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WO2011071054A1 - Alliage austénitique résistant à la chaleur - Google Patents

Alliage austénitique résistant à la chaleur Download PDF

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Publication number
WO2011071054A1
WO2011071054A1 PCT/JP2010/071954 JP2010071954W WO2011071054A1 WO 2011071054 A1 WO2011071054 A1 WO 2011071054A1 JP 2010071954 W JP2010071954 W JP 2010071954W WO 2011071054 A1 WO2011071054 A1 WO 2011071054A1
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content
haz
toughness
austenitic heat
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PCT/JP2010/071954
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English (en)
Japanese (ja)
Inventor
平田　弘征
岡田　浩一
仙波　潤之
小川　和博
伊勢田　敦朗
吉澤　満
Original Assignee
住友金属工業株式会社
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Application filed by 住友金属工業株式会社 filed Critical 住友金属工業株式会社
Priority to DK10835974.6T priority Critical patent/DK2511389T3/en
Priority to CA2780655A priority patent/CA2780655C/fr
Priority to KR1020157009606A priority patent/KR101740164B1/ko
Priority to EP10835974.6A priority patent/EP2511389B1/fr
Priority to CN201080055959.5A priority patent/CN102686757B/zh
Priority to ES10835974.6T priority patent/ES2533429T3/es
Priority to KR1020147033861A priority patent/KR20150004918A/ko
Priority to JP2010548304A priority patent/JP4697357B1/ja
Publication of WO2011071054A1 publication Critical patent/WO2011071054A1/fr
Priority to US13/472,640 priority patent/US8808473B2/en

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    • 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
    • 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
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • 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 an austenitic heat resistant alloy. Specifically, the present invention relates to an austenitic heat-resistant alloy that is excellent in both weld crack resistance used in high-temperature equipment such as power generation boilers and chemical industrial plants, and HAZ toughness after long-term use, and also excellent in creep strength at high temperatures. .
  • the high temperature and high pressure of steam increases the temperature at the time of actual operation of high-temperature equipment consisting of a boiler superheater tube, a reaction furnace tube for the chemical industry, and a thick plate and a forged product as a heat and pressure resistant member to 700 ° C. or more. . Therefore, a material used for a long time in such a harsh environment is required to have not only high-temperature strength and high-temperature corrosion resistance, but also good long-term metal structure stability and creep characteristics.
  • Patent Documents 1 to 3 disclose heat-resistant alloys that increase the content of Cr and Ni and further improve the creep rupture strength as a high-temperature strength by containing one or more of Mo and W. Yes.
  • Patent Documents 4 to 7 describe mass%, Cr is 28 to 38%, and Ni is 35 to 60. And a heat-resistant alloy that further improves the creep rupture strength by utilizing precipitation of an ⁇ -Cr phase having a body-centered cubic structure mainly composed of Cr.
  • Patent Documents 8 to 11 include Mo and / or W to enhance the solid solution, and Al and Ti are included in the ⁇ ′ phase that is an intermetallic compound, specifically, Ni 3 ( A Ni-based alloy that is used in the severe environment described above by utilizing precipitation strengthening of Al, Ti) is disclosed.
  • Patent Document 12 proposes a high Ni austenitic heat-resistant alloy in which the creep strength is improved by adjusting the addition range of Al and Ti and precipitating the ⁇ 'phase.
  • Patent Documents 13 to 16 disclose Ni-based alloys containing Co in addition to Cr and Mo for the purpose of further strengthening.
  • Patent Documents 1 to 14 disclose austenitic heat-resistant alloys with improved creep rupture strength, but have not been studied from the viewpoint of “weldability” when assembled as a structural member.
  • Austenitic heat-resistant alloys are generally assembled into various structures by welding and used at high temperatures. However, when the amount of alloying elements increases, the heat affected zone (hereinafter referred to as “HAZ”), particularly among the welded heat-affected zones during welding work. Regarding the problem that cracking occurs in the HAZ adjacent to the melting boundary, for example, in Non-Patent Document 1 (Welding Society: Welding and Joining Handbook 2nd Edition (2003, Maruzen) pp. 948-950) It has been reported.
