EP2126152B1 - Verfahren für rissdesensibilisierung mittels legierungsumgebung auf nickelbasis, hauptsächlich für ein kernbrennstabbündel und für einen kernreaktor sowie aus derartig verarbeiteter legierung hergestelltes teil - Google Patents

Verfahren für rissdesensibilisierung mittels legierungsumgebung auf nickelbasis, hauptsächlich für ein kernbrennstabbündel und für einen kernreaktor sowie aus derartig verarbeiteter legierung hergestelltes teil Download PDF

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EP2126152B1
EP2126152B1 EP07871802.0A EP07871802A EP2126152B1 EP 2126152 B1 EP2126152 B1 EP 2126152B1 EP 07871802 A EP07871802 A EP 07871802A EP 2126152 B1 EP2126152 B1 EP 2126152B1
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alloy
treatment
desensitisation
based alloy
cracking
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French (fr)
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EP2126152A2 (de
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Jean-Marc Cloue
Véronique GARAT
Eric Andrieu
Julien Deleume
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Areva NP SAS
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Framatome SA
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • 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 invention relates to the metallurgy of nickel-based alloys, and more precisely the alloys used to manufacture structural components for nuclear reactors or for fuel assemblies inserted in said reactors.
  • Certain components of nuclear reactors such as heat exchangers, cluster guide pins, piping, screws and bolts used to secure the steel components used to make the cooling circuits of light water nuclear reactors or nuclear reactors with gas heat transfer fluid or molten salt or liquid metal, are made of nickel-based alloys, for example in different types of Inconel®. These components must, at high temperature and at high pressure, have good resistance to oxidation, to corrosion, to creep and to both thermal and mechanical cyclic stresses, and this for high durations (several tens of years), and nickel-based alloys are well suited for these uses.
  • Light water nuclear reactor fuel assemblies can also have some of their structural components made of a nickel-based alloy, of which alloy 718 is a preferred example. This is, in particular, the case of grid springs, usually produced from strips of such alloys, and retaining springs produced either from flat semi-finished products for leaf springs, or from wires for coil springs, and fasteners, made from bars.
  • the elements for which a minimum value is not fixed can be completely absent, or present only in the trace state.
  • a problem whose importance is growing in the operation of reactors containing such components is the resistance of said components to cracking assisted by the environment.
  • the specific conditions of the primary environment of light water reactors (LWR in English) are favorable to the development of cracking assisted by the environment.
  • Another method is to apply a suitable coating to the materials.
  • nickel plating of the grid springs of alloy 718 to reduce the number of their ruptures in service.
  • Other types of coatings for example surface treatments by diffusion, are also possible.
  • US-A-5 164 270 proposes to carry out an implantation of Nb and / or Zr on the surface of a ferrous alloy with 9-30% Cr and to expose it to a gas mixture O 2 / S. This would also apply to an Ni-based alloy.
  • Another solution consists in carrying out global or local heat treatments at high temperature (1100 ° C.) on the structural elements, causing modifications to the microstructure of the material. Local treatments are thus carried out on the elbows of steam generators in alloy 600. In this way, we have also sought to eliminate any trace of phase ⁇ in alloy 718 (see the document US-A-5,047,093 ).
  • Another solution consists in modifying the chemical composition of the material, in a more or less radical way, which can sometimes lead to the development of a new alloy shade. Alloy 600 has thus been replaced by alloy 690 for the manufacture of steam generator tubes. It is an expensive approach in terms of research and development, and it does not always lead to technically and / or economically viable results for industrial applications.
  • Desulfurization by annealing in hydrogen reduces the formation of interfacial porosity and can improve the resistance to cyclic oxidation until it becomes comparable to that obtained by adding reactive elements.
  • the article " Effects of hydrogen annealing, sulfur segregation and diffusion on the cyclic oxidation resistance of superalloys ", JL Smialek et al .; Thin solid films 253 (1994), pp. 285-292 discloses effective desulfurization performed by hydrogen annealing which results in excellent resistance to cyclic oxidation for a number of advanced superalloys.
