EP3913103A1 - Ni-basierte legierung und schweissverbindung - Google Patents

Ni-basierte legierung und schweissverbindung Download PDF

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Publication number
EP3913103A1
EP3913103A1 EP21175398.3A EP21175398A EP3913103A1 EP 3913103 A1 EP3913103 A1 EP 3913103A1 EP 21175398 A EP21175398 A EP 21175398A EP 3913103 A1 EP3913103 A1 EP 3913103A1
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EP
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Prior art keywords
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content
good
based alloy
reason
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EP21175398.3A
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English (en)
French (fr)
Inventor
Hiroyuki Hirata
Mitsuru Yoshizawa
Takahiro Osuki
Masaaki Terunuma
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Nippon Steel Corp
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Nippon Steel Corp
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Publication of EP3913103A1 publication Critical patent/EP3913103A1/de
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C22C30/04—Alloys containing less than 50% by weight of each constituent containing tin or lead
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon

Definitions

  • the present invention relates to a Ni-based alloy tube and a welded joint.
  • Some kind of plant equipment is produced by constructing by welding.
  • a weld bead shape may influence on corrosion behavior.
  • some kind of heat exchanger consists of Ni-base alloy tubes serving as passage of coolant and constructed by butt-welding.
  • various kinds of corrosive fluid flow inside the tubes.
  • the corrosive fluid accumulates and concentrates at a toe of weld, where a surface of the bead and a surface of a base metal intersect with each other.
  • corrosion is liable to proceed at the toe of weld, which raises a problem.
  • Patent Documents 1 to 8 have no discussions about these problems.
  • Ni-based alloy having high corrosion resistance is used as a material to produce tubes, it is difficult to form an internal bead having an appropriate shape during butt welding and making corrosion not liable to proceed between the tubes.
  • a problem is that it is difficult to obtain a Ni-based alloy tube that allows an internal bead to be stably formed inside during welding and prevents a reinforcement with excessive height.
  • an objective of the present invention is to solve the problems described above and to provide a Ni-based alloy tube that allows an internal bead having good properties of its weldment to be formed stably, and a welded joint.
  • the present invention is made to solve the above problems, and the gist of the present invention is the following Ni-based alloy tube and welded joint.
  • the present invention makes it possible to obtain a Ni-based alloy tube that allows an internal bead having good properties of a weldment to be formed stably.
  • Figure 1 is a diagram illustrating a bevel shape in EXAMPLE.
  • the present inventors studied weldability of a Ni-based alloy tube and obtained the following findings (a) to (d).
  • the content of C is set at 0.050% or less.
  • the content of C is to be preferably 0.025% or less, more preferably 0.020% or less, and still more preferably 0.015% or less. From the viewpoint of corrosion resistance, the content of C is desirably reduced as much as possible, but an excessive reduction of the content of C increases production costs. For this reason, the content of C is to be 0.001% or more.
  • the content of C is to be preferably 0.002% or more, more preferably 0.003% or more, and still more preferably 0.005% or more.
  • Si has a deoxidation effect.
  • a content of Si is to be 0.05% or more.
  • the content of Si is to be preferably 0.08% or more, more preferably 0.10% or more, and still more preferably 0.12% or more.
  • the content of Si is to be 0.50% or less.
  • the content of Si is to be preferably 0.48% or less, more preferably 0.45% or less, and still more preferably, the content of Si is to be 0.40% or less.
  • Mn has a deoxidation effect.
  • Mn has an effect of increasing a phase stability of metal and makes no small contribution to stable formation of the internal bead.
  • a content of Mn is to be 0.05% or more.
  • the content of Mn is to be preferably 0.10% or more, more preferably 0.15% or more, and still more preferably 0.20% or more.
  • the content of Mn is to be 1.00% or less.
  • the content of Mn is to be preferably 0.90% or less, and more preferably 0.80% or less. Still more preferably, the content of Mn is to be 0.70% or less.
  • a content of P is to be 0.025% or less.
  • the content of P is to be preferably 0.023% or less, and more preferably 0.020% or less.
  • the content of P is preferably reduced as much as possible, but an excessive reduction of the content of P increases production costs. For this reason, the content of P is to be preferably 0.001% or more, and more preferably 0.002% or more.
  • S is normally contained in the Ni-based alloy as an impurity, but in the alloy tube according to the present invention, S has an effect of increasing capability of forming the internal bead together with O during welding. For this reason, a content of S is to be 0.0001% or more.
