EP0109350A2 - Alliage nickel-chrome - Google Patents

Alliage nickel-chrome Download PDF

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Publication number
EP0109350A2
EP0109350A2 EP83730106A EP83730106A EP0109350A2 EP 0109350 A2 EP0109350 A2 EP 0109350A2 EP 83730106 A EP83730106 A EP 83730106A EP 83730106 A EP83730106 A EP 83730106A EP 0109350 A2 EP0109350 A2 EP 0109350A2
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Prior art keywords
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alloy
temperature
nickel
resistance
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EP83730106A
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German (de)
English (en)
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EP0109350A3 (en
EP0109350B1 (fr
Inventor
Toshio Takasago Technical Institute Yonezawa
Nobuya Takasago Technical Institute Sasaguri
Kichiro Takasago Technical Institute Onimura
Hiroshi Takasago Technical Institute Susukida
Katsuji Takasago Technical Institute Kawaguchi
Takaya C/O Kobe Shipyard & Engine Works Kusakabe
Hiroo Nagano
Takao Minami
Kazuo Yamanaka
Yasutaka Okada
Mamoru Inoue
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Mitsubishi Heavy Industries Ltd
Nippon Steel Corp
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Mitsubishi Heavy Industries Ltd
Sumitomo Metal Industries Ltd
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Priority claimed from JP57197362A external-priority patent/JPS5985850A/ja
Priority claimed from JP10409583A external-priority patent/JPS59232246A/ja
Priority claimed from JP10409483A external-priority patent/JPS59229457A/ja
Priority claimed from JP58156427A external-priority patent/JPS6050134A/ja
Application filed by Mitsubishi Heavy Industries Ltd, Sumitomo Metal Industries Ltd filed Critical Mitsubishi Heavy Industries Ltd
Publication of EP0109350A2 publication Critical patent/EP0109350A2/fr
Publication of EP0109350A3 publication Critical patent/EP0109350A3/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
    • 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 non-deposition hardening type nickel based alloy which will be subjected to a high-temperature and high-pressure water or vapor and which has a remarkably improved crystal boundary etching resistance, mechanical properties and pitting corrosion resistance, in addition to the maintenance of a stress corrosion cracking resistance, and further has a bettered stress corrosion resistance in an aqueous NaOH solution.
  • the present invention relates to a nickel-chromium alloy excellent in a stress corrosion cracking resistance, more specifically, to a nickel-chromium alloy in which the stress corrosion cracking resistance is noticeably improved by depositing an insolubilized carbide in grains thereof and by strengthening a coating on the surface thereof.
  • the present invention also relates to an alloy for a heat transfer pipe, particularly to an alloy for a heat transfer pipe on the secondary side of a nuclear reactor.
  • nickel based alloys such as INCOROI 800 (trade name), and INCONEL 600 (trade name) and INCONEL 690 (trade name) set forth in Table 1 below.
  • these alloys have further been treated by heating them at a rather lower temperature than a level (hereinafter referred to as T°C), at which a carbide is thoroughly solubilized, alternatively by further additionally specifically heating and retaining them at a temperature of 650 to 750°C, in order to improve the crystal boundary etching resistance and stress corrosion cracking resistance.
  • T°C a level at which a carbide is thoroughly solubilized
  • the nickel based alloys which have undergone such a conventional thermal treatment are still poor in the pitting corrosion resistance and stress corrosion cracking resistance.
  • an object of the present invention is to provide a method for a thermal treatment of a nickel based alloy without such drawbacks above, i.e. a method for a thermal treatment of a nickel based alloy by which its mechanical properties, pitting corrosion resistance, stress corrosion cracking resistance and crystal boundary etching resistance can be improved.
  • the summary of the present invention is directed to a nickel based alloy, characterized in that said nickel based alloy for a material which will be subjected to a high-temperature and high-pressure water or vapor comprises, in terms of % by weight, 58% or more of Ni, 25 to 35% of Cr, 0.003% or less of B, 0.012 to 0.035% of C, 1% or less of Mn, 0.5% or less of Si, 0.015% or less of P, 0.015% or less of S, and the residue of Fe and usual impurities; in a first thermal treatment process, said nickel based alloy is heated and retained at a temperature of T°C to (T + 100)°C and is cooled at a greater cooling rate than a furnace cooling rate; and in a second thermal treatment process, said nickel based alloy is then retained at a temperature of 600 to 750°C and a temperature within a sensitization recovery range for a period of 0.1 to 100 hours and is cooled at a greater cooling rate than
  • an object of the present invention is to provide an alloy which can overcome such a drawback inherent in the 30% Cr-60% Ni system alloy and which is excellent in a corrosion resistance, especially the stress corrosion cracking resistance so that it may be used for the tubes, the containers and their fittings in the nuclear reactors, the chemical plants and the like in the form of thick-walled plates, round rods or pipes.
