EP2816133A1 - Austenitischer edelstahl für vorrichtung zur hochtemperaturverwendung mit geschweisster rohrstruktur - Google Patents

Austenitischer edelstahl für vorrichtung zur hochtemperaturverwendung mit geschweisster rohrstruktur Download PDF

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EP2816133A1
EP2816133A1 EP13749790.5A EP13749790A EP2816133A1 EP 2816133 A1 EP2816133 A1 EP 2816133A1 EP 13749790 A EP13749790 A EP 13749790A EP 2816133 A1 EP2816133 A1 EP 2816133A1
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Prior art keywords
welding
stainless steel
austenitic stainless
weldability
cracking
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French (fr)
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EP2816133A4 (de
EP2816133B1 (de
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Hiroyuki Matsuyama
Eiichiro Ishimaru
Michio Nakata
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • 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
    • 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
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to an austenitic stainless steel to be used for a high-temperature apparatus having a welded tubular structure, which is to be used at a high temperature.
  • a fuel reformer for producing a hydrogen gas including a fuel cell, may be an apparatus for producing hydrogen gas from a fuel such as city gas, kerosene and gasoline, by using a fuel reforming catalyst.
  • the catalyst operating temperature for producing hydrogen may be a high temperature of about 700°C or more and therefore, the catalyst-holding structure material should be required to have excellent oxidation resistance and high-temperature strength.
  • the oxidation resistance and high-temperature strength of the catalyst-holding structure material should be necessary so as to ensure the long-term durability thereof as a structure or construction. A partial fracture or deformation due to oxidative damage or lack of strength at a high temperature may deteriorate the performance as a hydrogen gas generator.
  • the performance deterioration of the hydrogen gas generator may in turn deteriorate the performance of a fuel cell body for generating electricity, to thereby cause performance reduction of the system.
  • SUS310S JIS Standards
  • SUS310S JIS Standards
  • a fuel reformer having an integral cylindrical structure, which has been fabricated by welding a thin sheet of austenitic stainless steel including SUS310S into a tubular shape, and then being stacked into a multiple tubular form (Patent Document 1).
  • the cylindrically structured fuel reformer may have a much complicated structure, where the stacked tubes are function-separated.
  • the welding is conducted not only at the time of the welding into a tubular shape, but also at the time of the formation of a gas passage, wherein tubes are joined with each other by girth welding.
  • an austenitic stainless steel which is excellent not only in weldability but also in high-temperature characteristics may be demanded.
  • the term "excellent in weldability" means that the high-temperature cracking may be less liable to occur mainly at the time of welding.
  • the high-temperature cracking capable of occurring during the welding of an austenitic stainless steel may be cracking which is attributable to the segregation of a low-melting point compound such as P, S, Si and Nb on the austenite grain boundary or columnar crystal grain boundary in the solidification process, and may also be referred to as "solidification cracking".
  • a low-melting point compound such as P, S, Si and Nb
  • the high-temperature cracking may be prevented by incorporating several % of ferrite into the weld metal.
  • the reason why ferrite is effective may be, for example, that the solid solubility of S and P is higher in ferrite, the wettability of a liquid is reduced so as to make a liquid film difficult to be spread, and a ferrite/austenite interface is solidified while retaining a complicated configuration thereof, to thereby provide an austenite grain boundary, whereby the cracking is less liable to be propagated.
  • a low-melting point metal-producing element such as P, S and Si.
  • an austenitic stainless steel for a high-temperature apparatus having high-temperature characteristics, which are substantially equal to those of SUS310S
  • a material wherein the Si content is increased so as to improve the oxidation resistance thereof As described above, an increase in the Si content is liable to cause high-temperature cracking and therefore, the component adjustment may be performed so as incorporate therein several % of ferrite at the time of solidification thereof (for example, as shown in Patent Documents 1 to 4).
  • An object of the present invention is to provide an austenitic stainless steel which is excellent in profitability and excellent in weldability for providing an article having a complicated tubular structure.
  • the present inventors have conducted reproducibility tests on the high-temperature cracking by using stainless steels, which have been changed in various components thereof, and by changing the welding heat input, to thereby study the high-temperature cracking during the welding.