  • the content of S is to be preferably 0.0002% or more, and more preferably 0.0003% or more.
  • the content of S is to be 0.0030% or less.
  • the content of S is to be preferably 0.0025% or less, and more preferably 0.0020% or less. Note that S is required to satisfy Formula (i) described below together with O and Sn.
  • Fe is useful for increasing hot workability.
  • Fe contributes to reduction of an alloy cost.
  • a content of Fe is to be 18.0% or more.
  • the content of Fe is to be preferably 18.5% or more, and more preferably 19.0% or more. Still more preferably, the content of Fe is to be 25.0% or more.
  • the content of Fe is to be 40.0% or less.
  • the content of Fe is to be preferably 39.5% or less, and more preferably 39.0% or less. Still more preferably, the content of Fe is to be 35.0% or less.
  • Cu increases phase stability of metal and has an effect of increasing corrosion resistance under an environment where non-oxidizing acid and chloride are present. For this reason, a content of Cu is to be 1.50% or more.
  • the content of Cu is to be preferably 1.52% or more, more preferably 1.55% or more, and still more preferably 1.57% or more.
  • the content of Cu is to be 3.00% or less.
  • the content of Cu is to be preferably 2.98% or less, and more preferably 2.95% or less. Still more preferably, the content of Cu is to be 2.80% or less.
  • Co has an effect of increasing phase stability of metal.
  • a content of Co is to be 0.01% or more.
  • the content of Co is to be preferably 0.02% or more, and more preferably 0.03% or more. Still more preferably, the content of Co is to be 0.05% or more.
  • the content of Co is to be 0.80% or less.
  • the content of Co is to be preferably 0.78% or less, more preferably 0.75% or less, and still more preferably 0.70% or less.
  • Cr is an element that is essential in keeping corrosion resistance.
  • Cr causes formation of a passivation film on a surface, increasing corrosion resistance under an acid environment of oxidative properties.
  • a content of Cr is to be 19.5% or more.
  • the content of Cr is to be preferably 19.7% or more, more preferably 20.0% or more, and still more preferably 20.2% or more.
  • the content of Cr is to be 23.5% or less.
  • the content of Cr is to be preferably 23.0% or less, more preferably 22.5% or less, and still more preferably 22.3% or less.
  • Mo increases corrosion resistance under an environment where non-oxidizing acid and chloride are present. For this reason, a content of Mo is to be 2.4% or more.
  • the content of Mo is to be preferably 2.6% or more, more preferably 2.8% or more, and still more preferably 2.9% or more.
  • the content of Mo is to be 3.6% or less.
  • the content of Mo is to be preferably 3.4% or less, more preferably 3.2% or less, and still more preferably 3.1% or less.
  • W increases corrosion resistance under an environment where non-oxidizing acid and chloride are present.
  • a content of W is to be 0.01% or more.
  • the content of W is to be preferably 0.02% or more, more preferably 0.03% or more, and still more preferably 0.04% or more.
  • the content of W is to be 0.80% or less.
  • the content of W is to be preferably 0.70% or less, more preferably 0.60% or less, and still more preferably 0.50% or less.
  • Ti forms its carbide to contribute to strengthening and to prevent or reduce formation of Cr carbide, so as to mitigate deterioration in corrosion resistance of grain boundaries.
  • a content of Ti is to be 0.50% or more.
  • the content of Ti is to be preferably 0.55% or more, more preferably 0.60% or more, and still more preferably 0.65% or more.
  • the content of Ti is to be 1.20% or less.
  • the content of Ti is to be preferably 1.00% or less, more preferably 0.80% or less, and still more preferably 0.75% or less.
  • N contributes to phase stability of metal and has an effect of increasing pitting resistance. For this reason, a content of N is to be 0.0010% or more.
  • the content of N is to be preferably 0.0020% or more, more preferably 0.0030% or more, and still more preferably 0.0040% or more.
  • the content of N is to be 0.0200% or less.
  • the content of N is to be preferably 0.0180% or less, more preferably 0.0150% or less, and still more preferably, the content of N is to be 0.0130% or less.
  • Al has a deoxidation effect. Al contributes to increase in oxidation resistance at high temperature. For this reason, a content of Al is to be 0.001% or more.
  • the content of Al is to be preferably 0.005% or more, and more preferably 0.010% or more. Still more preferably, the content of Al is to be 0.020% or more.
