EP2816133B1 - Austenitischer edelstahl für vorrichtung zur hochtemperaturverwendung mit geschweisster röhrenförmiger struktur - Google Patents

Austenitischer edelstahl für vorrichtung zur hochtemperaturverwendung mit geschweisster röhrenförmiger struktur Download PDF

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EP2816133B1
EP2816133B1 EP13749790.5A EP13749790A EP2816133B1 EP 2816133 B1 EP2816133 B1 EP 2816133B1 EP 13749790 A EP13749790 A EP 13749790A EP 2816133 B1 EP2816133 B1 EP 2816133B1
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welding
stainless steel
austenitic stainless
tubular structure
weldability
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EP2816133A4 (de
EP2816133A1 (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 for an article having a welded tubular structure, which is to be used at a high temperature, an article having a tubular structure comprising said austenitic stainless steel, and a method for producing a welded structural body involving TIG welding using said austenitic stainless steel.
  • 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).
  • JP H03-61322 describes that a hot rolling stock of austenitic stainless steel which has a composition containing, by weight, C: 0.005-0.10%, Si: 0.2-1.0%, Mn: 0.2-2.5%, P: ⁇ 0.045%, S: ⁇ 0.020%, Ni: 6-20%, Cr: 15-25%, N: 0.01-0.10%, Al: 0.0005-0.005%, Ca: 0.0001-0.002%, Mg: 0.0001-0.001%, and O: ⁇ 0.0025% or further containing Mo and/or Cu: 0.5-3.5%; is heated at 1000-1300°C for ⁇ 10 min to undergo hot rolling.
  • the hot rolled stock is annealed, pickled, and cold-drawn or cold-rolled into an extra fine wire or foil shape. By this method, an extra fine wire or foil of the stainless steel free from breaking of wire and fracture can be produced.
  • 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 present invention provides an austenitic stainless steel for an article having a tubular structure, consisting of, in mass%,
  • 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 is 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 is 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 is set to 1.5%. For this reason, the upper limit may preferably be 1.0%, more preferably 0.8%. The lower limit is 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 is set to 1.5% or less.
  • the upper limit may preferably be 1.3%, more preferably 1.0%.
  • the lower limit is 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 is 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 is 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 is 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 is 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 is 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 is set to 0.07%.
  • the upper limit may preferably be 0.06%, more preferably 0.05%.
  • the lower limit is 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 is set to 0.05%. For this reason, the upper limit may preferably be 0.045%, more preferably 0.035%. Further, the lower limit is 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 is set to 0.005% or less. For this reason, the upper limit may preferably be 0.004%, more preferably 0.003%.
  • the lower limit is 0.0003% in consideration of the production cost. For this reason, the lower limit may preferably be 0.0005%, more preferably 0.0008%.
  • Weldability Index As the weldability index for an adequate amount of welding penetration so as to inhibit the high-temperature cracking, 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.
  • 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 are Cu: 0.3%, Mo: 0.3%, 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 are 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 are 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 are 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 are 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 is 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 ⁇ 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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Claims (6)

  1. Ein austenitischer rostfreier Stahl für einen Gegenstand mit einer röhrenförmigen Struktur, bestehend aus, in Massen-%,
    C: von 0,001 bis 0,2%,
    Si: von 0,01 bis 1,5%,
    Mn: von 0,01 bis 1,5%,
    Cr: von 20,0 bis 26,0%,
    Ni: von 15,0 bis 23,0%,
    N: von 0,001 bis 0,07%,
    Al: von 0,003 bis 0,05%, und
    Ca: von 0,0003 bis 0,005%, und
    gegebenenfalls weiter ein Element oder zwei oder mehrere Elemente aus, in Massen-%,
    Cu: von 0,001 bis 0,3%,
    Mo: von 0,001 bis 0,3%,
    Sn: von 0,001 bis 0,05%,
    W: von 0,001 bis 0,10%,
    Co: von 0,001 bis 0,10%,
    Ti: von 0,001 bis 0,03%,
    Nb: von 0,001 bis 0,03%,
    V: von 0,001 bis 0,2%,
    Zr: von 0,001 bis 0,03%,
    B: von 0,00001 bis 0,001%,
    Mg: von 0,00001 bis 0,001%, und
    Seltenerdmetalle: 0,00001 bis 0,01%,
    wobei der Rest aus Fe und unvermeidbaren Verunreinigungen besteht,
    wobei die Anteile an P und S als Verunreinigungen begrenzt sind auf, in Massen-%,
    P: ≤ 0,022%, und
    S: ≤ 0,004%, und
    Al und Ca die folgende Formel erfüllen: 0,015 ≤ 0,29 % Al + 17,92 % Ca ≤ 0,093
    Figure imgb0010
  2. Der austenitische rostfreie Stahl für einen Gegenstand mit einer röhrenförmigen Struktur nach Anspruch 1, wobei Al und Ca die folgende Formel erfüllen: 0,03 ≤ 0,29 % Al + 17,92 % Ca ≤ 0,093
    Figure imgb0011
  3. Der austenitische rostfreie Stahl für einen Gegenstand mit einer röhrenförmigen Struktur nach Anspruch 1 oder 2, wobei die röhrenförmige Struktur ein geschweißter strukturierter Körper ist.
  4. Der austenitische rostfreie Stahl für einen Gegenstand mit einer röhrenförmigen Struktur nach Anspruch 1 oder 2, wobei ein Wulstbreitenverhältnis von Vorder- und Rückfläche (Wulstbreite der Rückfläche/Wulstbreite der Vorderfläche) 0,5 oder mehr beträgt, wenn das TIG-Schweißen in einer linearen Konfiguration mit einer Schweißgeschwindigkeit von 50 cm/min und mit einem Schweißwärmeinput von 480 J/cm durchgeführt wird, und das Wulstbreitenverhältnis von Vorder- und Rückseite 0,8 oder weniger beträgt, wenn das TIG-Schweißen in einer linearen Konfiguration mit einer Schweißgeschwindigkeit von 50 cm/min und mit einem Schweißwärmeinput von 600 J/cm durchgeführt wird, wobei das TIG-Schweißen ohne Schweißdraht erfolgt.
  5. Ein Verfahren zur Herstellung eines geschweißten strukturierten Körpers, wobei der geschweißte strukturierte Körper durch ein Verfahren hergestellt wird, das TIG-Schweißen unter Verwendung des austenitischen rostfreien Stahls für einen Gegenstand mit einer röhrenförmigen Struktur nach einem der Ansprüche 1 bis 3 umfasst.
  6. Ein Gegenstand mit einer röhrenförmigen Struktur, wobei die röhrenförmige Struktur einen austenitischen rostfreien Stahl nach einem der Ansprüche 1 bis 4 umfasst.
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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