  • the present inventors have found that, for the purpose of improving the high-temperature cracking, it may be important to attain a proper amount of welding penetration by studying appropriate material components thereof.
  • the present invention has been accomplished based on the resultant discovery.
  • the following descriptions should not be construed as limiting the present invention by any means.
  • the inventors have made tests and evaluations on the welding conditions, components and compositions, with which the amount of welding penetration due to appropriate welding can be ensured, even when the welding heat input is lowered so as to prevent the high-temperature cracking, while controlling the amount of low-melting point element such as Si, P and S for inhibiting the high-temperature cracking during the welding.
  • Tests were conducted by changing the welding heat input so as to examine the relationship of the bead width ratio between front and back surfaces after welding with high heat input (that is, the bead width of back surface/bead width of front surface), and the high-temperature cracking property, and examine the welding penetration at the time of low heat input.
  • the present inventors have found that, during the welding with high heat input, when the bead width ratio of front and back surfaces exceeds 0.8, the high-temperature cracking is liable to occur.
  • the present inventors have clarified that a specific relationship of Al and Ca contents in the steel affects the bead width ratio of front and back surfaces.
  • the "weldability index" represented by the following formula (1) may have a suitable range, and within such a suitable range, the bead width ratio of front and back surfaces may be 0.8 or less, to thereby make it possible to keep good weldability. 0.015 ⁇ 0.29 % Al + 17.92 % Ca ⁇ 0.093
  • the weldability index is less than 0.015, the amount of welding penetration may become large, and the high-temperature cracking is liable to occur.
  • the weldability index of formula (1) is 0.015 or more, the amount of welding penetration may be decreased, even at the time of high heat input, and the bead width ratio of front and back surfaces may become 0.8 or less. As a result, the occurrence of high-temperature cracking may be reduced.
  • the weldability index may preferably be 0.03 or more. If the weldability index exceeds 0.093, the welding penetration during the welding with low heat input may be reduced so as to deteriorate the weldability.
  • the upper limit of the weldability index may preferably be 0.079, more preferably 0.068.
  • the present inventors have gained the above-described knowledge relating to the test results, and have provided a useful measure for solving the technical problem in the welding of an austenitic stainless steel.
  • the austenitic stainless steel for an article having a tubular structure according to the present invention comprises: in mass%,
  • austenitic stainless steel for an article having a tubular structure according to the present invention may contain one member or two or members of, in mass%,
  • the above tubular structural body may include a welded structural body, and the welding may include TIG welding.
  • the austenitic stainless steel excellent in weldability for a tubular structure according to the present invention can be stably welded with an appropriate amount of welding penetration, so that the high-temperature cracking due to an increase in the welding heat input can be reduced, and an austenitic stainless steel excellent in weldability for a tubular structure can be provided at a low cost.
  • Fig. 1 is a view showing a relationship among Al and Ca contents, welding cracking and welding workability.
  • C may be an element which is effective in stabilizing the austenite structure. However, if the content is increased, this element may promote high-temperature cracking due to the segregation of S. For this reason, the upper limit thereof may be set to 0.2%. Further, for suppressing the occurrence of high-temperature cracking, the upper limit value may preferably be 0.15%, more preferably 0.1%. On the other hand, the lower limit may be set to 0.001% in view of production cost. For this reason, the lower limit may preferably be 0.002%, more preferably 0.003%.
  • Si may be used as a deoxidizing element and its content may preferably be larger in view of the oxidation resistance but if added in excess, this element may seriously deteriorate the weldability. Therefore, the upper limit may be set to 1.5%. For this reason, the upper limit may preferably be 1.0%, more preferably 0.8%. The lower limit may be set to 0.01% in view of production cost. For this reason, the lower limit value may preferably be 0.015%, more preferably 0.02%.
  • Mn may be an element which is necessary for stabilizing the austenite structure, and may also be an element for fixing S during the welding so as to suppress the reduction in the high-temperature cracking.
  • the upper limit may be set to 1.5% or less.
  • the upper limit may preferably be 1.3%, more preferably 1.0%.
  • the lower limit may be set to 0.01%. For this reason, the lower limit may preferably be 0.015%, more preferably 0.02%.