  • the content of Al is to be 0.200% or less.
  • the content of Al is to be preferably 0.180% or less, and more preferably 0.160% or less. Still more preferably, the content of Al is to be 0.150% or less.
  • O is normally contained in the Ni-based alloy as an impurity, but in the alloy tube according to the present invention, O has an effect of increasing capability of forming the internal bead together with S during welding. For this reason, a content of O is to be 0.0004% or more.
  • the content of O is to be preferably 0.0006% or more, and more preferably 0.0008% or more.
  • the content of O is set at 0.0120% or less.
  • the content of O is to be preferably 0.0100% or less, and more preferably 0.0080% or less. Note that O is required to satisfy Formula (i) described below together with S and Sn.
  • Sn may be contained within the range described below.
  • Sn has an effect of increasing a penetration depth during welding, increasing a capability of forming the internal bead. Therefore, it may be contained when necessary. However, if Sn is contained excessively, hot workability is decreased, and weld crack susceptibility is increased. In addition, the internal bead is liable to have a convex shape. For this reason, a content of Sn is to be 0.030% or less.
  • the content of Sn is to be preferably 0.028% or less, and more preferably 0.025% or less.
  • the content of Sn is to be preferably 0.001% or more, more preferably 0.002% or more, and still more preferably 0.003% or more. Note that Sn is required to satisfy Formula (i) described below together with S and O.
  • S and O are surface-active elements and have an action of strengthening inward convection in a molten pool during welding.
  • Sn contributes to formation of an arc energizing path and has an effect of increasing a degree of concentration of an arc. Welding heat is thereby transmitted in a depth direction at a center of the molten pool.
  • the middle value of Formula (i) is to be 0.0010% or more.
  • the middle value of Formula (i) is to be preferably 0.0012% or more, and more preferably 0.0015% or more.
  • the middle value of Formula (i) is more than 0.0220%, a surface tension of molten metal is decreased, or melting of the center of the molten pool is accelerated, which causes sagging. As a result, the internal bead is made to have a convex shape, and it is no longer possible to form the internal bead stably inside the tube. Therefore, the middle value of Formula (i) is to be 0.0220% or less.
  • the middle value of Formula (i) is to be preferably 0.0215% or less, and more preferably 0.0210% or less.
  • one or more elements selected from V, Nb, Ta, Ca, Mg, B, and REM may be contained within the ranges described below. Reasons for limiting a content of each element will be described.
  • V 0.40% or less
  • V combines with carbon to form its carbide, preventing or reducing formation of Cr carbide, so as to mitigate deterioration in corrosion resistance of grain boundaries. Therefore, it may be contained when necessary. However, if V is contained excessively, carbide and carbo-nitride of V precipitate in a large quantity, decreasing ductility. For that reason, the content of V is to be 0.40% or less. The content of V is to be preferably 0.35% or less, and more preferably 0.30% or less. On the other hand, to obtain the effect described above, the content of V is to be preferably 0.01% or more, and more preferably 0.02% or more.
  • Nb combines with carbon to form its carbide, preventing or reducing formation of Cr carbide, so as to mitigate deterioration in corrosion resistance of grain boundaries. Therefore, it may be contained when necessary. However, if Nb is contained excessively, carbide and carbo-nitride of Nb precipitate in a large quantity, decreasing ductility. In addition, weld crack susceptibility is increased. For that reason, a content of Nb is to be 0.40% or less. The content of Nb is to be preferably 0.35% or less, and more preferably 0.30% or less. On the other hand, to obtain the effect described above, the content of Nb is to be preferably 0.01% or more, and more preferably 0.02% or more.
  • Ta accelerates formation of a passivation film of Cr and has an effect of increasing corrosion resistance. Therefore, it may be contained when necessary. However, if Ta is contained excessively, carbide of Ta precipitates in a large quantity, decreasing ductility. For that reason, a content of Ta is to be 0.40% or less.
  • the content of Ta is to be preferably 0.35% or less, and more preferably 0.30% or less.
  • the content of Ta is to be preferably 0.01% or more, and more preferably 0.02% or more.
  • Ca has an effect of improving hot workability. Therefore, it may be contained when necessary. However, if Ca is contained excessively, Ca combines with oxygen, significantly decreasing cleanliness. As a result, hot workability is rather decreased. For this reason, a content of Ca is to be 0.0100% or less.