  • the object of the invention is to propose a means of improving the performance and reliability of the components of nuclear reactors made of a nickel-based alloy subjected to conditions liable to favor the appearance of environment-assisted cracking, regardless of their design, particularly for long operating cycles.
  • This means should also be a means of suppressing the material's sensitivity to environmentally assisted cracking, with little or no interference with the other characteristics of the material.
  • Said environment-assisted cracking desensitization treatment can be carried out between 950 and 1010 ° C.
  • Said environment-assisted cracking desensitization treatment can be carried out between 1010 and 1160 ° C.
  • Said environment-assisted cracking desensitization treatment can be carried out on a semi-finished product, intended then to undergo a treatment aimed at modifying its metallurgical structure.
  • Said treatment can be an annealing, recrystallization, dissolution or hardening treatment, also called aging.
  • Said environment-assisted cracking desensitization treatment can be carried out on a product which is then no longer subjected to a treatment intended to modify its metallurgical structure.
  • Said desensitization treatment can be carried out in the presence of a compound having a greater avidity for oxygen than said alloy.
  • Said compound is a metal such as Al, Zr, Ti, Hf, or an alloy containing at least one of these metals, or an element or a compound of elements such as Mg, Ca.
  • the Ni-based alloy may be wrapped in a strip of said metal or alloy or compound having a greater affinity for oxygen than said Ni base alloy.
  • said Ni-based alloy may be placed in a housing comprising one or more walls made of said metal or alloy or compound having a greater avidity for oxygen than said Ni base alloy.
  • said Ni-based alloy may be placed in a powder of said metal or alloy or compound having a greater avidity for oxygen than said Ni-based alloy.
  • the invention according to claim 15 also relates to a part made of a nickel-based alloy, characterized in that said alloy has undergone a heat treatment for environmental assisted cracking desensitization of the preceding type.
  • Said part can be a structural element for assembling a nuclear reactor fuel.
  • Said part can then be a grid spring or holding system, or a screw.
  • Said part can be an element of the cooling circuits of a nuclear reactor.
  • Said part can then be a pipe, or a cluster guide pin, or a spring, or a heat exchanger, or a screw, or a bolt, or any other nickel-based alloy component in contact with the heat transfer fluid.
  • Said part can be a semi-finished product from which parts can be produced by a shaping process, or by machining, or by cutting.
  • Said part can then be a sheet, or a strip, or a wire, or a bar or a blank.
  • the invention is first based on the development of a heat treatment of the material, carried out under hydrogen or under a hydrogenated atmosphere, in the latter case generally in the presence of a powerful reducing agent.
  • This treatment leads to a lasting desensitization of the alloy with respect to cracking assisted by the environment, by a mechanism which will be explained.
  • This desensitization treatment does not replace any thermal treatment conventionally applied by a person skilled in the art to obtain the desired mechanical characteristics, but can be added to it.
  • the invention is also applicable to boiling water reactors (REB), and to reactors cooled by gas or molten salt or liquid metal, as well as to other devices using structural elements of nickel base alloy operating in oxidizing conditions, at medium (200-500 ° C) and high (500-1200 ° C) temperatures in liquid or gaseous medium.
  • REB boiling water reactors
  • the invention is also applicable to boiling water reactors (REB), and to reactors cooled by gas or molten salt or liquid metal, as well as to other devices using structural elements of nickel base alloy operating in oxidizing conditions, at medium (200-500 ° C) and high (500-1200 ° C) temperatures in liquid or gaseous medium.
  • the desensitization treatment must, if the desensitization temperature leads to a microstructure poorly suited to the application, to be supplemented by other thermal and / or thermomechanical treatments, aiming to restore the alloy to a structure and mechanical properties. making it optimally suited to the intended uses.
  • the oxygen atoms come from the impurities present in the surrounding medium or even from the material itself, the least amount of oxygen being compensated for by the higher operating temperature of the nickel-based alloy component.
  • a tensile test at 650 ° C in air, with a tensile speed of 10 -3 s -1 shows a facies of rupture of the test piece with some primers of intergranular rupture, but in significantly lower quantity than on samples of reference not processed.