  • P may be an element which is segregated on the grain boundary at the time of the solidification, to thereby reduce the weldability. Therefore, the upper limit may be set to 0.022% or less. The upper limit may preferably be 0.020%, more preferably 0.015%. P may be an element which is unavoidably contained in the steel, but in view of the weldability, it may be preferred that P is not present.
  • S may also be an element which is segregated on the grain boundary at the time of the solidification, to thereby reduce the weldability. Therefore, the upper limit may be set to 0.004% or less. The upper limit may preferably be 0.0015%, more preferably 0.0001%. S may be an element which is unavoidably contained in the steel, but in view of weldability, it may be preferred that S is not present.
  • Cr Cr may be an element which is necessary for ensuring the corrosion resistance, which is a basic characteristic of a stainless steel, and for ensuring the oxidation resistance and strength in a high-temperature environment, which are important in the present invention. Therefore, its content should be 20.0% or more. For this reason, the lower limit may preferably be 22.0%, more preferably 23.0%. The upper limit may be set to 26.0% so as not to reduce the formability, raise the production cost or deteriorate the productivity. For this reason, the upper limit may preferably be 25.5%, more preferably 24.0%.
  • Ni may be an element which is necessary for stabilizing the austenite structure, to thereby ensure the strength at a high temperature. Therefore, the lower limit may be set to 15.0%. For this reason, the lower limit may preferably be 16.0%, more preferably 17.0%. However, if the content is increased, the high-temperature cracking due to the segregation of S may be promoted, the production cost may be raised, or the productivity may be deteriorated, and therefore, the upper limit may be set to 23.0%. For this reason, the upper limit may preferably be 21.0%, more preferably 19.0%.
  • N may be an element which is effective in stabilizing the austenite structure.
  • the upper limit may be set to 0.07%.
  • the upper limit may preferably be 0.06%, more preferably 0.05%.
  • the lower limit may be set to 0.001%.
  • the lower limit may preferably be 0.002%, more preferably 0.003%.
  • Al may be a deoxidizing element, and may be an element which is effective in achieving an adequate amount of welding penetration during the welding. However, if the amount thereof to be added is too large, the welding penetration property (amount of welding penetration, or width or depth of welding penetration) may be decreased so as to deteriorate the weldability. Therefore, the upper limit may be set to 0.05%. For this reason, the upper limit may preferably be 0.045%, more preferably 0.035%. Further, the lower limit may be set to 0.003% in view of the production cost. The lower limit may preferably be 0.004%, more preferably 0.005%.
  • Ca may be an element which is necessary for achieving an adequate amount of welding penetration during the welding by decreasing the content of S which may deteriorate the weldability. However, if the amount thereof to be added is too large, the weldability may be conversely reduced so as to deteriorate the weldability. Therefore, the upper limit may be set to 0.005% or less. For this reason, the upper limit may preferably be 0.004%, more preferably 0.003%.
  • the lower limit may be 0.0003% in consideration of the production cost. For this reason, the lower limit may preferably be 0.0005%, more preferably 0.0008%.
  • formula (1) which is a relational expression of Al and Ca contents has been developed.
  • This may be a formula for determining the relationship of Al and Ca contents by evaluating the welding penetration based on the bead width ratio between the front and back surfaces after welding. 0.015 ⁇ 0.29 % Al + 17.92 % Ca ⁇ 0.093
  • the "weldability index" represented by formula (1) may have a suitable range, and within such a suitable range, the bead width ratio of front and back surfaces may be 0.8 or less, so as to make it possible to keep good weldability. in this way, the present inventors have developed formula (1). It has been found that, although Al is usually added as a deoxidizing element and Ca is added to reduce the S content, each of these elements is an element which is necessary for achieving an adequate amount of welding penetration during the welding. If the weldability index is less than 0.015, the amount of welding penetration may become large, and the high-temperature cracking is liable to occur.
  • the weldability index of formula (1) when the weldability index of formula (1) is 0.015 or more, the amount of welding penetration may be decreased also at the time of high heat input, and the bead width ratio of front and back surfaces may become 0.8 or less. As a result, the occurrence of high-temperature cracking may be reduced.
  • the weldability index may preferably be 0.03 or more.
  • the weldability index exceeds 0.093, the welding penetration during the welding with low heat input may be reduced so as to deteriorate the weldability.