  • the inventors of the present case have paid much attention to the fact that the aforesaid 30% Cr-60% Ni based alloy is finally annealed at a relatively high temperature of 980 to 1150°C in compliance with a carbon content and is used in a state of including no insolubilized carbide, and they have researched into a relation between a morphology of the carbide in the alloy system and its corrosiveness. As a result, it has been found that an active deposition of the carbide, if in the grains thereof, is rather effective for the improvement in the stress corrosion cracking resistance.
  • the gist of the present invention is directed to a nickel-chromium alloy excellent in a stress corrosion cracking resistance which is obtained by carrying out an annealing treatment under required conditions, said alloy having the following composition:
  • the above-mentioned required conditions mean annealing conditions within a range (Y) surrounded by points A, B, C, D and E in Figure 4 attached hereto or an annealing operation at a temperature of 900 to 975°C.
  • 0.2 to 5.0% of Nb is further added to the above-mentioned composition on condition that the content of Ti-is 0.2 to 1.0% and Nb/C is 10 to 125.
  • the stress corrosion cracking resistance of the Ni-Cr alloy which is heretofore insufficient, can be remarkably improved.
  • Such an unexpected effect would be considered to be due to a synergistic effect of (i) the requirement that the C content is limited to 0.04% or less and a final annealing is carried out at a relatively low temperature in compliance with the C content, and (ii) the requirement that at least one of Mo, W and V is added as an element for reinforcing the coating.
  • the stress corrosion cracking resistance of the Ni-Cr alloy which is heretofore insufficient, can also be remarkably improved.
  • Such an effect would be considered to be due to a synergistic effect of (i) the fact that when the C content is limited to 0.04% or less and the final annealing operation is carried out at a relatively low temperature of 900 to 975°C, in the case of the Ni based alloy including 40% or more of Ni, Nb has a greater carbon-fixing effect than Ti, therefore a less amount of Cr carbide will deposit on crystal boundaries, and (ii) the intention that at least one of Mo, W and V is added for the reinforcement of the coatings.
  • a heat transfer pipe of a steam generator in a nuclear reactor such as a pressurized water reactor is made of an only annealed alloy or Alloy 600 (trade name, 75%Ni-15%Cr-8%Fe) which has further been subjected to a specific thermal treatment (700°C x 15 hr).
  • Alloy 600 which is the alloy for the heat transfer pipe has the following problems.
  • a stress corrosion cracking sometimes occurs owing to an alkaline concentrate in the gap between the heat transfer pipe and a pipe-supporting plate in envrironments (alkaline environments including ammonia and hydrazine and having a pH of 9.2 to 9.5 and a temperature of 280°C) on the secondary side of the nuclear reactor, and a pitting corrosion tends to take place owing to Cl - ions in leaked seawater in the same environments on the secondary side of the nuclear reactor. Further, this pitting corrosion will deeply penetrate and the number of the pitting corrosions will augment with the increase in a concentration of the Cl ions.
  • Japanese Patent Disclosure No. 25216/1979 discloses a method in which after a final annealing treatment, the alloy is successively heated and retained at a temperature of 550 to 850°C for a period of 1 to 100 hours in order to deposit a carbide on crystal boundaries, thereby heightening the SCC resistance.
  • a resistance to the stress corrosion cracking caused by the alkaline concentrate i.e. an alkali stress corrosion cracking resistance and the pitting corrosion resistance cannot be improved.
  • the nickel based alloy obtained by such a conventional method cannot always provide a satisfactory combination of the alkali stress corrosion cracking resistance and the pitting corrosion resistance.
  • an object of the present invention is to provide an alloy for a heat transfer pipe excellent in the corrosion resistance, especially an alloy for a heat transfer pipe excellent in the alkali stress corrosion cracking resistance and the pitting corrosion resistance.
  • Another object of the present invention- is to provide an alloy for a heat transfer pipe which can be used particularly advantageously under alkali environments in a steam generator of a pressurized water reactor.
  • the nickel based alloy inter alia the high Cr-Ni based alloy including 25 to 35% of Cr is small in the solubility of C therein, Cr carbide deposits on crystal boundaries during the cooling process or practical use after the annealing step in order to form Cr-poor layers thereon, so that the stress corrosion cracking will take place thereon.
  • the present invention is characterized by an alloy for heat transfer pipes excellent in an alkali stress corrosion cracking resistance which is obtained by heating and retaining said alloy at a temperature within the range of a temperature (T°C), at which a carbide in said alloy is thoroughly solubilized, to T + 100°C for 1 minute or more; cooling it once to a level of 200°C or less; and carrying out a thermal treatment under conditions within a hatched range Z in Figure 15, said alloy comprising:
  • the present invention is directed to the alloy for a heat transfer pipe which is excellent in the alkali stress corrosion cracking resistance and the pitting corrosion resistance in the alkaline environments, but in a preferred embodiment, it is directed to the alloy for a heat transfer pipe on the secondary side of a nuclear reactor, for example a heat transfer pipe of a steam generator in a pressurized water reactor.