  • austenitic heat-resistant alloys contain a variety of alloy elements as the strength increases, and in recent high-efficiency boilers, these austenitic heat-resistant alloys are mainly used. It has been studied to use it in mechanically severe places such as thick-walled members typified by steam pipes and complicated-shaped members typified by water wall pipes, and cracks occurring in HAZ tend to become more obvious. .
  • HAZ is required to have sufficient low-temperature toughness when stopped.
  • the toughness of HAZ also decreases with an increase in the amount of alloying elements.
  • the toughness of HAZ significantly decreases after use for a long time in a material to which Al, Ti and Nb are added.
  • Patent Document 15 mentions the cracking of the HAZ, as described above, there is still anxiety in application to a mechanically severe part. Furthermore, although the toughness of the weld metal is described, the toughness of the HAZ is not considered. For this reason, a problem remains in the HAZ performance particularly when applied to a thick member such as a main steam pipe.
  • Patent Document 16 Although mention is made of reheat cracking occurring in the weld metal and toughness of the weld metal, nothing is mentioned about the performance of the HAZ.
  • the present invention has been made in view of the above situation, and is an austenitic heat-resistant alloy that is excellent in both weld crack resistance and toughness of HAZ used in equipment used at high temperatures, and also excellent in creep strength at high temperatures.
  • the purpose is to provide.
  • excellent in weld crack resistance specifically refers to excellent resistance to liquefaction cracking of HAZ.
  • HAZ cracks were observed on the fracture surface of the HAZ cracks, and P and B concentration, particularly B concentration, was observed on the fracture surface.
  • HAZ liquefaction crack the HAZ crack generated during welding is sometimes referred to as “HAZ liquefaction crack”.
  • the present inventors also conducted a detailed investigation on the toughness of the HAZ part after prolonged aging. As a result, the following items [4] to [7] were confirmed.
  • the present inventors estimated that the above phenomenon is caused by the following mechanism.
  • the present inventors estimated the reason why the degree of influence of P and B on the liquefaction cracking and toughness of HAZ is affected by the amount of Cr contained in the alloy as follows.
  • both P and B are elements that are easily segregated at the grain boundary.
  • the Cr content is large, a large amount of Cr having a strong affinity with P exists in the grain. Grain boundary segregation of P during welding heat cycle and subsequent use at high temperatures is suppressed.
  • B is segregated at the segregation site where the void is generated, and the influence of B on liquefaction cracking is stronger as the HAZ of the material having a higher Cr content, and the decrease in toughness after long-time heating is reduced.
  • the present inventors contain a proper amount of one or more elements of Al, Ti, and Nb, and finely precipitate intermetallic compounds bonded to Ni in a grain, thereby improving the temperature at a high temperature. It was found that creep strength and toughness after long-time heating can be secured.
  • the parameter F1 represented by the following formula (1) is set to 1 or more and 12 or less, and the following (2)
  • the parameter F2 represented by the formula is set to 0.035 or less, the creep strength and creep ductility at high temperatures can be secured, and the HAZ liquefaction cracking during welding caused by P and B grain boundary segregation It was found that both the occurrence and the decrease in toughness after long-term use can be reduced.
  • F1 4 ⁇ Al + 2 ⁇ Ti + Nb (1)
  • F2 P + 0.2 ⁇ Cr ⁇ B (2).
  • the present invention has been completed based on the above findings, and the gist thereof is an austenitic heat resistant alloy shown in the following (1) and (2).
  • the “impurities” in the remaining “Fe and impurities” are those which are mixed due to various factors in the manufacturing process, including raw materials such as ore or scrap, when industrially manufacturing heat-resistant alloys. Point to.
  • the austenitic heat-resistant alloy of the present invention is excellent in both weld crack resistance and toughness of HAZ, and is also excellent in creep strength at high temperatures. For this reason, the austenitic heat-resistant alloy of this invention can be used suitably as a raw material of high temperature apparatuses, such as a boiler for electric power generation and a chemical industrial plant.
  • % display of the content of each element means “mass%”.
  • C 0.15% or less C stabilizes the austenite structure, forms fine carbides at grain boundaries, and improves creep strength at high temperatures. However, when the content becomes excessive, the carbide becomes coarse and precipitates in a large amount, thereby lowering the ductility of the grain boundary, leading to a decrease in toughness and creep strength. Therefore, the C content is 0.15% or less. A more preferable upper limit of the C content is 0.12%.
