WO2011158706A1 - MATÉRIAU DE SOUDAGE POUR ALLIAGE À BASE DE Ni RÉSISTANT À LA CHALEUR, ET MÉTAL SOUDÉ ET JOINT SOUDÉ AU MOYEN DE CELUI-CI - Google Patents

MATÉRIAU DE SOUDAGE POUR ALLIAGE À BASE DE Ni RÉSISTANT À LA CHALEUR, ET MÉTAL SOUDÉ ET JOINT SOUDÉ AU MOYEN DE CELUI-CI Download PDF

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WO2011158706A1
WO2011158706A1 PCT/JP2011/063097 JP2011063097W WO2011158706A1 WO 2011158706 A1 WO2011158706 A1 WO 2011158706A1 JP 2011063097 W JP2011063097 W JP 2011063097W WO 2011158706 A1 WO2011158706 A1 WO 2011158706A1
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welding
content
resistant alloy
cracking
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PCT/JP2011/063097
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English (en)
Japanese (ja)
Inventor
弘征 平田
満 吉澤
和博 小川
敦朗 伊勢田
潤之 仙波
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住友金属工業株式会社
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Priority to CN201180029556.8A priority Critical patent/CN102947048B/zh
Publication of WO2011158706A1 publication Critical patent/WO2011158706A1/fr

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
    • B23K35/3033—Ni as the principal 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%
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/18—Dissimilar materials
    • B23K2103/26—Alloys of Nickel and Cobalt and Chromium

Definitions

  • the present invention relates to a welding material for a Ni-base heat-resistant alloy, a weld metal and a welded joint using the same. More specifically, the present invention relates to a welding material suitable for welding a Ni-based heat-resistant alloy used in equipment used at high temperatures such as a power generation boiler, and a weld metal and a welded joint obtained by using the welding material.
  • Patent Documents 1 to 5 disclose various Ni-based alloys. These all define various alloy element ranges in order to satisfy the required performance as a base material.
  • Ni-base heat-resistant alloys When these Ni-base heat-resistant alloys are used as structures, they are generally assembled by welding.
  • the “hot cracking at the time of welding” includes “solidification cracking” and “ductility-reducing cracking”.
  • AWS A5.14-2005 ER NiCrCoMo-1 is known as a welding material for Ni-base heat-resistant alloys used when assembling by welding.
  • Patent Documents 6 to 8 propose various welding materials for Ni-based alloys.
  • Patent Document 6 discloses a welding material used for welding high-strength oxide dispersion strengthened alloys and heat-resistant alloys. By actively containing solid solution strengthening elements such as Mo and Nb, strength is increased. An improved oxide dispersion strengthened alloy welding material has been proposed. Patent Document 7 and Patent Document 8 propose a welding material for Ni-based alloys, which has been strengthened by utilizing the solid solution strengthening effect by Mo and W and the precipitation strengthening effect by Al and Ti.
  • Non-Patent Document 1 points out that intergranular cracking occurs during post-weld heat treatment in a welding heat-affected zone (hereinafter referred to as “HAZ”) of a Ni-base heat-resistant alloy. In addition to precipitation, it is suggested that S grain boundary segregation affects.
  • HZ welding heat-affected zone
  • Non-Patent Document 2 discusses measures for preventing intergranular cracking in HAZ during long-time heating of 18Cr-8Ni-Nb austenitic heat-resistant steel welds. And the countermeasure from the welding process surface that reduction of the welding residual stress by application of appropriate post-heat treatment is effective in preventing grain boundary cracking in HAZ has been proposed.
  • a weld metal obtained using the above-mentioned welding material for Ni-base heat-resistant alloys is a crack that occurs during long-term use (hereinafter referred to as “stress relaxation crack”). Is still a challenge. Also, in the above Patent Documents 6 to 8, no consideration is given to stress relaxation cracking. For this reason, the weld metal obtained using the welding materials proposed in Patent Documents 6 to 8 still has a problem with respect to stress relaxation cracking.
  • Japanese Patent Laid-Open No. 2-1077736 JP 63-050440 A Japanese Patent Laid-Open No. 7-150277 Japanese Patent Laid-Open No. 9-157779 JP 2001-073053 A Japanese Patent Laid-Open No. 10-193174 WO2010-013565 WO2007-119847
  • the present invention has been made in view of the above situation, and provides a welding material for a Ni-base heat resistant alloy having excellent hot cracking resistance at the time of welding, and hot cracking resistance during welding using the same. It is an object of the present invention to provide a weld metal having stress relaxation crack resistance and good creep strength during long-time use. Furthermore, it is also an object of the present invention to provide a welded joint comprising a weld metal using this weld material and a base material of a Ni-base heat-resistant alloy excellent in high temperature strength.