  • FIGS. 1 to 3 the detailed description will be made to an alloy to be treated.
  • the content of Cr is less than 25%, the alloy will have a less crystal boundary etching resistance and stress corrosion cracking resistance; when it is more than 35%, abnormal substances will deposit in the second thermal treatment process, which fact will lead to the deterioration in ductility. Therefore, the content of Cr is within the range of 25 to 35%.
  • the content of B is 0.003% or less.
  • the content of C is less than 0.012%, the alloy will have an insufficient strength; when it is in excess of 0.035%, it will be poor in the stress corrosion cracking resistance. Therefore, the content of C is within the range of 0.012 to 0.035%.
  • Elements P, S and the like are incorporated into the product as impurities during a process of a usual iron manufacture or steel manufacture, but too much impurities have bad influence upon the corrosion resistance. Therefore, the content of P is 0.015% or less and that of S is also 0.015% or less.
  • Mn and Si are added for the sake of a deoxidation, a reinforcement of a matrix and a reinforcement of grain boundaries, but when the content of Mn is more than 1%, the alloy will be hard to melt, and when the content of Si is more than 0.5%, the alloy will be poor in welding properties. Therefore, the content of Mn is 1% or less, and that of Si is limited to 0.5% or less.
  • the retention time is prolonged with the increase in the wall thickness of the material, hence it is impossible to uniformly define the retention time.
  • the retention time takes 30 minutes or so per 2.54 cm (1 inch) of the material thickness, and in the case that the material thickness is 2.54 cm or less, 1 to 30 minutes will be usually taken.
  • the alloy is cooled, for example, from a level of 200°C to room temperature.
  • the cooling rate less than a furnace cooling rate is not advantageous, but any rate of the furnace cooling rate or more is in fact satisfactory.
  • the cooling rate of the furnace cooling rate or more can be obtained by, for example, the furnace cooling, an air cooling, gas cooling, oil cooling, water cooling and the like.
  • the nickel based alloy according to the present invention can noticeably improve the crystal boundary etching resistance, pitting corrosion resistance, mechanical properties and stress corrosion cracking resistance, therefore this invention is most suitable for the thermal treatment for materials which will be subjected to a high-temperature and high-pressure water of 200 to 400°C, for example, materials for a container for giving off vapor in a nuclear reactor and materials for a cooling system in the nuclear reactor.
  • the element Cr is essential for the improvement in the corrosion resistance, but its amount less than 25% is insufficient to enhance the SCC resistance. On the contrary, when it is more than 35%, a hot workability will remarkably deteriorate. Therefore, the content of Cr is limited to the range of 25 to 35% in the present invention.
  • the element P is present in the alloy as an impurity. If its content is above 0.030%, it will exert a harmful influence upon the acid resistance and the hot workability.
  • the element S is also one of the impurities. If being present in an amount more than 0.02%, it will be deleterious to the acid resistance and hot workability, as in the case of P.
  • This element Ti is added as a stabilizing agent. That is to say, even if the contents of P and S are controlled below the above-mentioned levels, a remarkable effect cannot be obtained. Therefore, in the present invention, Ti is added in an amount of 0.05% or more to assure the desired hot workability. On the contrary, when the content of Ti is more than 1.0%, its effect will reach a ceiling level. Therefore, the upper limit of this element is to be set to 1.0%.
  • these elements are effective to heighten the pitting corrosion resistance especially in a high-temperature water including Cl - ions.
  • the content of at least one of these elements is less than 0.5% in all, the passive coating on the surface will not be heightened and a pitting corrosion will occur, thereby deteriorating the stress corrosion cracking resistance.
  • the content of at least one of them is more than 5.0% in all, the effect of the improvment in the pitting corrosion resistance will reach a ceiling level, and the hot workability will noticeably be deteriorated. Therefore, in the present invention, the amount of one or more of Mo, W and V to be added is limited to the range of 0.5 to 5.0% in all.
  • Nb is greater in the effect of a carbon fixation than Ti.
  • the content of Nb is set to the range of 0.2 to 5.0%. In this range, the ratio of Nb/C will become 10 to 125. In the case of its amount being 0.2% or less, the effect of fixing carbon is small and a sensitization will thus occur, thereby generating the SCC (stress corrosion cracking).
  • the content of Nb is more than 5%, the effect (carbon fixation) will reach a ceiling level, and additionally the hot workability will noticeably be deteriorated. Therefore, its upper limit is set to 5.0%.
  • lines BC and CD represent recrystallization lines of the alloy according to the present invention. If the annealing treatment is carried out at a temperature below the levels of the lines BC and CD, no recrystallization will occur, so that the strength of the annealed alloy will be high and its corrosion resistance will be bad. Therefore, the annealing treatment is required to be carried out at a temperature above the levels of the lines BC and CD in accordance with a C content in the alloy.