  • the desirable lower limit of the C content is 0.01%.
  • Si 2% or less Si is an element which is added as a deoxidizing agent and is effective in improving corrosion resistance and oxidation resistance at high temperatures.
  • the Si content is 2% or less.
  • the Si content is desirably 1.5% or less, and more desirably 1.0% or less.
  • the desirable lower limit of the Si content is 0.02%.
  • Mn 3% or less Mn is added as a deoxidizer in the same manner as Si and is an element that contributes to stabilization of austenite.
  • the Mn content is 3% or less.
  • the Mn content is desirably 2.5% or less, and more desirably 2.0% or less.
  • the desirable lower limit of the Mn content is 0.02%.
  • Ni 40-60%
  • Ni is an effective element for obtaining an austenite structure, and is an essential element for ensuring the structural stability after long-term use. Further, Ni combines with Al, Ti, and Nb to form a fine intermetallic compound phase, and also has an effect of increasing creep strength. In order to sufficiently obtain the above Ni effect within the Cr content range of 15% or more and less than 28% of the present invention, a Ni content of 40% or more is necessary. However, since Ni is an expensive element, a large content exceeding 60% causes an increase in cost. Therefore, the Ni content is 40 to 60%. The desirable lower limit of the Ni content is 42%, and the desirable upper limit is 58%.
  • Co 0.03-25%
  • Co is an austenite-forming element and contributes to the improvement of creep strength by increasing the stability of the austenite phase.
  • the Co content needs to be 0.03% or more.
  • a desirable lower limit of the Co content is 0.1%, and a more desirable lower limit is 8%.
  • the desirable upper limit of the Co content is 23%.
  • Cr 15% or more and less than 28% Cr is an essential element for securing oxidation resistance and corrosion resistance at high temperatures.
  • a Cr content of 15% or more is necessary.
  • the Cr content is 15% or more and less than 28%.
  • a desirable lower limit of the Cr content is 17%, and a desirable upper limit is 26%.
  • Cr is an element that affects the grain boundary segregation behavior of P and B in the HAZ during welding, and indirectly affects the HAZ liquefaction cracking sensitivity increase and the HAZ toughness deterioration after long-term use. Therefore, as will be described later, the parameter F2 represented by the equation (2) composed of P, B, and Cr needs to be 0.035 or less.
  • Both W and Mo are elements that contribute to the improvement of the creep strength at high temperatures by dissolving in the austenite structure as a matrix. In order to acquire this effect, it is necessary to contain one or both in total 0.1% or more. However, when the total content of Mo and W becomes excessive, especially exceeding 12%, the stability of the austenite phase is lowered, and the creep strength is lowered. Since W has a larger atomic weight than Mo, it needs to be contained in a larger amount in order to obtain the same effect as Mo, which is disadvantageous from the viewpoint of ensuring cost and phase stability. For this reason, the W amount in the case of containing is made less than 4%.
  • the content of Mo and W is set to 0.1 to 12% in total for one or both of Mo: 12% or less and W: less than 4%.
  • a desirable lower limit of the total content of W and Mo is 1%, and a desirable upper limit is 10%.
  • W and Mo do not need to be combined.
  • the content may be 0.1 to 12%.
  • W when W is contained alone, the content is 0.1% or more and less than 4%. I just need it.
  • the desirable upper limit of Mo is 10%.
  • Nd 0.001 to 0.1%
  • Nd is an important element that characterizes the present invention. That is, Nd is an element essential for fixing P and removing the adverse effects of P on HAZ liquefaction cracking and toughness by forming a compound with P that has a strong affinity with P, a high melting point, and is stable up to high temperatures. It is. Moreover, it is an element which precipitates as a carbide
  • the Nd content is set to 0.001 to 0.1%.
  • a desirable lower limit of the Nd content is 0.005%, and a desirable upper limit is 0.08%.
  • B 0.0005 to 0.006%
  • B is an element necessary for improving the creep strength by segregating at the grain boundary in use to strengthen the grain boundary and finely dispersing the grain boundary carbide. In addition, it has the effect of segregating at the grain boundaries to improve the fixing force and contribute to toughness improvement. In order to obtain these effects, a B content of 0.0005% or more is necessary. However, if the B content increases and exceeds 0.006%, a large amount of segregation occurs in the high-temperature HAZ near the melting boundary due to the welding heat cycle during welding, and the melting point of the grain boundary is lowered by overlapping with P. To increase the susceptibility of HAZ to liquefaction cracking. Therefore, the B content is set to 0.0005 to 0.006%.