  • the content of Ca is to be preferably 0.0080% or less, and more preferably 0.0060% or less.
  • the content of Ca is to be preferably 0.0005% or more, and more preferably 0.0010% or more.
  • Mg has an effect of improving hot workability. Therefore, it may be contained when necessary. However, if Mg is contained excessively, Mg combines with oxygen, significantly decreasing cleanliness. As a result, hot workability is rather decreased. For this reason, a content of Mg is to be 0.0100% or less.
  • the content of Mg is to be preferably 0.0080% or less, and more preferably 0.0060% or less.
  • the content of Mg is to be preferably 0.0005% or more, and more preferably 0.0010% or more.
  • B segregates in grain boundaries at high temperature and has effects of strengthening the grain boundaries and increasing hot workability. Therefore, it may be contained when necessary. However, if B is contained excessively, weld crack susceptibility is increased. For this reason, a content of B is set at 0.0100% or less.
  • the content of B is to be preferably 0.0080% or less, and more preferably 0.0060% or less.
  • the content of B is to be preferably 0.0002% or more, and more preferably 0.0005% or more.
  • REM has an effect of improving hot workability in production. Therefore, it may be contained when necessary. However, if REM is contained excessively, REM combines with oxygen, significantly decreasing cleanliness. As a result, hot workability is rather decreased. For this reason, a content of REM is set at 0.0800% or less.
  • the content of REM is to be preferably 0.0600% or less, and more preferably 0.0500% or less.
  • the content of REM is to be preferably 0.0005% or more, and more preferably 0.0010% or more.
  • REM refers to Sc, Y, and lanthanoids
  • the content of REM refers to the amount of these elements.
  • the balance is Ni and impurities.
  • impurities means elements that are not added intentionally but are mixed in the Ni-based alloy in producing the Ni-based alloy industrially due to various factors such as raw materials and a production process, and that are allowed to be within ranges in which the impurities have no adverse effect on the present invention.
  • An internal bead is formed when end portions of alloy tubes are welded together. To form a favorable internal bead, it is preferable to control, an arithmetic average roughness Ra on an internal surface of the alloy tube in a longitudinal direction.
  • An internal surface roughness of the alloy tube herein refers to a surface roughness after a final process in a production process. In other words, although the internal surface roughness of the alloy tube fluctuates in a course of the production, a surface roughness in a middle of the production does not matter in obtaining an advantageous effect of the present invention, and it will suffice that the internal surface roughness of the tube in the longitudinal direction after the final process satisfies a range specified in the present invention.
  • the arithmetic average roughness Ra of the tube in the longitudinal direction is more than 9.0 ⁇ m, weld metal is hindered from wetting on the internal surface of the tube, and thus the weld metal resists spreading along a width direction, that is, a circumference of the tube.
  • the internal bead is liable to have a convex shape, and a height of reinforcement is liable to increase.
  • the arithmetic average roughness Ra of the tube in the longitudinal direction is to be preferably 9.0 ⁇ m or less.
  • the arithmetic average roughness Ra is to be preferably 7.0 ⁇ m or less, and more preferably 5.0 ⁇ m or less.
  • a lower limit value of the arithmetic average roughness Ra is not limited to a specific value; however, in many cases, the arithmetic average roughness Ra is normally 0.1 to 1.0 ⁇ m or more in a case where a production method described below is used.
  • the arithmetic average roughness Ra is specified in JIS B 0601:2001 and can be measured by using a contact-type surface roughness instrument.
  • a welded joint of Ni-based alloy tubes described above can be obtained by performing butt welding on tube ends of the Ni-based alloy tubes under predetermined conditions.
  • the welded joint of the Ni-based alloy tubes includes weld metal which is to be a weldment by solidification, and base material portion.
  • the base material portions each include a weld heat affected zone that is influenced by heat input of welding.
  • the base material portion excluding the weld heat affected zone inherits the chemical composition, the surface roughness, and other properties of the Ni-based alloy tube described in Sections 1 and 2 described above.
  • the weldment refers to the weld metal and the weld heat affected zone.
  • Ni-based alloy tube according to the present invention provides its advantageous effects irrespective of its production method as long as the Ni-based alloy tube has the requirement described above; nonetheless, the Ni-based alloy tube can be produced stably by a production method described below, for example.
  • Ni-based alloy ingot being a starting material of the Ni-based alloy tube is produced.