  • the welding conditions are liable to be varied because of the complicated structure.
  • the heat input during the welding is low and the amount of welding penetration is small, a joint failure may be generated.
  • the welding is conducted by raising the heat input during the welding so as to surely achieve the melting and joint thereby, the amount of welding penetration may be readily increased to an excessive extent.
  • the austenitic stainless steel according to the present invention may be characterized in that the high-temperature cracking hardly occurs, even when the welding heat input is increased, and on the other hand, the weldability is not deteriorated, even when the welding heat input is decreased.
  • Cu, Mo, Sn, W and Co may be mixed from a scrap of the raw material. These elements may be effective in enhancing the corrosion resistance, but if added in an excess amount, the cost may be raised, or the productivity may be reduced. Therefore, the upper limits of those elements may be Cu: 0.30%, Mo: 0.30%, Sn: 0.05%, W: 0.10% and Co: 0.10%; preferably Cu: 0.25%, Mo: 0.25%, Sn: 0.04%, W: 0.08% and Co: 0.06%; more preferably Cu: 0.20%, Mo: 0.20%, Sn: 0.03%, W: 0.05% and Co: 0.05%. The lower limits of these components may be set to 0.001% as an unavoidable level.
  • Ti, Nb, V and Zr may be effective in enhancing the grain boundary corrosion resistance by combining with C and N so as to form a precipitate, to thereby reduce the amounts of C and N capable of forming a solid solution in the steel.
  • an excessive addition of these elements may allow a liquid phase film due to the production of carbide so as to promote the high-temperature cracking and deteriorate the weldability.
  • the upper limits of the elements above may be Ti: 0.03%, Nb: 0.03%, V: 0.2% and Zr: 0.03%; preferably Ti: 0.02%, Nb: 0.02%, V: 0.1% and Zr: 0.01%; more preferably Ti: 0.015%, Nb: 0.015%, V: 0.05% and Zr: 0.005%.
  • the lower limits of those elements may be set all to 0.001% as an unavoidable level.
  • B and Mg may be elements which are effective in improving the hot formability, but their excessive addition may deteriorate the weldability. Therefore, the contents thereof may be B: from 0.00001 to 0.001% and Mg: from 0.00001 to 0.001%; preferably B: from 0.00001 to 0.0008% and Mg: from 0.00001 to 0.0006%; more preferably B: from 0.00001 to 0.0005% and Mg: from 0.00001 to 0.0004%.
  • REM may include La, Ce, Y, etc.
  • REM may be an element which is effective in enhancing the hot formability, but an excessive addition thereof may deteriorate the weldability. Therefore, the content thereof may be REM: from 0.00001 to 0.01%; suitably REM: from 0.00001 to 0.005%; more preferably REM: from 0.00001 to 0.003%.
  • Each of austenitic stainless steels composed of components shown in Tables 1 and 2 was melted in a vacuum melting furnace, cast into a steel ingot of 50 kg, and cut out in a block shape. Thereafter, the block which had been cut out was subjected to hot rolling, annealing/pickling, cold rolling, and annealing/pickling, to thereby produce a steel plate having a thickness of 0.8 mm. Then, each of the resultant steel plates was evaluated.
  • Tables 1 and 2 each of P, S, O and N may be contained as an impurity. Further, the blank column in the Tables indicates that the element was not added.
  • the numerical value outside the scope of the present invention is underlined.
  • each of the above steel plates was subjected to a welding test.
  • the welding method should not be limited, and welding may be conducted by using a filler material (or filler metal), or without using a filler material or a welding rod.
  • the test was conducted by TIG welding in this Example. That is, on the surface of a 50 mm-square test material which had been cut out from the steel plate as described above, TIG welding was applied in a ring configuration with a diameter of 35 mm. Further, TIG welding (without using a welding rod) was applied linearly from a corner to the opposing corner of the test material so as to intersect the welded part having the ring configuration.
  • the welding by TIG welding was conducted at a welding speed of 50 cm/min under argon gas sealing.
  • the welding heat input in the TIG welding was 720 J/cm for TIG welding in a ring configuration and 600 J/cm for TIG welding (without a welding rod) in a linear configuration.