  • the parameter F2 represented by the equation (2) composed of P, B, and Cr needs to be 0.035 or less.
  • N 0.03% or less N is an element effective for stabilizing the austenite phase.
  • the Cr content range of 15% to less than 28% of the present invention, if it is excessively contained, During use, a large amount of fine nitride precipitates in the grains, resulting in a decrease in creep ductility and toughness. Therefore, the N content is 0.03% or less.
  • the N content is desirably 0.02% or less.
  • the desirable lower limit of the N content is 0.0005%.
  • O 0.03% or less O is contained in the alloy as one of the impurity elements. However, if excessively contained, the hot workability is deteriorated and the toughness and ductility are deteriorated. It is necessary to make it 03% or less.
  • the content of O is desirably 0.02% or less.
  • the desirable lower limit of the O content is 0.001%.
  • Al, Ti, Nb Al: 3% or less, Ti: 3% or less, and Nb: 1% or more of Nb: 3% or less Al, Ti, and Nb all combine with Ni to form fine intermetallic compounds It is an element essential for precipitating and ensuring creep strength at high temperatures. However, when the content is too large and exceeds 3% for any element, the above effects are saturated, and creep ductility and toughness after prolonged heating are lowered. Therefore, the content of each of Al, Ti, and Nb is 3% or less, and one or more of these elements are contained. Each content is preferably 2.8% or less, and more preferably 2.5% or less.
  • the parameter F1 represented by the formula (1) consisting of Al, Ti and Nb is 1 as will be described later. It must be 12 or less.
  • P 0.03% or less
  • P is an element contained in the alloy as an impurity, but segregates at the grain boundaries of HAZ during welding to increase liquefaction cracking sensitivity and adversely affect toughness after long-term use. is there. Therefore, although it is preferable to reduce as much as possible, extreme reduction leads to an increase in steelmaking cost. Therefore, the P content is 0.03% or less. Desirably, it is 0.02% or less.
  • S 0.01% or less S is an element contained in the alloy as an impurity, but segregates at the grain boundaries of HAZ during welding to increase liquefaction cracking sensitivity and adversely affect toughness after long-term use. is there. Therefore, although it is preferable to reduce as much as possible, extreme reduction leads to an increase in steelmaking cost. Therefore, the S content is 0.01% or less. Desirably, it is 0.005% or less.
  • F1 1 or more and 12 or less
  • F1 represented by the above formula (1) that is, [4 ⁇ Al + 2 ⁇ Ti + Nb ] Is 1 or more and 12 or less
  • a desirable lower limit of F1 is 3, and a desirable upper limit is 11.
  • P and B are elements that segregate at the HAZ grain boundary near the melting boundary during the welding process due to the thermal cycle, lower the melting point, and increase the HAZ liquefaction cracking susceptibility. .
  • P segregated at the grain boundaries decreases the fixing force of the grain boundaries, whereas B conversely strengthens the grain boundaries, so P adversely affects toughness and B is reversed.
  • Cr is an element that affects the grain boundary segregation behavior of P and B, and indirectly affects their performance.
  • the above-mentioned amount of Nd is contained as an essential element, and the above ( 2) F2 represented by the formula, that is, [P + 0.2 ⁇ Cr ⁇ B] needs to be 0.035 or less.
  • a desirable upper limit of F2 is 0.030.
  • the lower limit of F2 may be a value close to 0.0015 when the content of P as an impurity is extremely low and Cr is 15% and B is 0.0005%.
  • One of the austenitic heat-resistant alloys of the present invention contains elements from C to O in the above-mentioned range, and contains at least one of Al, Ti, and Nb in the above-mentioned range, with the balance being Fe and impurities.
  • the austenitic heat-resistant alloy of the present invention instead of part of its Fe, if necessary, First group: Ca: 0.02% or less, Mg: 0.02% or less, La: 0.1% or less, and Ce: 0.1% or less Second group: Ta: 0.1% or less, Hf: 0 One or more elements belonging to each group of .1% or less and Zr: 0.1% or less can be selectively contained.