  • Non-Patent Document 1 shows that the reduction of S that weakens the grain boundaries or the inclusion of Ca and Mg to fix S is effective in preventing the cracking.
  • the weld metal is generally used in an as-solidified structure, and the phenomenon is expected to be different from HAZ based on a tempered base material such as heat treatment. It is unlikely that the proposed HAZ crack countermeasures can be applied to stress relaxation cracks as they are.
  • Ca and Mg proposed in Non-Patent Document 1 have a very strong affinity for oxygen, oxides are easily formed during welding.
  • (J) Mo contributes to the improvement of creep strength as a solid solution strengthening element, but in this case, the decrease in intra-grain deformability is small compared to the case where fine intermetallic compounds precipitate.
  • the welding material for the Ni-base heat-resistant alloy is based on an alloy of Cr: 20-25% and Ni: 46-56% by mass, C: 0.06-0.18%, Mo : By containing more than 10.0% and not more than 14% and Al: 0.1 to 1.0%, resistance to hot cracking during welding, resistance to stress relaxation cracking during long-term use at high temperature, and desired It was found that good creep strength can be secured.
  • the Ni base excellent in high-temperature strength including Ni: 46 to 56%, Cr: 20 to 25% and Mo: 7.0 to 10.0% in mass%. It is preferable to use a heat-resistant alloy as a base material because excellent creep strength can be secured even in the base material.
  • the Ni-base heat-resistant alloy having excellent high-temperature strength used as the base material may be a Ni-base heat-resistant alloy having the same chemical composition as the welding material according to the present invention, or may be different.
  • C 0.04 to 0.12%, Si: 1.0% or less, Mn: 1.5% or less, P: 0.03% or less, S: 0.01% or less, Ni: 46 to 56%, Co: 10 to 15%, Cr: 20 to 25%, Mo: 7.0 to 10.0%, W: 0.5% or less, Ti: 0.00. 1 to 0.5%, N: 0.01% or less, B: 0.005% or less, Al: 0.8 to 1.8% and Nd: 0.005 to 0.1%, the balance being It is preferable to use a Ni-base heat-resistant alloy composed of Fe and impurities and excellent in high temperature strength.
  • impurities in the “Fe and impurities” as the balance are due to various factors in the manufacturing process including raw materials such as ore or scrap when industrially manufacturing welding materials or heat-resistant alloys. It refers to what gets mixed.
  • the present invention has been completed based on the above findings, and the gist of the present invention is the welding materials shown in the following (1) and (2), the weld metal shown in (3), and (4) to (6). It is in the welded joint shown in
  • a welded joint comprising the weld metal according to (3) above and a base material of a Ni-based heat-resistant alloy having excellent high-temperature strength.
  • the base material of the Ni-based heat-resistant alloy having excellent high-temperature strength contains, by mass%, Mo: 7.0 to 10.0%, Ni: 46 to 56%, and Cr: 20 to 25%.
  • the base material of the Ni-based heat-resistant alloy having excellent high-temperature strength is, in mass%, C: 0.04 to 0.12%, Si: 1.0% or less, Mn: 1.5% or less, P: 0.03% or less, S: 0.01% or less, Ni: 46 to 56%, Co: 10 to 15%, Cr: 20 to 25%, Mo: 7.0 to 10.0%, Ti: 0.00. 1 to 0.5%, N: 0.01% or less, B: 0.005% or less, Al: 0.8 to 1.8% and Nd: 0.005 to 0.1%, the balance being It consists of Fe and an impurity, The weld joint as described in said (4) characterized by the above-mentioned.
  • a welding material for a Ni-base heat resistant alloy having excellent hot cracking resistance during welding, and using it, hot cracking resistance during welding and use at high temperatures for a long time. It is possible to provide a weld metal having moderate stress relaxation cracking resistance and good creep strength. Furthermore, using this welding material, a high temperature cracking resistance during welding, a stress relaxation cracking resistance during long-time use at high temperatures, and a base of a Ni-base heat-resistant alloy excellent in high-temperature strength and a weld metal having good creep strength. A welded joint made of a material can be provided.
  • the reason for limiting the chemical composition of the welding material for the Ni-base heat-resistant alloy is as follows.
  • “%” display of the content of each element means “mass%”.