  • a polishing on 15 ⁇ m of each face of a test piece identical to the previous one allows to obtain a totally ductile and transgranular fracture facies, thanks to the elimination of the surface area not completely desensitized.
  • Polishing is an optional operation. Its introduction into the desensitization process makes it possible to reduce the duration of the heat treatment.
  • a test program was then carried out to confirm the previous good results and to determine the range of suitable treatments.
  • the samples were strip 0.27 mm thick, the high sensitivity to cracking assisted by the environment was known (ruptures observed during use in the reactor).
  • the heat treatment temperature for desensitization was 990 ° C ⁇ 10 ° C, to avoid a magnification of the austenitic grain and limit the precipitation of phase ⁇ .
  • the treatment atmosphere was Ar-H 2 (5%).
  • the duration of the desensitization treatment went up to 100 hours.
  • the rupture facies was examined to determine if it was intergranular (IG), transgranular (TG) or mixed (IG + TG).
  • Test pieces 1 and 2 which have not undergone a desensitization treatment, have a facies of mixed fragile intergranular and transgranular ductile rupture.
  • the ductile transgranular character of the facies is all the more marked when the desensitization treatment has been long. From 36h, we find purely transgranular facies, and the facies become systematically purely transgranular beyond 39 hours of treatment. For treatment durations of 36 to 39 h, we are therefore at the limit of total desensitization of the samples, and obtaining partial or total desensitization is, in this case, dependent on the variability of the treatment conditions. , such as temperature.
  • a desensitization treatment at 980 ° C for at least 40 hours is therefore fully effective on these strips to obtain in all cases a total desensitization of the material to cracking assisted by the environment in air at 650 ° C.
  • phase ⁇ When an alloy 718 is treated at 850-1010 ° C, there is precipitation of a phase ⁇ the amount of which depends on the temperature and the treatment time.
  • the heating rate also has an important influence on the quantity of phase ⁇ present, particularly at high temperatures, above 950 ° C. For the lowest heating rates, phase ⁇ can form during heating. Therefore, depending on the holding temperature, the volume fraction of phase ⁇ tends to increase if the temperature is low, or to decrease and then stabilize if the temperature is at the top of the admissible range.
  • An essential condition for the desensitization of the alloy is that the heat treatment atmosphere is not oxidizing, and, even more, the atmosphere must allow the reduction of the oxide layer generally naturally present on the surface of the material. Unless a pure hydrogen atmosphere is used, it is very preferable to carry out the desensitization treatment in the presence of a compound which captures the oxygen present with more avidity than the part to be treated.
  • a metal or other compound very eager for oxygen such as Al, Ti, Hf, Zr, or an alloy containing at least one such metal at a high content, or an element or a compound of elements such as Mg, Ca can be used.
  • a first technique consists in wrapping the part in a strip having the composition of the metal or of the alloy playing the role of oxygen trap.
  • a second technique consists in placing the part in a box comprising one or more walls of this metal or of this alloy.
  • FeCrAlY alloy used during the desensitization tests described above.
  • This material used as a constituent of catalytic converters for the automobile industry, or as a constituent of parts for machine tools or of electrical resistances, is commonly available on the market and proves to be very effective.
  • Tests have also been carried out intended to test the sensitivity to cracking assisted by the environment of grid springs produced from an alloy 718 of the same composition as the aforementioned tensile test pieces. They were tested at 350 ° C in a primary REP environment with a displacement speed of 10 -7 s -1 and an imposed displacement adapted to the designs tested.
  • the atmosphere is made up either of pure hydrogen, or of a neutral gas, such as argon, mixed with at least 100 ppm of hydrogen, the absence of oxygen being preferably guaranteed by the presence in the environment.
  • a neutral gas such as argon
  • Said compound can be a metal such as Al, Zr, Ti, Hf or an alloy containing at least one of these metals, such as an FeCrAlY alloy, or an element or a compound of one or more elements such as Mg or Ca ...