  • one or more elements belonging to the group of the first group and / or the second group may be added and contained as an optional element.
  • Group 1 Ca: 0.02% or less, Mg: 0.02% or less, La: 0.1% or less, and Ce: 0.1% or less
  • the elements of the first group, Ca, Mg, La and Ce, are , Has the effect of increasing hot workability. Furthermore, these elements have the effect
  • the elements of the first group will be described in detail.
  • Ca 0.02% or less Ca has a strong affinity for S and has an effect of improving hot workability. Moreover, there exists an effect which reduces both generation
  • excessive addition of Ca leads to a decrease in cleanliness due to bonding with oxygen. In particular, when the content exceeds 0.02%, the decrease in cleanliness becomes significant, and the hot workability is deteriorated. . Therefore, the Ca content when contained is 0.02% or less.
  • the amount of Ca is desirably 0.01% or less.
  • the lower limit of the Ca content when contained is preferably 0.0001%, and more preferably 0.0005%.
  • Mg 0.02% or less Mg also has a strong affinity with S and has an effect of improving hot workability, and also an effect of reducing both the occurrence of liquefaction cracking of HAZ and a decrease in toughness due to S Have
  • excessive addition of Mg leads to a decrease in cleanliness due to bonding with oxygen.
  • the content exceeds 0.02%, the cleanliness decreases significantly, and the hot workability is deteriorated. . Therefore, the amount of Mg when contained is 0.02% or less.
  • the amount of Mg is desirably 0.01% or less.
  • the lower limit of the Mg content in the case of inclusion is preferably 0.0001%, and more preferably 0.0005%.
  • La 0.1% or less
  • La has a strong affinity for S, has an effect of improving hot workability, and also reduces the occurrence of liquefaction cracking of HAZ and a decrease in toughness due to S.
  • excessive addition of La leads to a decrease in cleanliness due to bonding with oxygen.
  • the content exceeds 0.1%, the cleanliness decreases remarkably, and the hot workability is deteriorated. . Therefore, the amount of La when contained is 0.1% or less.
  • the lower limit of the La amount when contained is preferably 0.001%, and more preferably 0.005%.
  • Ce 0.1% or less Ce also has a strong affinity with S and has an effect of improving hot workability. Moreover, there exists an effect which reduces both generation
  • excessive addition of Ce leads to a decrease in cleanliness due to bonding with oxygen. In particular, when the content exceeds 0.1%, the cleanliness decreases remarkably, and the hot workability is deteriorated. . Therefore, the amount of Ce when contained is 0.1% or less. In addition, it is desirable that the amount of Ce when contained is 0.08% or less.
  • the lower limit of the Ce content when contained is preferably 0.001%, and more preferably 0.005%.
  • said Ca, Mg, La, and Ce can be contained only in any 1 type in them, or 2 or more types of composites.
  • the total amount of these elements when contained may be 0.24%, but is preferably 0.15% or less.
  • Second group Ta: 0.1% or less, Hf: 0.1% or less, and Zr: 0.1% or less Ta, Hf and Zr, which are elements of the second group, have an effect of increasing the high-temperature strength. In order to obtain this effect, the above elements may be added and contained. Hereinafter, the second group of elements will be described in detail.
  • Ta 0.1% or less Ta has a function of improving the strength at high temperature by being dissolved in a matrix or precipitated as a carbide. However, if the Ta content increases and exceeds 0.1%, a large amount of carbide precipitates, resulting in a decrease in toughness. Therefore, when Ta is included, the amount of Ta is set to 0.1% or less. When Ta is included, the amount of Ta is desirably 0.08% or less.
  • the lower limit of the Ta content when contained is preferably 0.002%, and more preferably 0.005%.
  • Hf 0.1% or less Hf also has the effect of improving the strength at high temperatures by solid solution or precipitation as carbides in the matrix. However, if the Hf content increases and exceeds 0.1%, a large amount of carbide precipitates, resulting in a decrease in toughness. Therefore, the amount of Hf when contained is 0.1% or less. In addition, when it contains, it is desirable that the quantity of Hf shall be 0.08% or less.
  • the lower limit of the amount of Hf when contained is preferably 0.002%, and more preferably 0.005%.