  • C 0.06 to 0.18%
  • C is an austenite-forming element and is an element effective for enhancing the stability of the austenite structure when used at high temperatures.
  • C is an important element for preventing hot cracking during welding in the present invention. That is, C mainly binds to Cr in the solidification process to generate eutectic carbide, accelerates the disappearance of the liquid phase, and changes the structure of the final solidified portion to a lamella of (Cr, M) 23 C 6 and austenite. A tissue is used. As a result, the remaining form of the liquid phase changes from a planar shape to a point shape, and stress concentration on a specific surface is suppressed, so that solidification cracking can be prevented.
  • C increases the final solidification interface area that becomes a segregation site of impurities, and thus contributes to the prevention of ductile deterioration cracking during welding and the reduction of the sensitivity of stress relaxation cracking during high temperature use.
  • excess C that does not become carbide during solidification is finely precipitated as carbide during high temperature use, and on the contrary, the stress relaxation cracking sensitivity is increased. Therefore, the C content is 0.06 to 0.18%.
  • a desirable lower limit of the C content is 0.07%, and a desirable upper limit is 0.15%.
  • Si 0.5% or less Si is contained as a deoxidizer, but segregates at the columnar grain boundaries during solidification of the weld metal, lowers the melting point of the liquid phase, and increases the susceptibility to solidification cracking. Therefore, the Si content needs to be 0.5% or less.
  • the Si content is preferably 0.3% or less.
  • the lower limit of the Si content is not particularly set, but is desirably 0.01%. If at least 0.01% of Si is contained, a deoxidizing effect can be obtained. A more desirable lower limit of the Si content is 0.02%.
  • Mn 1.5% or less Mn is contained as a deoxidizer in the same manner as Si. However, when Mn is excessively contained, embrittlement is caused, so the Mn content needs to be 1.5% or less.
  • the Mn content is preferably 1.2% or less. Although there is no particular lower limit for the Mn content, it is preferably 0.01%. The above effect can be obtained if at least 0.01% of Mn is contained. A more desirable lower limit of the Mn content is 0.02%.
  • Ni 46-56%
  • Ni is an effective element for obtaining an austenite structure, and is an essential element for ensuring the structure stability during long-time use and obtaining sufficient creep strength.
  • a Ni content of 46% or more is necessary.
  • Ni is an expensive element, and a large amount of Ni exceeding 56% causes an increase in cost. Therefore, the Ni content is set to 46 to 56%.
  • a desirable lower limit of the Ni content is 46.5%, and a desirable upper limit is 55.5%.
  • a more desirable lower limit of the Ni content is 47%, and a more desirable upper limit is 55%.
  • Co 10-15% Co, like Ni, is an element effective for obtaining an austenite structure, and contributes to creep strength by increasing phase stability. In order to sufficiently obtain the effect, a Co content of 10% or more is necessary. However, Co is an extremely expensive element, and a large content of Co exceeding 15% causes an increase in cost. Therefore, the Co content is 10 to 15%. A desirable lower limit of the Co content is 10.5%, and a desirable upper limit is 14.5%.
  • Cr 20-25%
  • Cr is an essential element for securing oxidation resistance and corrosion resistance at high temperatures. Cr combines with C in the solidification process to produce eutectic carbide, prevents solidification cracking and ductile degradation cracking during welding, and also has the effect of reducing stress relaxation cracking susceptibility during high temperature use. In order to obtain these effects, it is necessary to contain 20% or more of Cr. However, if the Cr content is excessive and exceeds 25%, the stability of the structure at high temperatures deteriorates, leading to a decrease in creep strength. For this reason, the Cr content is 20 to 25%. A desirable lower limit of the Cr content is 20.5%, and a desirable upper limit is 24.5%. The more desirable lower limit of the Cr content is 21%, and the more desirable upper limit is 24%.
  • Mo more than 10.0% and not more than 14.0%
  • Mo is an element that contributes greatly to the improvement of creep strength at a high temperature exceeding 700 ° C. by dissolving in the matrix. Further, Mo has a strong affinity with P, and by bonding, it reduces grain boundary embrittlement due to heat treatment after welding and P during high temperature use, and contributes to prevention of stress relaxation cracking. In order to ensure such effects sufficiently to achieve both stress relaxation crack resistance and creep strength during high temperature use, the Mo content exceeds 10.0% in relation to other elements constituting the present invention. is required. However, even if Mo is excessively contained, the effect is saturated, and on the contrary, toughness and creep strength are lowered. Furthermore, Mo is an expensive element, and a large amount of Mo exceeding 14.0% causes an increase in cost.