  • the Ni-based alloy ingot is preferably produced by melting an alloy having the chemical composition described above using an electric furnace, refining the alloy to remove impurities, and casting the alloy. Subsequently, the obtained ingot is preferably subjected to hot forging to be formed into a billet having a columnar shape. Thereafter, the obtained billet is worked to be shaped into a tube.
  • the billet is preferably subjected to hot extrusion and then to cold rolling or cold drawing. Softening heat treatment and intermediate pickling may be performed in the middle of the working when necessary. Thereafter, the alloy tube is preferably subjected to solution treatment as heat treatment. After the solution treatment, pickling or working may be performed when necessary.
  • the solution treatment is preferably performed under such conditions of heating in a temperature region of 950°C to 1230°C for 1 to 15 minutes and performing water cooling. Additionally, it is preferable to perform one of machining such as grinder processing and grinding, and shotblast or shotpeening treatment, on the internal surface of the tube.
  • an advantageous effect of the present invention does not pertain to the surface roughness in the middle of the course and is influenced only by the surface roughness of the tube in the longitudinal direction after the final process.
  • a welded joint can be obtained by welding together end portions of Ni-based alloy tubes according to the present invention as starting materials.
  • a method for the welding is not limited to a specific method; however, the welding can be performed by arc welding, for example.
  • a heat input is preferably set to be within the range from 4 to 20 kJ/cm.
  • Ar gas as shielding gas and back shielding gas during welding.
  • a flow rate of the gas flowed to a welding location is preferably adjusted as appropriate.
  • a chemical composition of a welding material (filler material) to be used is not limited to a specific material, either; however, the chemical composition is preferably a composition described below.
  • the composition it is preferable for the composition to contain, in mass%, C: 0.150% or less, Si: 1.00% or less, Mn: 3.50% or less, P: 0.030% or less, S: 0.0001 to 0.0100%, Fe: 38.0% or less, Cu: 3.00% or less, Co: 15.0% or less, Cr: 14.0 to 26.0%, Mo: 17.0% or less, W: 4.5% or less, at least one of Nb and Ta: 4.20% or less in total, Ti: 1.50% or less, V: 0.35% or less, N: 0.0500% or less, Al: 1.50% or less, and O: 0.0004 to 0.0120%, with the balance being Ni and impurities, and to make a relation between contents of S and O satisfy Formula (a) shown below.
  • Formula (a) shown below.
  • the alloy plates were performed solution treatment that the alloy plates were retained in a hydrogen furnace at 1150°C for 10 minutes and cooled by water cooling. Thereafter, test plates each having a width of 50 mm and a length of 100 mm were cut from the alloy plates.
  • shotpeening was conducted on only one side, assuming the internal surface of the alloy tube, as shown in Table 2.
  • one side of test plates were machine-ground or polished 1 to 5 times using a whetstone with granularity of #40 or #60.
  • polishing (#40 ⁇ 1 time) indicates that a test plate was polished once using a whetstone with a granularity of #40.
  • welded joints each of which a back bead was formed across an overall length of its weld line were determined to have no problem in capability of forming an internal bead of the alloy tube and were rated as "Good".
  • welded joints each of which a width of a back bead was 2 mm or more across an overall length of its weld line were rated as "Excellent”, and welded joints each of which a width of a back bead formed was less than 2 mm but 1 mm or more were rated as "Acceptable”.
  • a back bead in this example corresponds to an internal bead that is formed when the weld is made from the outside of the alloy tube.
  • Test pieces made of alloy types A to H and L to N all satisfied the specifications according to the present invention, and their capabilities of forming a back bead and shapes of their back beads were good.
  • the test piece N1 made of the alloy type N satisfied the range specified by Formula (i), and therefore, its capability of forming a back bead and a height of its back bead were both satisfactory.
  • test pieces I1 and K1 made of the alloy types I and K their contents of S and O did not satisfy Formula (i) and were higher than the respective specified ranges. Therefore, sagging of its molten metal was significant, and a height of its back bead did not satisfy a target of the height.
  • a test piece J1 made of the alloy type J a relation between its contents of S and O did not satisfy Formula (i), and the contents were lower than the respective specified ranges. Therefore, melting in a plate thickness direction was not sufficient, and a capability of forming the back bead as targeted was not obtained.