  • a line AE in the same drawing means an upper limit of temperatures at which the carbon in the alloy is not thoroughly solubilized. Accordingly, so long as the annealing treatment is carried out at a temperature below this upper limit, a carbide will be present in the grains.
  • the annealing operation is done at a temperature above a level of the line AE, all the carbide will be deposited on crystal boundaries in the case that a sensitization treatment is accomplished at at a temperature of 600°C for a period of 3 hours. This will lead to the deterioration in the crystal boundary etching resistance. Therefore, the final annealing is required to be carried out at a temperature below the level of the line AE.
  • Alloys (Alloy Nos. of the present invention 1 to 29, conventional alloys Nos. 30 to 37 and comparative alloys Nos. 38 to 41) of compositions comprising chemical components exhibited in Table 1 below were dissolvingly formed in a 17-kg vacuum furnace and subjected to a forging, hot rolling and thermal treatment under usual conditions, and they were then cold rolled as much as 30%, followed by annealing at a variety of temperatures. Further, a thermal treatment, i.e.
  • the specimens for the stress corrosion cracking tests were, after polished, caused to overlap each other every 2 specimens and each pair of them was bent into a U-shape to prepare double U-bent speciments.
  • the thus prepared specimens were immersed in a solution including 1000 ppm of Cl (as N aCl) at 325°C for 1500 hours by the use of an autoclave (a high-temperature and high-pressure container). After the completion of the tests,cracks on inside surfaces of the specimens were measured for their depth by a microscope.
  • the specimens for the crystal boundary etching tests were immersed in a boiling solution including 60% of HNO 3 and 0.1% of HF for 4 hours, and a weight loss caused by the corrosion was measured.
  • the annealing temperature is high and when 3 hours' heating at 600°C (the sensitization treatment) and an air cooling operation are carried out, the carbide of Cr will all deposit on the crystal boundaries and Cr-free layers will be formed in the vicinity of the crystal boundaries, so that corrosion will occur. Therefore, it is necessary to lower the annealing temperature.
  • the graphs in Figure 6 show the crystal boundary etching resistances of the alloys comprising the compositions regarding the present invention and conventional allohs.
  • the alloys in both the groups which had the composition of 0.02 to 0.03% of C and 0.6% of Mo were heated at 900°C for 30 minutes to accomplish the annealing treatment. After water cooling, they were heated at 600°C for 3 hours to accomplish the sensitization treatment, followed by air cooling.
  • white and black circles represent the alloys including more than 30% of Cr and those including 25 to 30% of Cr, respectively.
  • the alloys including an Ni amount below 40% are all great in a corrosion rate; the alloys including an Ni amount of 40% or more have an improved crystal boundary etching resistance. Therefore, the Ni content of 40% or more is necessary.
  • the total amount of one or more of the added Mo, V and W is required to be 0.5% or more.
  • the graphs in Figure 8 show influences of an Ni content(%) and Cr content (%) upon the SCC resistance.
  • Used alloy specimens were prepared through the annealing treatment of 30 minutes' heating at 900°C, water cooling, sensitization treatment of 3 hours' heating at 600°C, and air cooling.
  • white and black circles represent the alloys without stress corrosion cracks and those with some cracks of 20 p or more.
  • the Ni content is required to be 40% or more.
  • the annealing treatment is carried out at a temperature of 900 to 975°C.
  • this annealing temperature is less than 900°C, recrystallization cannot be effected. Therefore, the treated alloy has a high strength and is insufficient in the corrosion resistance.
  • the annealing temperature is more than 975°C, the carbon in the alloy will be thoroughly solubilized during the annealing operation, so that no carbide will exist in the grains any more.
  • the final annealing operation in the present invention is carried out at a temperature of 900 to 975°C.
  • Alloys (Alloy Nos. of the present invention 1 to 36 and comprative alloys Nos. 37 to 63) of compositions comprising chemical components exhibited in Table 5 below were dissolvingly formed in a 17-kg vacuum furnace and subjected to a forging, hot rolling and thermal treatment under usual conditions, and they were then cold rolled as much as 30%, followed by annealing at a variety of temperatures. Further, a thermal treatment, i.e.
  • the specimens for the stress corrosion cracking tests were, after polished, caused to overlap each other every 2 specimens and were bent into a U-shape to prepare double U-bent specimens.
  • the thus prepared specimens were immersed in a solution including 1000 ppm of Cl (as NaCl) at 330°C for 1500 hours by the use of an autoclave (a high-temperature and high-pressure container). After the completion of the tests, cracks on inside surfaces of the specimens were measured for their depth by a microscope.
  • the specimens for the crystal boundary etching tests were immersed in a boiling solution including 60% of HNO 3 and 0.1% of HF for 4 hours, and a weight loss caused by the corrosion was measured.
  • Graphs in Figure 9 show crystal boundary etching test results of the alloys in which about 0.6% of Mo, W and V was respectively added to the 25% Cr-55% Ni system alloy and various amounts of Nb were added thereto varying the ratio of Nb/C.