  • the Mo content is more than 10.0% and not more than 14.0%.
  • a desirable lower limit of the Mo content is 10.5%, and a desirable upper limit is 13.8%.
  • a more desirable lower limit of the Mo content is 11.0%, and a more desirable upper limit is 13.5%.
  • Ti 0.01 to 0.5% Ti combines with Ni and precipitates finely as an intermetallic compound, thereby contributing to the improvement of creep strength at high temperatures.
  • a Ti content of 0.01% or more is necessary in relation to other elements constituting the present invention.
  • the Ti content is set to 0.01 to 0.5%.
  • a desirable lower limit of the Ti content is 0.1%, and a desirable upper limit is 0.4%.
  • Al 0.1 to 1.0%
  • Al like Ti, binds to Ni, precipitates finely as an intermetallic compound, and contributes to the improvement of creep strength at high temperatures.
  • an Al content of 0.1% or more is necessary in relation to other elements constituting the present invention.
  • the Al content is 0.1 to 1.0%.
  • a desirable lower limit of the Al content is 0.2%, and a desirable upper limit is 0.9%.
  • a more desirable lower limit of the Al content is 0.3%, and a more desirable upper limit is 0.8%.
  • N 0.006% or less
  • N is an element effective for stabilizing the austenite phase, but in the Cr content range of the present invention, if the N content becomes excessive and exceeds 0.006%. During use at a high temperature, a large amount of fine nitride precipitates in the grains, resulting in a decrease in creep ductility and toughness. Therefore, the N content is 0.006% or less.
  • a desirable upper limit of the N content is 0.005%. Although the lower limit of the N content is not particularly set, an extreme decrease leads to an increase in manufacturing cost. For this reason, the desirable lower limit of the N content is 0.0005%.
  • One of the welding materials for a Ni-base heat-resistant alloy of the present invention contains the elements C to N described above, the balance is made of Fe and impurities, and the contents of O, P and S as impurities are respectively It has a chemical composition limited to the stated range.
  • O 0.02% or less O exists as an impurity, but when it is contained in a large amount, it degrades the workability of the welding material and the ductility of the weld metal. Therefore, the content of O needs to be 0.02% or less.
  • the O content is preferably 0.015% or less.
  • P 0.008% or less
  • P is contained as an impurity, lowers the melting point of the final solidified portion during solidification of the weld metal, remarkably increases solidification cracking susceptibility, and causes intergranular embrittlement during high-temperature use, resulting in resistance to resistance. It is an element that causes a decrease in stress relaxation cracking property. Therefore, the P content needs to be 0.008% or less.
  • the P content is preferably 0.006% or less.
  • S 0.005% or less
  • S is an element that is contained as an impurity, lowers the melting point of the final solidified portion during solidification of the weld metal, and increases the susceptibility to solidification cracking. Furthermore, it is an element that segregates and concentrates at the grain boundaries during high temperature use and significantly increases the stress relaxation cracking susceptibility. Therefore, the S content needs to be 0.005% or less. The S content is preferably 0.003% or less.
  • Another one of the welding materials for Ni-base heat-resistant alloys of the present invention has a chemical composition containing 0.1% or less of Nd in place of a part of Fe in the remaining “Fe and impurities”. is there.
  • Nd 0.1% or less Nd has a strong affinity with P and forms a compound, and also combines with S and O to form a compound, suppresses weakening of grain boundaries by P and S, and stress relaxation cracking resistance It is an element that contributes to improving the properties. For this reason, you may contain Nd as needed. However, if the content of Nd becomes excessive and exceeds 0.1%, the above effect is saturated, and a large amount of carbide precipitates in the grains, which increases the stress relaxation cracking sensitivity. Therefore, the amount of Nd in the case of inclusion is set to 0.1% or less. In the case of inclusion, the amount of Nd is preferably 0.08% or less.
  • the amount of Nd when contained is preferably 0.005% or more, and more preferably 0.01% or more.
  • the chemical composition of the welding material for the Ni-base heat-resistant alloy according to the present invention has been described in detail.
  • This welding material has excellent hot cracking resistance during welding.
  • the weld metal which has the high temperature cracking resistance in welding, the stress relaxation cracking resistance in use for a long time at high temperature, and favorable creep strength can be obtained.
  • a welded joint made of a material can be obtained.
  • Ni-base heat-resistant alloy excellent in high-temperature strength as a base material because the base material also has excellent ductility and creep strength in a high-temperature region of 700 ° C. or higher.