  • the occurrence of high-temperature cracking during the welding was evaluated by increasing the welding heat gain in TIG welding so as to set up the conditions such that the amount of welding penetration was excessively increased and high-temperature cracking was liable to occur.
  • weld cracking evaluation of the occurrence of high-temperature cracking during the welding
  • the occurrence or no occurrence of the cracking in the finally solidified part after the TIG welding (without a welding rod) in a linear configuration was observed on both front and back surfaces by using a magnifier (magnification of 10 times).
  • the score of the weld cracking was 0.5, when the cracking was observed on either the front or back surface, and the score was 1 (one), when the cracking was observed on both the front and back surfaces.
  • the evaluations were conducted by using 5 test materials, the incidence of the cracking was determined from the score of the occurrence of the cracking.
  • test material of which the incidence of cracking exceeded 30%, was judged as "failed" because of bad weldability.
  • the evaluation results of bead width of the back surface/bead width of front surface, which had been determined by measuring the bead width on front and back surfaces by using a ruler are shown together.
  • weld workability the welding penetration when the welding heat input is low and the amount of welding penetration is liable to be excessively decreased was evaluated.
  • TIG welding without a welding rod
  • the bead width was measured on the front and back surfaces by using a ruler.
  • the test material where bead width of back surface/bead width of front surface ⁇ 0.5 was judged as "failed" because of bad welding penetration.
  • a continuous oxidation test was conducted at 1,000°C for 200 hours in the atmosphere by using a test piece of 20 mm x 30 mm, and the oxidation resistance was evaluated in terms of the oxidation increment. The test piece where the oxidation increment exceeded 5 g/m 2 was judged as "failed".
  • Fig. 1 shows a relationship among the amounts added of Al and Ca, which are features of the present invention, and the weldability index.
  • the region where the solidification cracking at the time of excessive welding heat input may be suppressed by adding appropriate amounts of Al and Ca is shown by a region above the lower limit line of formula (1) in the Figure.
  • the region where the excessive addition of Al and Ca may decrease the welding penetration is shown by a region below the upper limit line of formula (1), the upper limit line of Al, and the upper limit line of Ca.
  • the solidification cracking at the time of excessive heat input did not occur and the performance in terms of the weld cracking was good.
  • the insufficient welding penetration at the time of low heat input was not caused and the welding workability was good.
  • Comparative Examples outside the scope of the present invention the solidification cracking or insufficient welding penetration was observed.
  • the present invention may provide an austenitic stainless steel with excellent weldability for an article having a tubular structure. Therefore, the present invention may greatly enhance the welding workability at the time of producing an article with a tubular structure having a complicated shape, and may be of great industrial value.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Arc Welding In General (AREA)