  • an annealing treatment was carried out by heating the alloy specimens at 950°C for 30 minutes. After water cooling, the sensitization treatment was carried out by heating them at 600°C for 5 hours and they were then air cooled.
  • Figure 9 indicates that the alloys in which the ratio of Nb/C is less than 10 is very bad in the crystal boundary etching resistance, but when this ratio is 10 or more, the crystal boundary etching resistance is sharply improved.
  • Figure 10 shows SCC test results of the alloys in which the Nb/C was 15 to 20; a Cr content was 25%; Mo, W and V were respectively included in an amount of 0.6%; and an Ni content was caused to vary within the range of 18 to 75%.
  • the used alloy specimens were prepared by heating them at 950°C for 30 minutes to accomplish the annealing treatment, followed by water cooling.
  • Graphs in Figure 11 indicate the presence of a pitting corrosion on the Cr-V-W alloys in a high-temperature and high-pressure solution including 1000 ppm of Cl ions, in which alloy the Nb/C was 12 or more and the Ni content was 40% or more.
  • the alloy specimens were used which were prepared by heating them at 950°C for 30 minutes in order to accomplish the annealing treatment, followed by water cooling.
  • circle and triangle marks represent the alloy specimens including V and the alloy specimens including W, respectively. As seen from the drawing, if the Cr content is less than 25%, the pitting corrosion will occur, even though the contents of V and W each are 0.6% or more and the ratio of the Nb/C is 12 or more.
  • the pitting corrosion resistance can be improved by the synergistic effect resulting from the addition of Cr, V and/or W.
  • Figure 12 shows, as in Figure 11, data regarding the pitting corrosion resistance of the alloys each in which M o or a group of M o, W and V is further included in addition to such a synergistic effect.
  • the alloy specimens were used which were prepared by heating them at 950°C for 30 minutes in order to accomplish the annealing treatment, followed by water cooling.
  • circle and rhomb marks represent the alloy specimens including Mo and the group of Mo, W and V, respectively.
  • the graphs in Figure 13 show influence of the annealing temperatures upon the stress corrosion cracking.
  • the specimens of alloy Nos. 1 and 12 exhibited in Table 5 were employed, and the annealing operation was carried out variously changing the annealing temperatures within the range of 850 to 1050°C.
  • the sensitization treatment was carried out by heating them at 600°C for 5 hours and they were then air cooled. Stress corrosion cracking tests were effected on the thus obtained specimens to measure a depth of cracks.
  • the alloy specimens which were annealed at a temperature of 900 to 975°C are excellent in the stress corrosion cracking resistance. This reason would be that NbC deposits in order to fix the solubilized carbon.
  • composition of the alloy and the conditions of the thermal treatment are restricted as mentioned above in the present invention is as follows:
  • the above-mentioned temperature at which the carbide in the alloy is thoroughly solubilized varies with a carbon content as exhibited in Figure 14, but it is, e.g. 950°C at 0.01% carbon content, 1050°C at 0.02% content and 1100°C at 0.03% content.
  • the specific thermal treatment is carried out by retaining a temperature of 600 to 750°C for 0.1 to 100 hours as shown in Figure 15, whereby the carbide will semicontinuously deposit on the crystal boundaries and the Cr-poor layers in the vicinity of positions where the carbide exists will recover, thereby increasing the crystal boundary stress corrosion cracking resistance.
  • the reason why such specific thermal treatment conditions are restricted to the hatched range (Z) in Figure 15 is as follows: On the left side of the hatched range (Z) in Figure 15, the retention time is lacking. As a result, the Cr carbide will deposit on the crystal boundaries and the Cr-poor layers formed therearound will not enough recover, so that the SCC resistance cannot be obtained to a satisfactory degree.
  • the hatched range (Z) terminates at a position corresponding to 100 hours.
  • Such a restriction is for an economical reason, though the farther prolonged heating treatment is good for the SCC resistance.
  • temperature when it is less than 600°C, diffusion rates of Cr and C will be low.
  • the very longtime heating operation will be required, which fact is not practical. Therefore, the lower limit of the temperature is set to 600°C.
  • the thermal treatment conditions in the present invention are restricted to the hatched range (Z) surrounded by points A (10 1 hours, 750°C), B (10 2 hours, 750° C ) and C (10 2 hours, 600°C) in Figure 15.
  • the alkali stress corrosion cracking test was accomplished by polishing the specimens with emery paper No. 320; bending them into a U-shape and holding them with bolts and nuts; immersing them in a solution including 30% of NaOH in an autoclave container (a high-temperature and high-pressure container) at 325°C for 2000 hours; and, after the completion of the immersion process, measuring a depth of cracks by a microscope.