  • the Ni-base heat-resistant alloy having excellent high-temperature strength used as the base material may be a Ni-base heat-resistant alloy having the same chemical composition as the Ni-base heat-resistant alloy welding material according to the present invention, or may be different.
  • the base material when a Ni-base heat-resistant alloy having excellent high-temperature strength is used as a base material, the base material includes Mo: 7.0 to 10.0%, Ni: 40 to 50%, and Cr: 20 to 25%. The reason why it is preferable to contain the material will be described in detail.
  • Mo 7.0 to 10.0%
  • Mo is an element that contributes greatly to the improvement of creep strength at a high temperature exceeding 700 ° C. by dissolving in the matrix.
  • the base material is homogenized by heat treatment, and the effect is more easily obtained. For this reason, it is preferable that a base material contains Mo, and the amount should just be 7.0% or more.
  • Mo is an expensive element and causes an increase in cost. Therefore, when Mo is contained, the amount is desirably 10.0% or less.
  • the more desirable lower limit of the Mo content in the base material is 7.5%, and the more desirable upper limit is 9.8%.
  • a more desirable lower limit of the Mo content in the base material is 8.0%, and a more desirable upper limit is 9.5%.
  • Ni 46-56%
  • Ni is an element effective for obtaining an austenite structure, as well as in a weld metal, and is an element effective for ensuring sufficient structural strength during long-time use and obtaining sufficient creep strength.
  • the base material preferably contains Ni, and the amount thereof is preferably 46% or more as in the weld metal.
  • Ni is an expensive element and causes an increase in cost. Therefore, when Ni is contained, the amount is desirably 56% or less.
  • the more desirable lower limit of the Ni content in the base material is 46.5%, and the more desirable upper limit is 55.5%.
  • the more desirable lower limit of the Ni content in the base material is 47%, and the more desirable upper limit is 55%.
  • Cr 20-25% Cr is an effective element for ensuring the oxidation resistance and corrosion resistance of the base metal at high temperatures, as in the case of weld metal.
  • the base material preferably contains Cr, and the amount thereof is preferably 20% or more.
  • the Cr content is excessive, the stability of the structure at high temperatures is deteriorated and the creep strength is lowered. For this reason, when it contains Cr, it is desirable that the amount be 25% or less.
  • a more desirable lower limit of the Cr content in the base material is 20.5%, and a more desirable upper limit is 24.5%.
  • a more desirable lower limit of the Cr content in the base material is 21%, and a more desirable upper limit is 24%.
  • the base material of the Ni-base heat-resistant alloy having excellent high-temperature strength contains the elements described below in addition to Mo, Ni and Cr in the above ranges, with the balance being Fe and impurities.
  • C 0.04 to 0.12% C is an austenite-forming element, as in the weld metal, and is an element effective for enhancing the stability of the austenite structure when used at high temperatures. Unlike a weld metal that is used as it is, the base metal is homogenized by heat treatment, and its effect is more easily obtained, and no measures for preventing weld cracks are required. For this reason, it is preferable that the base material contains C, and the amount may be 0.04% or more. However, if the C content is excessive, coarse carbides are generated during use at high temperatures, which in turn leads to a decrease in creep strength. Therefore, when C is contained, the amount is desirably 0.12% or less. A more desirable lower limit of the C content in the base material is 0.05%, and a more desirable upper limit is 0.10%.
  • Si 1.0% or less Si has a deoxidizing action.
  • the base material does not require measures for preventing weld cracking as described above, the toughness is lowered when the Si content is excessive and exceeds 1.0%. Therefore, when the base material contains Si, the amount is desirably 1.0% or less.
  • the Si content in the base material is more preferably 0.8% or less. However, excessive reduction of the Si content does not provide a sufficient deoxidation effect, lowers the cleanliness of the steel, and increases the manufacturing cost. Therefore, the lower limit of the Si content in the base material is not particularly set, but is desirably 0.01%. If at least 0.01% of Si is contained, a deoxidizing effect can be obtained. A more desirable lower limit of the Si content is 0.02%.
  • Mn 1.5% or less Mn has a deoxidizing action like Si. However, when the Mn content is excessive, embrittlement is caused. For this reason, when the base material contains Mn, the amount is desirably 1.5% or less, and more preferably 1.2% or less.
  • the lower limit of the Mn content in the base material is not particularly set, but is desirably 0.01%. If at least 0.01% of Mn is contained, a deoxidizing effect can be obtained. A more desirable lower limit of the Mn content is 0.02%.