  • test piece O1 made of the alloy type O its contents of S, O, and Sn were lower than the range specified by Formula (i). Therefore, melting in a plate thickness direction was not sufficient, and a capability of forming the back bead did not satisfy a target of the capability.
  • test pieces P1 and Q1 made of the alloy types P and Q1 their contents of S, O and Sn were higher than the range specified by Formula (i), or their contents of Sn were more than the specified range. Therefore, sagging of its molten metal was large, and a back bead height as targeted was not satisfied.
  • the present invention makes it possible to obtain a Ni-based alloy tube that allows an internal bead to be formed stably during butt welding and prevents a reinforcement with excessive height.

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EP21175398.3A 2020-05-22 2021-05-21 Ni-basierte legierung und schweissverbindung Pending EP3913103A1 (de)

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Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS54110918A (en) 1978-02-21 1979-08-30 Cabot Corp Anticorrosion nickel alloy
JPS6389637A (ja) 1986-10-01 1988-04-20 インコ、アロイス、インターナショナル　インコーポレーテッド 耐食性高強度ニッケル基合金
JPH02156034A (ja) 1988-10-21 1990-06-15 Inco Alloys Internatl Inc 耐食性ニッケル基合金
JPH03173732A (ja) 1989-11-17 1991-07-29 Haynes Internatl Inc 耐食性の良好なニッケル基合金
JPH05271832A (ja) 1992-02-06 1993-10-19 Krupp Vdm Gmbh 耐食性ニッケル基オースナイト合金および耐食部材
JPH0987786A (ja) 1995-09-27 1997-03-31 Sumitomo Metal Ind Ltd 高Ｍｏニッケル基合金および合金管
JPH1030140A (ja) 1996-07-15 1998-02-03 Sumitomo Metal Ind Ltd 耐食性と加工性に優れたニッケル基合金
EP1637785A1 (de) * 2004-09-15 2006-03-22 Sumitomo Metal Industries, Ltd. Stahl-Rohr mit ausgezeichneter Beständigkeit gegen Abblättern auf der inneren Oberfläche
EP2415883A1 (de) * 2009-04-01 2012-02-08 Sumitomo Metal Industries, Ltd. Verfahren zur herstellung eines hochfesten nahtlosen rohrs aus einer cr-ni-legierung
JP2012072446A (ja) 2010-09-29 2012-04-12 Sumitomo Chemical Co Ltd 耐食性部材
WO2018002328A1 (en) * 2016-07-01 2018-01-04 Sandvik Intellectual Property Ab A new process for manufacturing an austenitic alloy

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6323188B2 (ja) * 2014-06-11 2018-05-16 新日鐵住金株式会社 Ｎｉ基耐熱合金溶接継手の製造方法

Patent Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS54110918A (en) 1978-02-21 1979-08-30 Cabot Corp Anticorrosion nickel alloy
JPS6389637A (ja) 1986-10-01 1988-04-20 インコ、アロイス、インターナショナル　インコーポレーテッド 耐食性高強度ニッケル基合金
JPH02156034A (ja) 1988-10-21 1990-06-15 Inco Alloys Internatl Inc 耐食性ニッケル基合金
JPH03173732A (ja) 1989-11-17 1991-07-29 Haynes Internatl Inc 耐食性の良好なニッケル基合金
JPH05271832A (ja) 1992-02-06 1993-10-19 Krupp Vdm Gmbh 耐食性ニッケル基オースナイト合金および耐食部材
JPH0987786A (ja) 1995-09-27 1997-03-31 Sumitomo Metal Ind Ltd 高Ｍｏニッケル基合金および合金管
JPH1030140A (ja) 1996-07-15 1998-02-03 Sumitomo Metal Ind Ltd 耐食性と加工性に優れたニッケル基合金
EP1637785A1 (de) * 2004-09-15 2006-03-22 Sumitomo Metal Industries, Ltd. Stahl-Rohr mit ausgezeichneter Beständigkeit gegen Abblättern auf der inneren Oberfläche
EP2415883A1 (de) * 2009-04-01 2012-02-08 Sumitomo Metal Industries, Ltd. Verfahren zur herstellung eines hochfesten nahtlosen rohrs aus einer cr-ni-legierung
JP2012072446A (ja) 2010-09-29 2012-04-12 Sumitomo Chemical Co Ltd 耐食性部材
WO2018002328A1 (en) * 2016-07-01 2018-01-04 Sandvik Intellectual Property Ab A new process for manufacturing an austenitic alloy

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