  • an autoclave container a high-temperature and high-pressure container
  • the corrosion test was accomplished by polishing the specimens with emery paper No. 320; immersing them in a solution including 100 ppm of Cl ions and having a pH of 4.5 in an autoclave container at 288°C for 2000 hours; and measuring a corrosion amount.
  • Figure 15 presents the stress corrosion cracking test results of the specimens of alloy No. 1 under the above-mentioned alkaline conditions.
  • white circles and black circles represent specimens having cracks less than 25 p in depth and those having cracks more than 25 ⁇ in depth, respectively.
  • the specimens in the hatched range (Z) surrounded by points A, B and C have good alkali stress corrosion cracking resistance.
  • the alloys according to the present invention other than alloy No. 1 also had substantially similar results.
  • Table 7 summarizes the results of the corrosion resistance under the same conditions as in Figure 16.
  • circles, triangles and crosses represent specimens not having any pitting corrosion, those having the slight pitting corrosions and those having the pitting corrosions. It can be understood from these results that the alloys according to the present invention are more excellent in the pitting corrosion resistance, as compared with the conventional alloys. Particularly, when the total amount of Mo, V and W to be added is 1.0% or more the alloy can have the extremely excellent pitting corrosion resistance.
  • the alloy according to the present invention is excellent in the pitting corrosion resistance, the stress corrosion cracking resistance and the alkali stress corrosion cracking resistance, and, in place of the conventional Alloy 600, the alloy according to the present invention can be thus used, for example, particularly for a heat transfer pipe of a steam generator in a pressurized water reactor.

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EP83730106A 1982-11-10 1983-11-09 Alliage nickel-chrome Expired - Lifetime EP0109350B1 (fr)

Applications Claiming Priority (8)

Application Number Priority Date Filing Date Title
JP197362/82 1982-11-10
JP57197362A JPS5985850A (ja) 1982-11-10 1982-11-10 Ｎｉ基合金の熱処理法
JP10409583A JPS59232246A (ja) 1983-06-13 1983-06-13 耐応力腐食割れ性に優れたＮｉ−Ｃｒ合金
JP104094/83 1983-06-13
JP104095/83 1983-06-13
JP10409483A JPS59229457A (ja) 1983-06-13 1983-06-13 耐応力腐食割れ性に優れたＮｉ基高Ｃｒ合金
JP156427/83 1983-08-29
JP58156427A JPS6050134A (ja) 1983-08-29 1983-08-29 伝熱管用合金およびその製造方法

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Application Number Title Priority Date Filing Date
EP19890103551 Division-Into EP0329192B1 (fr) 1982-11-10 1983-11-09 Alliage nickel-chrome
EP89103551.1 Division-Into 1983-11-09

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EP0109350A2 true EP0109350A2 (fr) 1984-05-23
EP0109350A3 EP0109350A3 (en) 1987-08-26
EP0109350B1 EP0109350B1 (fr) 1991-10-16

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Cited By (27)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0235075A2 (fr) * 1986-01-20 1987-09-02 Mitsubishi Jukogyo Kabushiki Kaisha Alliage à base de nickel et procédé pour sa fabrication
EP0261880A2 (fr) * 1986-09-25 1988-03-30 Inco Alloys International, Inc. Traitement thermique d'un alliage à base de nickel
US4877465A (en) * 1986-03-18 1989-10-31 Electicite De France (Service National) Structural parts of austenitic nickel-chromium-iron alloy
EP0398761A1 (fr) * 1989-05-19 1990-11-22 Inco Alloys International, Inc. Méthode de traitement thermique pour diminuer la corrosion par fissuration sous contraintes en présence d'acide polythionique
EP0421705A1 (fr) * 1989-10-02 1991-04-10 Inco Alloys Limited Alliage pour soupape d'échappement
US5211911A (en) * 1992-03-09 1993-05-18 Epri High vanadium austenitic heat resistant alloy
FR2845098A1 (fr) * 2002-09-26 2004-04-02 Framatome Anp Alliage a base de nickel pour la soudure electrique d'alliages de nickel et d'aciers fil de soudage et utilisation
EP1433864A3 (fr) * 2002-12-25 2004-11-03 Sumitomo Metal Industries, Ltd. Alliage de nickel et procédé de fabrication
WO2008021650A2 (fr) * 2006-08-08 2008-02-21 Huntington Alloys Corporation Alliage de soudage et articles destinés à être utilisés pour le soudage, ensembles soudés et procédé de production d'ensembles soudés