  • P 0.03% or less P is contained as an impurity, and when the content of P is excessive, the creep ductility is reduced. Unlike the case of a weld metal, the base material does not require measures for preventing weld cracking, and the extreme reduction of the P content causes a significant increase in steelmaking costs. For this reason, it is desirable that the P content in the base material be 0.03% or less, and more preferably 0.02% or less.
  • the base material does not require measures for preventing weld cracking, and the extreme reduction of the S content causes a significant increase in steelmaking costs. For this reason, the S content in the base material is preferably 0.01% or less, and more preferably 0.008% or less.
  • Co is an element that is effective for obtaining an austenite structure as in the case of a weld metal, and is an element that ensures the structure stability during long-time use and contributes to the improvement of creep strength. For this reason, it is preferable that the base material contains Co, and the amount may be 10% or more. However, Co is an extremely expensive element, and a large content of Co exceeding 15% causes an increase in cost. Therefore, when it contains Co, it is desirable that the amount be 0.15% or less. A more desirable lower limit of the Co content in the base material is 10.5%, and a more desirable upper limit is 14.5%.
  • Ti 0.1 to 0.5%
  • the base material preferably contains Ti, and the amount thereof is preferably 0.1% or more.
  • the amount is desirably 0.5% or less.
  • a more desirable lower limit of the Ti content in the base material is 0.15%, and a more desirable upper limit is 0.45%.
  • N 0.01% or less N is an element effective for stabilizing the austenite phase, but when the content is large, a large amount of carbonitride precipitates during use, and ductility and toughness Incurs a decline.
  • the content of N may be 0.01% or less in the base material.
  • a more desirable upper limit of the N content in the base material is 0.008%.
  • B 0.005% or less
  • B is an element effective for improving the creep strength by segregating at grain boundaries during use at high temperatures to strengthen the grain boundaries and finely dispersing grain boundary carbides. is there. For this reason, it is preferable that the base material contains B. However, if the B content is excessive, the HAZ liquefaction cracking sensitivity is increased. Therefore, when B is contained, the amount is preferably 0.005% or less. A desirable lower limit of the B content in the base material is 0.0002%.
  • Al 0.8 to 1.8%
  • Al is an element that combines with Ni and precipitates finely as a fine intermetallic compound and contributes to the improvement of creep strength at high temperatures.
  • the material may be actively used to increase the strength.
  • the base material preferably contains Al, and the amount is preferably 0.8% or more.
  • the amount is desirably 1.8% or less.
  • a more desirable lower limit of the Al content in the base material is 0.9%, and a more desirable upper limit is 1.6%.
  • Nd 0.005 to 0.1%
  • Nd has a strong affinity for P, S, and O, and is effective in improving the manufacturability of the base material.
  • Nd is an element effective in reducing the susceptibility to liquefaction cracking of HAZ.
  • the base material preferably contains Nd, and the amount is preferably 0.005% or more.
  • the amount is desirably 0.1% or less.
  • a more desirable lower limit of the Nd content in the base material is 0.01%, and a more desirable upper limit is 0.08%.
  • a plate material having a thickness of 12 mm, a width of 50 mm, and a length of 100 mm is welded from an ingot in which a material having the chemical composition shown in Table 1 is melted and cast in a laboratory by hot forging, hot rolling, heat treatment and machining. It was produced as a material.
  • the outer diameter was 1.2 mm and the length was 1000 mm by hot forging, hot rolling and machining.
  • a welding material welding wire
  • the welded joints were welded for each symbol, and the remaining one was subjected to aging heat treatment at 700 ° C. for 500 hours before being subjected to the next test.
  • Table 3 shows the results of the above tests.
  • “ ⁇ ” in the “Creep rupture test result” column indicates that the welded joint has a “pass” in which the creep rupture time exceeds 1000 hours, which is the target rupture time of the base plate.
  • “x” indicates that the creep rupture time did not reach 1000 hours.
  • the “ ⁇ ” of welding material code 6 indicates that the creep rupture test was not performed because cracks were observed in the weld metal of the sample taken from the welded joint as welded.
  • welded joints welded using the welding materials of reference numerals 4 and 6 whose chemical composition deviates from the range specified in the present invention are stress relaxation cracks during aging heat treatment and hot cracks during welding. Either occurrence was observed.
  • regulated by this invention had low creep strength.
  • a welded joint welded with a welding material having a low C content of 0.03% and outside the range specified in the present invention can produce (Cr, M) 23 C 6 sufficient for the final solidified part. As a result, solidification cracking occurred.