  • Zr 0.1% or less Zr precipitates as a carbide and has an action of improving strength at high temperatures. However, when the Zr content increases and exceeds 0.1%, a large amount of carbide precipitates, leading to a decrease in toughness and an increase in liquefaction cracking sensitivity during welding. Therefore, the amount of Zr when contained is 0.1% or less. When Zr is included, the amount of Zr is preferably 0.08% or less.
  • the lower limit of the Zr content when contained is preferably 0.002%, and more preferably 0.005%.
  • said Ta, Hf, and Zr can be contained only in any 1 type in them, or 2 or more types of composites.
  • the total amount of these elements when contained may be 0.3%, but is preferably 0.15% or less.
  • Austenitic alloys A1 to A11 and B1 to B8 having the chemical composition shown in Table 1 were melted, and a plate material having a thickness of 20 mm, a width of 50 mm, and a length of 100 mm was obtained by hot forging, hot rolling, heat treatment and machining. Produced.
  • Alloys A1 to A11 in Table 1 are alloys whose chemical compositions are within the range defined by the present invention.
  • the alloys B1 to B8 are alloys whose chemical compositions deviate from the conditions defined in the present invention.
  • a groove having the shape shown in FIG. 1 is processed in the longitudinal direction of each of the plate materials having a thickness of 20 mm, a width of 50 mm, and a length of 100 mm, and heat input using a welding wire (AWS standard A5.14 ERNiCrCoMo-1).
  • AWS standard A5.14 ERNiCrCoMo-1 After performing the first layer welding by TIG welding at 9 kJ / cm, on a SM400C steel plate (JIS standard G 3106 (2008)) having a thickness of 25 mm, a width of 200 mm, and a length of 200 mm, a coated arc welding rod (JIS standard Z 3224 ( 2007) Four rounds were restrained and welded using DNiCrFe-3).
  • a cross-sectional sample was taken from each welded joint as-welded, and the cross-section was mirror-polished and corroded, and then examined with an optical microscope to examine the presence or absence of HAZ liquefaction cracks.
  • Table 2 summarizes the above test results.
  • “ ⁇ ” in the “HAZ liquefaction cracking” column indicates that no cracks were observed, while “x” indicates that cracks were observed.
  • “ ⁇ ” in the “Creep Rupture Test” column indicates that the creep rupture time under the above conditions is “pass” exceeding 1000 hours, which is the target fracture time of the base material, and “ ⁇ ” indicates creep Indicates that the break time did not reach 1000 hours.
  • “ ⁇ ” in the “Toughness” column indicates that the decrease in absorbed energy does not exceed 50 J when aging heat treatment is performed, and “ ⁇ ” indicates that the decrease in absorbed energy exceeds 50 J. It shows that.
  • Test symbol 12 using the alloy B1 containing no Nd was not effective in removing the adverse effect of P on the liquefaction cracking and toughness of HAZ, so that HAZ liquefaction cracking occurred and the toughness decreased after prolonged heating did.
  • Test symbol 13 shows that although alloy B2 used contains Nd, F2 defined by P, B and Cr exceeds 0.035, so that HAZ liquefaction cracks occur and toughness decreases after heating for a long time. It was.
  • Test symbol 14 indicates that the alloy B3 used does not contain Nd, and F2 defined by P, B and Cr exceeds 0.035, so that HAZ liquefaction cracks occur and after heating for a long time. The toughness reduction was significant.
  • Test symbol 15 shows that the alloy B4 used contains Nd, and F2 defined by P, B, and Cr satisfies the conditions defined in the present invention, and therefore no HAZ liquefaction cracking occurred. However, since the alloy B4 does not contain B, a sufficient creep strength cannot be obtained.
  • Test symbol 16 shows that the alloy B5 used contained Nd, P, B, and Cr, and F2 satisfied the conditions defined in the present invention, so that HAZ liquefaction cracking did not occur.
  • Alloy B5 F1 defined by Al, Ti, and Nb exceeds 12, and thus the toughness after heating for a long time is remarkable.
  • Test symbols 17 and 18 show that the alloys B6 and B7 used contain La or / and Ce collectively called REM, but do not contain Nd, so that P has an adverse effect on liquefaction cracking and toughness of HAZ. The removal effect was not obtained, and HAZ liquefaction cracks occurred, and the toughness decreased after heating for a long time.