WO2012166295A3 (fr) * 2011-06-01 2013-01-24 Ati Properties, Inc. Traitement thermo-mécanique d'alliages à base de nickel
US8722062B2 (en) 2001-01-23 2014-05-13 Sanofi Pasteur, Inc. Multivalent meningococcal polysaccharide-protein conjugate vaccine
US8834653B2 (en) 2010-07-28 2014-09-16 Ati Properties, Inc. Hot stretch straightening of high strength age hardened metallic form and straightened age hardened metallic form
US9050647B2 (en) 2013-03-15 2015-06-09 Ati Properties, Inc. Split-pass open-die forging for hard-to-forge, strain-path sensitive titanium-base and nickel-base alloys
US9192981B2 (en) 2013-03-11 2015-11-24 Ati Properties, Inc. Thermomechanical processing of high strength non-magnetic corrosion resistant material
US9206497B2 (en) 2010-09-15 2015-12-08 Ati Properties, Inc. Methods for processing titanium alloys
US9255316B2 (en) 2010-07-19 2016-02-09 Ati Properties, Inc. Processing of α+β titanium alloys
US9523137B2 (en) 2004-05-21 2016-12-20 Ati Properties Llc Metastable β-titanium alloys and methods of processing the same by direct aging
US9777361B2 (en) 2013-03-15 2017-10-03 Ati Properties Llc Thermomechanical processing of alpha-beta titanium alloys
US9796005B2 (en) 2003-05-09 2017-10-24 Ati Properties Llc Processing of titanium-aluminum-vanadium alloys and products made thereby
US9869003B2 (en) 2013-02-26 2018-01-16 Ati Properties Llc Methods for processing alloys
US10053758B2 (en) 2010-01-22 2018-08-21 Ati Properties Llc Production of high strength titanium
US10094003B2 (en) 2015-01-12 2018-10-09 Ati Properties Llc Titanium alloy
US10435775B2 (en) 2010-09-15 2019-10-08 Ati Properties Llc Processing routes for titanium and titanium alloys
US10502252B2 (en) 2015-11-23 2019-12-10 Ati Properties Llc Processing of alpha-beta titanium alloys
US10513755B2 (en) 2010-09-23 2019-12-24 Ati Properties Llc High strength alpha/beta titanium alloy fasteners and fastener stock
US11111552B2 (en) 2013-11-12 2021-09-07 Ati Properties Llc Methods for processing metal alloys
CN115247225A (zh) * 2022-03-09 2022-10-28 江西宝顺昌特种合金制造有限公司 一种中频炉冶炼uns n06600钢方法

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Cited By (53)

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EP0235075A3 (en) * 1986-01-20 1988-09-21 Mitsubishi Jukogyo Kabushiki Kaisha Ni-based alloy and method for preparing same
EP0235075A2 (fr) * 1986-01-20 1987-09-02 Mitsubishi Jukogyo Kabushiki Kaisha Alliage à base de nickel et procédé pour sa fabrication
US4877465A (en) * 1986-03-18 1989-10-31 Electicite De France (Service National) Structural parts of austenitic nickel-chromium-iron alloy
EP0261880A2 (fr) * 1986-09-25 1988-03-30 Inco Alloys International, Inc. Traitement thermique d'un alliage à base de nickel
EP0261880A3 (en) * 1986-09-25 1988-09-14 Inco Alloys International, Inc. Nickel-base alloy heat treatment
EP0398761A1 (fr) * 1989-05-19 1990-11-22 Inco Alloys International, Inc. Méthode de traitement thermique pour diminuer la corrosion par fissuration sous contraintes en présence d'acide polythionique
EP0421705A1 (fr) * 1989-10-02 1991-04-10 Inco Alloys Limited Alliage pour soupape d'échappement
US5211911A (en) * 1992-03-09 1993-05-18 Epri High vanadium austenitic heat resistant alloy
EP0561488A2 (fr) * 1992-03-09 1993-09-22 Electric Power Research Institute, Inc Acier austenitique et résistant à la chaleur à haute teneur en vanadium
EP0561488A3 (fr) * 1992-03-09 1993-11-03 Electric Power Research Institute, Inc Acier austenitique et résistant à la chaleur à haute teneur en vanadium
US8722062B2 (en) 2001-01-23 2014-05-13 Sanofi Pasteur, Inc. Multivalent meningococcal polysaccharide-protein conjugate vaccine
FR2845098A1 (fr) * 2002-09-26 2004-04-02 Framatome Anp Alliage a base de nickel pour la soudure electrique d'alliages de nickel et d'aciers fil de soudage et utilisation
EP1408130A1 (fr) * 2002-09-26 2004-04-14 Framatome ANP Alliage à base de nickel pour la soudure électrique d'alliages de nickel et d'aciers, fil de soudage et utilisation
EP1433864A3 (fr) * 2002-12-25 2004-11-03 Sumitomo Metal Industries, Ltd. Alliage de nickel et procédé de fabrication
US7799152B2 (en) 2002-12-25 2010-09-21 Sumitomo Metal Industries, Ltd. Method for manufacturing nickel alloy