  • the welded joint welded with the welding material of reference numeral 5 whose Mo content is outside the range defined in the present invention did not generate cracks but did not reach 1000 hours and did not satisfy the creep strength. .
  • a welding material for a Ni-base heat resistant alloy having excellent hot cracking resistance during welding, and using it, hot cracking resistance during welding and use at high temperatures for a long time. It is possible to provide a weld metal having moderate stress relaxation cracking resistance and good creep strength. Furthermore, using this welding material, a high temperature cracking resistance during welding, a stress relaxation cracking resistance during long-time use at high temperatures, and a base of a Ni-base heat-resistant alloy excellent in high-temperature strength and a weld metal having good creep strength. A welded joint made of a material can be provided.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Arc Welding In General (AREA)

Abstract

L'invention concerne un matériau de soudage pour un alliage à base de Ni résistant à la chaleur, qui comprend une composition chimique contenant 0,06-0,18 % de C, 0,5 % ou moins de Si, 1,5 % ou moins de Mn, 46-56 % de Ni, 10-15 % de Co, 20-25 % de Cr, plus de 10,0 % mais 14,0 % ou moins de Mo, 0,01-0,5 % de Ti, 0,1-1,0 % de Al et 0,006 % ou moins de N, et en outre, si nécessaire, 0,1 % ou moins de Nd, le reste étant composé de Fe et d'impuretés, tout en maintenant O, P et S contenus comme impuretés à 0,02 % ou moins, 0,008 % ou moins, et 0,005 % ou moins, respectivement. Le matériau de soudage pour un alliage à base de Ni résistant à la chaleur présente une excellente résistance à la fissuration à haute température pendant le soudage. Un métal soudé présentant une résistance à la fissuration à haute température pendant le soudage, une résistance à la fissuration de relaxation des contraintes lors de l'utilisation pendant une longue durée à haute température, et une bonne résistance au fluage peut être fourni grâce au matériau de soudage susmentionné. En outre, un joint soudé peut être fourni au moyen du matériau de soudage susmentionné, ledit joint soudé étant composé d'une base d'un alliage à base de Ni résistant à la chaleur qui présente une excellente résistance à haute température et un métal soudé qui présente une résistance à la fissuration à haute température pendant le soudage, une résistance à la fissuration de relaxation des contraintes lors de l'utilisation pendant une longue durée à haute température, et une bonne résistance au fluage.
PCT/JP2011/063097 2010-06-14 2011-06-08 MATÉRIAU DE SOUDAGE POUR ALLIAGE À BASE DE Ni RÉSISTANT À LA CHALEUR, ET MÉTAL SOUDÉ ET JOINT SOUDÉ AU MOYEN DE CELUI-CI WO2011158706A1 (fr)

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WO2013101561A1 (fr) * 2011-12-30 2013-07-04 Scoperta, Inc. Compositions de revêtement
CN103358050A (zh) * 2012-03-30 2013-10-23 株式会社日立制作所 Ni基合金焊接材料以及使用该材料的焊丝、焊条及焊接用粉末
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US9738959B2 (en) 2012-10-11 2017-08-22 Scoperta, Inc. Non-magnetic metal alloy compositions and applications
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US9802387B2 (en) 2013-11-26 2017-10-31 Scoperta, Inc. Corrosion resistant hardfacing alloy
US10105796B2 (en) 2015-09-04 2018-10-23 Scoperta, Inc. Chromium free and low-chromium wear resistant alloys
US10173290B2 (en) 2014-06-09 2019-01-08 Scoperta, Inc. Crack resistant hardfacing alloys
US10329647B2 (en) 2014-12-16 2019-06-25 Scoperta, Inc. Tough and wear resistant ferrous alloys containing multiple hardphases
US10345252B2 (en) 2013-10-10 2019-07-09 Scoperta, Inc. Methods of selecting material compositions and designing materials having a target property
US10465267B2 (en) 2014-07-24 2019-11-05 Scoperta, Inc. Hardfacing alloys resistant to hot tearing and cracking
