und verfahren zur herstellung davon
US9970242B2 (en) 2013-01-11 2018-05-15 Tenaris Connections B.V. Galling resistant drill pipe tool joint and corresponding drill pipe
EP3845672A1 (de) * 2013-03-14 2021-07-07 Tenaris Coiled Tubes, LLC Hochleistungsmaterial für rohrwendelanwendungen und verfahren zur herstellung davon
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US10378075B2 (en) 2013-03-14 2019-08-13 Tenaris Coiled Tubes, Llc High performance material for coiled tubing applications and the method of producing the same
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US11377704B2 (en) 2013-03-14 2022-07-05 Tenaris Coiled Tubes, Llc High performance material for coiled tubing applications and the method of producing the same
US9803256B2 (en) 2013-03-14 2017-10-31 Tenaris Coiled Tubes, Llc High performance material for coiled tubing applications and the method of producing the same
US9657365B2 (en) 2013-04-08 2017-05-23 Dalmine S.P.A. High strength medium wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes
US9644248B2 (en) 2013-04-08 2017-05-09 Dalmine S.P.A. Heavy wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes
US11105501B2 (en) 2013-06-25 2021-08-31 Tenaris Connections B.V. High-chromium heat-resistant steel
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
EP3358028A4 (de) * 2015-09-29 2018-08-15 JFE Steel Corporation Widerstandsgeschweisstes stahlrohr für hochfesten hohlstabilisator, verfahren zur herstellung eines widerstandsgeschweissten stahlrohrs für hochfesten hohlstabilisator, hochfester hohlstabilisator und verfahren zur herstellung eines hochfesten hohlstabilisators
US11124852B2 (en) 2016-08-12 2021-09-21 Tenaris Coiled Tubes, Llc Method and system for manufacturing coiled tubing
US11833561B2 (en) 2017-01-17 2023-12-05 Forum Us, Inc. Method of manufacturing a coiled tubing string
US11512361B2 (en) 2017-12-27 2022-11-29 Jfe Steel Corporation Electric resistance welded steel pipe or tube and production method for electric resistance welded steel pipe or tube
WO2020127558A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur herstellung von konventionell warmgewalzten warmbanderzeugnissen
WO2020127557A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur herstellung von thermo-mechanisch hergestellten warmbanderzeugnissen
WO2020127561A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur herstellung von konventionell warmgewalzten, profilierten warmbanderzeugnissen
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EP2239343A4 (de) 2016-06-15
JP2009197327A (ja) 2009-09-03
EP2239343B1 (de) 2017-11-22
WO2009093728A1 (ja) 2009-07-30
CN101925678A (zh) 2010-12-22
KR101321681B1 (ko) 2013-10-23
KR20100112601A (ko) 2010-10-19
JP5353256B2 (ja) 2013-11-27
CN101925678B (zh) 2012-06-20

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