US9796005B2 (en) 2003-05-09 2017-10-24 Ati Properties Llc Processing of titanium-aluminum-vanadium alloys and products made thereby
US10422027B2 (en) 2004-05-21 2019-09-24 Ati Properties Llc Metastable beta-titanium alloys and methods of processing the same by direct aging
US9523137B2 (en) 2004-05-21 2016-12-20 Ati Properties Llc Metastable β-titanium alloys and methods of processing the same by direct aging
WO2008021650A2 (fr) * 2006-08-08 2008-02-21 Huntington Alloys Corporation Alliage de soudage et articles destinés à être utilisés pour le soudage, ensembles soudés et procédé de production d'ensembles soudés
WO2008021650A3 (fr) * 2006-08-08 2008-04-10 Huntington Alloys Corp Alliage de soudage et articles destinés à être utilisés pour le soudage, ensembles soudés et procédé de production d'ensembles soudés
US10053758B2 (en) 2010-01-22 2018-08-21 Ati Properties Llc Production of high strength titanium
US9255316B2 (en) 2010-07-19 2016-02-09 Ati Properties, Inc. Processing of α+β titanium alloys
US10144999B2 (en) 2010-07-19 2018-12-04 Ati Properties Llc Processing of alpha/beta titanium alloys
US9765420B2 (en) 2010-07-19 2017-09-19 Ati Properties Llc Processing of α/β titanium alloys
US8834653B2 (en) 2010-07-28 2014-09-16 Ati Properties, Inc. Hot stretch straightening of high strength age hardened metallic form and straightened age hardened metallic form
US9624567B2 (en) 2010-09-15 2017-04-18 Ati Properties Llc Methods for processing titanium alloys
US9206497B2 (en) 2010-09-15 2015-12-08 Ati Properties, Inc. Methods for processing titanium alloys
US10435775B2 (en) 2010-09-15 2019-10-08 Ati Properties Llc Processing routes for titanium and titanium alloys
US10513755B2 (en) 2010-09-23 2019-12-24 Ati Properties Llc High strength alpha/beta titanium alloy fasteners and fastener stock
US9616480B2 (en) 2011-06-01 2017-04-11 Ati Properties Llc Thermo-mechanical processing of nickel-base alloys
AU2012262929B2 (en) * 2011-06-01 2016-02-04 Ati Properties, Inc. Thermo-mechanical processing of nickel-base alloys
RU2607682C2 (ru) * 2011-06-01 2017-01-10 ЭйТиАй ПРОПЕРТИЗ ЭлЭлСи Термомеханическая обработка сплавов на основе никеля
WO2012166295A3 (fr) * 2011-06-01 2013-01-24 Ati Properties, Inc. Traitement thermo-mécanique d'alliages à base de nickel
CN103597105A (zh) * 2011-06-01 2014-02-19 Ati资产公司 镍基合金的热机械加工
US10287655B2 (en) 2011-06-01 2019-05-14 Ati Properties Llc Nickel-base alloy and articles
AU2016200033B2 (en) * 2011-06-01 2018-02-22 Ati Properties Llc Thermo-mechanical processing for nickel-base alloys
US8652400B2 (en) 2011-06-01 2014-02-18 Ati Properties, Inc. Thermo-mechanical processing of nickel-base alloys
EP3045552A1 (fr) * 2011-06-01 2016-07-20 ATI Properties, Inc. Traitement thermomécanique d'alliages à base de nickel
US10570469B2 (en) 2013-02-26 2020-02-25 Ati Properties Llc Methods for processing alloys
US9869003B2 (en) 2013-02-26 2018-01-16 Ati Properties Llc Methods for processing alloys
US10337093B2 (en) 2013-03-11 2019-07-02 Ati Properties Llc Non-magnetic alloy forgings
US9192981B2 (en) 2013-03-11 2015-11-24 Ati Properties, Inc. Thermomechanical processing of high strength non-magnetic corrosion resistant material
US10370751B2 (en) 2013-03-15 2019-08-06 Ati Properties Llc Thermomechanical processing of alpha-beta titanium alloys
US9777361B2 (en) 2013-03-15 2017-10-03 Ati Properties Llc Thermomechanical processing of alpha-beta titanium alloys
US9050647B2 (en) 2013-03-15 2015-06-09 Ati Properties, Inc. Split-pass open-die forging for hard-to-forge, strain-path sensitive titanium-base and nickel-base alloys
US11111552B2 (en) 2013-11-12 2021-09-07 Ati Properties Llc Methods for processing metal alloys
US10619226B2 (en) 2015-01-12 2020-04-14 Ati Properties Llc Titanium alloy
US10094003B2 (en) 2015-01-12 2018-10-09 Ati Properties Llc Titanium alloy
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US10502252B2 (en) 2015-11-23 2019-12-10 Ati Properties Llc Processing of alpha-beta titanium alloys
CN115247225A (zh) * 2022-03-09 2022-10-28 江西宝顺昌特种合金制造有限公司 一种中频炉冶炼uns n06600钢方法

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DE3382737T2 (de) 1994-05-19
EP0109350A3 (en) 1987-08-26
DE3382737D1 (de) 1994-03-10
EP0109350B1 (fr) 1991-10-16

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