EP13749790.5A 2012-02-15 2013-02-15 Austenitischer edelstahl für vorrichtung zur hochtemperaturverwendung mit geschweisster röhrenförmiger struktur Active EP2816133B1 (de)

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JP2012030415A JP5780598B2 (ja) 2012-02-15 2012-02-15 溶接管構造高温機器用オーステナイト系ステンレス鋼
PCT/JP2013/053764 WO2013122234A1 (ja) 2012-02-15 2013-02-15 溶接管構造高温機器用オーステナイト系ステンレス鋼

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EP2816133A4 EP2816133A4 (de) 2016-05-04
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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111004976A (zh) * 2019-12-30 2020-04-14 钢铁研究总院 一种节镍型气阀合金及其制备方法
WO2021037926A1 (de) * 2019-08-29 2021-03-04 Mannesmann Stainless Tubes GmbH Austenitische stahllegierung mit verbesserter korrosionsbeständigkeit bei hochtemperaturbeanspruchung und verfahren zur herstellung eines rohrkörpers hieraus
CN115896647A (zh) * 2022-11-16 2023-04-04 江苏新华合金有限公司 一种气氛保护退火炉用耐热钢无缝管坯材料的制造工艺方法

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
ES2922626T3 (es) * 2016-03-29 2022-09-19 Jfe Steel Corp Chapa de acero inoxidable ferrítico utilizada para soldadura TIG
US20210292876A1 (en) * 2016-10-03 2021-09-23 Nippon Steel Corporation Austenitic Heat Resistant Alloy and Welded Joint Including the Same
KR102506230B1 (ko) * 2017-10-03 2023-03-06 닛폰세이테츠 가부시키가이샤 오스테나이트계 스테인리스강

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4172716A (en) * 1973-05-04 1979-10-30 Nippon Steel Corporation Stainless steel having excellent pitting corrosion resistance and hot workabilities
JPS5929104B2 (ja) * 1980-05-20 1984-07-18 愛知製鋼株式会社 熱間加工性、耐酸化性のすぐれたオ−ステナイト系耐熱鋼
JPH0762171B2 (ja) * 1989-07-28 1995-07-05 新日本製鐵株式会社 伸線性ならびに冷間圧延性に優れたオーステナイト系ステンレス鋼の製造方法
JP2533968B2 (ja) * 1990-10-05 1996-09-11 新日本製鐵株式会社 ミグ溶接作業性に優れたオ―ステナイト系ステンレス線材
JPH06306548A (ja) * 1993-04-26 1994-11-01 Nippon Steel Corp 熱間加工性に優れた耐硝酸オーステナイト系ステンレス鋼
JPH073404A (ja) * 1993-06-22 1995-01-06 Nkk Corp 清浄度と溶接性に優れたオーステナイト系ステンレス鋼
JP3358678B2 (ja) * 1994-03-23 2002-12-24 新日本製鐵株式会社 建材用オーステナイト系ステンレス鋼
JP3381457B2 (ja) 1995-05-23 2003-02-24 住友金属工業株式会社 溶接性に優れた高温用オーステナイト系ステンレス鋼
JP3239763B2 (ja) * 1996-07-08 2001-12-17 住友金属工業株式会社 耐硫酸腐食性に優れたオーステナイト系ステンレス鋼
JP3964537B2 (ja) * 1998-04-08 2007-08-22 大平洋金属株式会社 熱間加工性に優れたオーステナイト系ステンレス鋼
JP2001107196A (ja) * 1999-10-07 2001-04-17 Sumitomo Metal Ind Ltd 耐溶接割れ性と耐硫酸腐食性に優れたオーステナイト鋼溶接継手およびその溶接材料
JP3886787B2 (ja) 2001-11-22 2007-02-28 日新製鋼株式会社 アルコール系燃料改質器用オーステナイト系ステンレス鋼
JP3886786B2 (ja) 2001-11-22 2007-02-28 日新製鋼株式会社 石油系燃料改質器用オーステナイト系ステンレス鋼
JP2003286005A (ja) 2002-03-28 2003-10-07 Nisshin Steel Co Ltd 燃料改質器
JP4299507B2 (ja) * 2002-07-12 2009-07-22 日新製鋼株式会社 耐赤スケール性に優れたオーステナイト系ステンレス鋼材
JP2005023353A (ja) * 2003-06-30 2005-01-27 Sumitomo Metal Ind Ltd 高温水環境用オーステナイトステンレス鋼
JP5208354B2 (ja) * 2005-04-11 2013-06-12 新日鐵住金株式会社 オーステナイト系ステンレス鋼
KR20090066000A (ko) * 2007-12-18 2009-06-23 주식회사 포스코 고진공, 고순도 가스 배관용 오스테나이트계 스테인리스강

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2021037926A1 (de) * 2019-08-29 2021-03-04 Mannesmann Stainless Tubes GmbH Austenitische stahllegierung mit verbesserter korrosionsbeständigkeit bei hochtemperaturbeanspruchung und verfahren zur herstellung eines rohrkörpers hieraus
CN111004976A (zh) * 2019-12-30 2020-04-14 钢铁研究总院 一种节镍型气阀合金及其制备方法
CN111004976B (zh) * 2019-12-30 2020-11-13 钢铁研究总院 一种节镍型气阀合金及其制备方法
CN115896647A (zh) * 2022-11-16 2023-04-04 江苏新华合金有限公司 一种气氛保护退火炉用耐热钢无缝管坯材料的制造工艺方法

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JP2013166989A (ja) 2013-08-29
JP5780598B2 (ja) 2015-09-16
EP2816133A4 (de) 2016-05-04
EP2816133B1 (de) 2020-08-19

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