US10465269B2 (en) 2014-07-24 2019-11-05 Scoperta, Inc. Impact resistant hardfacing and alloys and methods for making the same
US10851444B2 (en) 2015-09-08 2020-12-01 Oerlikon Metco (Us) Inc. Non-magnetic, strong carbide forming alloys for powder manufacture
US10954588B2 (en) 2015-11-10 2021-03-23 Oerlikon Metco (Us) Inc. Oxidation controlled twin wire arc spray materials
US11279996B2 (en) 2016-03-22 2022-03-22 Oerlikon Metco (Us) Inc. Fully readable thermal spray coating
US11939646B2 (en) 2018-10-26 2024-03-26 Oerlikon Metco (Us) Inc. Corrosion and wear resistant nickel based alloys

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JP6519007B2 (ja) * 2015-04-03 2019-05-29 日本製鉄株式会社 Ｎｉ基耐熱合金溶接継手の製造方法
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JP2017042796A (ja) * 2015-08-27 2017-03-02 株式会社神戸製鋼所 Ｎｉ基合金溶接金属
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CN112809242B (zh) * 2020-12-31 2022-05-13 钢铁研究总院 固溶强化型耐热合金c-hra-2焊接用焊条
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US8973806B2 (en) 2011-03-23 2015-03-10 Scoperta, Inc. Fine grained Ni-based alloys for resistance to stress corrosion cracking and methods for their design
US10100388B2 (en) 2011-12-30 2018-10-16 Scoperta, Inc. Coating compositions
US20140248509A1 (en) * 2011-12-30 2014-09-04 Scoperta, Inc. Coating compositions
CN104039483A (zh) * 2011-12-30 2014-09-10 思高博塔公司 涂层组合物
US11085102B2 (en) 2011-12-30 2021-08-10 Oerlikon Metco (Us) Inc. Coating compositions
WO2013101561A1 (fr) * 2011-12-30 2013-07-04 Scoperta, Inc. Compositions de revêtement
CN103358050A (zh) * 2012-03-30 2013-10-23 株式会社日立制作所 Ni基合金焊接材料以及使用该材料的焊丝、焊条及焊接用粉末
US9738959B2 (en) 2012-10-11 2017-08-22 Scoperta, Inc. Non-magnetic metal alloy compositions and applications
US10345252B2 (en) 2013-10-10 2019-07-09 Scoperta, Inc. Methods of selecting material compositions and designing materials having a target property
US11175250B2 (en) 2013-10-10 2021-11-16 Oerlikon Metco (Us) Inc. Methods of selecting material compositions and designing materials having a target property
US10495590B2 (en) 2013-10-10 2019-12-03 Scoperta, Inc. Methods of selecting material compositions and designing materials having a target property
US9802387B2 (en) 2013-11-26 2017-10-31 Scoperta, Inc. Corrosion resistant hardfacing alloy
EP3100818A4 (fr) * 2014-01-27 2017-10-11 Nippon Steel & Sumitomo Metal Corporation Matériau de soudage pour alliage résistant à la chaleur à base de ni, métal soudé à l'aide de ce matériau, et raccord soudé
US10173290B2 (en) 2014-06-09 2019-01-08 Scoperta, Inc. Crack resistant hardfacing alloys
US11130205B2 (en) 2014-06-09 2021-09-28 Oerlikon Metco (Us) Inc. Crack resistant hardfacing alloys
US11111912B2 (en) 2014-06-09 2021-09-07 Oerlikon Metco (Us) Inc. Crack resistant hardfacing alloys
US10465267B2 (en) 2014-07-24 2019-11-05 Scoperta, Inc. Hardfacing alloys resistant to hot tearing and cracking
US10465269B2 (en) 2014-07-24 2019-11-05 Scoperta, Inc. Impact resistant hardfacing and alloys and methods for making the same
US10329647B2 (en) 2014-12-16 2019-06-25 Scoperta, Inc. Tough and wear resistant ferrous alloys containing multiple hardphases
US10105796B2 (en) 2015-09-04 2018-10-23 Scoperta, Inc. Chromium free and low-chromium wear resistant alloys
US11253957B2 (en) 2015-09-04 2022-02-22 Oerlikon Metco (Us) Inc. Chromium free and low-chromium wear resistant alloys
US10851444B2 (en) 2015-09-08 2020-12-01 Oerlikon Metco (Us) Inc. Non-magnetic, strong carbide forming alloys for powder manufacture
US10954588B2 (en) 2015-11-10 2021-03-23 Oerlikon Metco (Us) Inc. Oxidation controlled twin wire arc spray materials
US11279996B2 (en) 2016-03-22 2022-03-22 Oerlikon Metco (Us) Inc. Fully readable thermal spray coating
US11939646B2 (en) 2018-10-26 2024-03-26 Oerlikon Metco (Us) Inc. Corrosion and wear resistant nickel based alloys

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