  • Test symbol 19 shows that the alloy B8 used contained Nd, P, B, and Cr, and F2 satisfied the conditions defined in the present invention, so that HAZ liquefaction cracking did not occur. However, in Alloy B8, F1 defined by Al, Ti, and Nb was less than 1, so that sufficient creep strength was not obtained.
  • the austenitic heat-resistant alloy of the present invention is excellent in both HAZ weld crack resistance and toughness, and is also excellent in creep strength at high temperatures. For this reason, the austenitic heat-resistant alloy of this invention can be used suitably as a raw material of high temperature apparatuses, such as a boiler for electric power generation and a chemical industrial plant.

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Abstract

La présente invention concerne un alliage austénitique résistant à la chaleur, contenant 0,15 % ou moins de C, 2 % ou moins de Si, 3 % ou moins de Mn, de 40 à 60 % de Ni, de 0,03 à 25 % de Co, 15 % ou plus mais moins de 28 % de Cr, 12 % ou moins de Mo et/ou moins de 4 % de W, le total étant égal à une valeur entre 0,1 et 12 %, de 0,001 à 0,1 % de Nd, de 0,0005 à 0,006 % de B, 0,03 % ou moins de N, 0,03 % ou moins d'O, et un ou plusieurs choisis parmi 3 % ou moins d'Al, 3 % ou moins de Ti et 3 % ou moins de Nb, le reste étant composé de Fe et d'impuretés comprenant 0,03 % ou moins de P et 0,01 % ou moins de S, et satisfaisant à 1 ≤ 4 × Al + 2 × Ti + Nb ≤ 12 et P + 0,2 × Cr × B < 0,035. L'alliage austénitique résistant à la chaleur présente à la fois une excellente résistance à l'attaque par la soudure et une excellente résistance dans la zone thermiquement affectée, tout en présentant une excellente résistance au fluage à des températures élevées. Par conséquent, l'alliage austénitique résistant à la chaleur est approprié pour une utilisation comme matériau destiné à des dispositifs pour température élevée tels qu'une chaudière destinée à générer de l'énergie et une installation industrielle chimique. L'alliage austénitique résistant à la chaleur peut contenir un ou plusieurs éléments choisis parmi les Ca, Mg, La, Ce, Ta, Hf et Zr en une quantité spécifique.
PCT/JP2010/071954 2009-12-10 2010-12-08 Alliage austénitique résistant à la chaleur WO2011071054A1 (fr)

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DK10835974.6T DK2511389T3 (en) 2009-12-10 2010-12-08 Austenitic heat resistant alloy
CA2780655A CA2780655C (fr) 2009-12-10 2010-12-08 Alliage austenitique resistant a la chaleur
KR1020157009606A KR101740164B1 (ko) 2009-12-10 2010-12-08 오스테나이트계 내열 합금
EP10835974.6A EP2511389B1 (fr) 2009-12-10 2010-12-08 Alliage austénitique résistant à la chaleur
CN201080055959.5A CN102686757B (zh) 2009-12-10 2010-12-08 奥氏体系耐热合金
ES10835974.6T ES2533429T3 (es) 2009-12-10 2010-12-08 Aleaciones austeníticas resistentes al calor
KR1020147033861A KR20150004918A (ko) 2009-12-10 2010-12-08 오스테나이트계 내열 합금
JP2010548304A JP4697357B1 (ja) 2009-12-10 2010-12-08 オーステナイト系耐熱合金
US13/472,640 US8808473B2 (en) 2009-12-10 2012-05-16 Austenitic heat resistant alloy

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US8808473B2 (en) 2014-08-19
DK2511389T3 (en) 2015-02-23
KR20150004918A (ko) 2015-01-13
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US20120288400A1 (en) 2012-11-15
CN102686757A (zh) 2012-09-19
EP2511389A1 (fr) 2012-10-17
JP4697357B1 (ja) 2011-06-08
EP2511389B1 (fr) 2015-02-11
JPWO2011071054A1 (ja) 2013-04-22
CA2780655C (fr) 2014-04-01
KR20120073356A (ko) 2012-07-04
KR101740164B1 (ko) 2017-06-08
EP2511389A4 (fr) 2013-08-28

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