  • the Ni-based alloy may be wrapped in a strip of said compound having a greater affinity for oxygen, carbon and nitrogen than said alloy with Ni base.
  • said Ni-based alloy may be placed in a housing comprising one or more walls made with said compound having a greater avidity for oxygen than said base-based alloy Or.
  • said Ni-based alloy may be immersed in a powder of said compound having a greater affinity for oxygen than said Ni-based alloy.
  • the brittleness F of the material is here defined as being the ratio of the cumulative length of the zones with intergranular cracking and the total length of the perimeter of the rupture facies, during a test carried out in a medium representative of the operating conditions of the component.
  • the choice of the treatment temperature range depends essentially on the phase of preparation of the material on which this treatment is carried out and on the requirements required on the microstructure at the end of treatment.
  • the treatment at higher temperature is preferably carried out at the semi-finished product stage, the subsequent treatments of the production range making it possible to regenerate the microstructure of the material if it has been adversely affected by desensitization.
  • the treatment at lower temperature is preferably carried out at the stage of the finished product, and therefore constitutes the last stage of production, the grain size then generally not being significantly influenced by the desensitization treatment.
  • the high temperature treatment can be carried out on the finished product when no microstructure requirement is imposed, such as for example on the cluster guide pins.
  • the treatment at lower temperature can be carried out on a semi-finished product, a treatment longer than at higher temperature being, in this case, necessary to obtain total desensitization, all other things being equal.
  • the duration of the heat treatment may, however, be desired to reduce the duration of the heat treatment, in particular when it is carried out at the semi-finished product stage.
  • the semi-finished product thus obtained will still be slightly sensitive to cracking assisted by the surface environment at the end of the treatment, due to the edge effects which lead to a concentration of the sensitizing elements at the metal / treatment atmosphere interface. .
  • the heat treatment is completed by an operation of removing the surface layer which is not completely desensitized.
  • the removal of the surface layer can be carried out by machining and / or chemical, electrochemical or mechanical polishing.
  • the environment-assisted cracking desensitization treatment of said Ni-based alloy can be followed, if necessary, by heat treatments of annealing, recrystallization, dissolution or hardening (also called aging treatments) conventionally applied.
  • heat treatments of annealing, recrystallization, dissolution or hardening also called aging treatments
  • An essential condition is that these possible heat treatments are carried out in a non-oxidizing atmosphere to avoid re-sensitizing the material to cracking assisted by the environment.
  • the invention allows parts and semi-finished products to be obtained, a non-exhaustive list of which will be given.
  • a part thus produced can be a structural element for assembling a nuclear reactor fuel.
  • Said part can then be a grid spring or holding system, or a screw.
  • Said part can be an element of the cooling circuits of a nuclear reactor.
  • Said part can then be a pipe, a cluster guide pin, a spring, a heat exchanger, a screw or a bolt, or any other nickel-based alloy component in contact with the heat transfer fluid.
  • a semi-finished product can be a sheet, a strip, a wire, a bar or even a blank obtained, for example, by forging, stamping, molding or even by sintering, from which parts can be produced by various processes conventional shaping, or machining, or cutting.
  • Alloy 718 thus treated, in particular, finds a privileged application in the manufacture of springs of grids and components of springs of system of maintenance for fuel assemblies of nuclear reactors, but can be used to constitute other parts including usage is compatible with its mechanical properties and which would be intended to be exposed in service to an environment favorable to the development of cracking assisted by the environment.

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Claims (22)

  1. Verfahren zum Wärmebehandeln zum Desensibilisieren gegen die Rissbildung durch die Umgebung einer Legierung basierend auf Ni der Zusammensetzung in Gewichtsprozent: C ≤ 0,10%, Mn ≤ 0,5%, Si ≤ 0,5%, P ≤ 0,015%, S ≤ 0,015%, Ni ≥ 40%, Cr = 12-40%, Co ≤ 10%, Al ≤ 5%, Mo = 0,1-15%, Ti ≤ 5%, B ≤ 0,01%, Cu ≤ 5%, W = 0,1-15%, Nb = 0-10%, Ta ≤ 10%, der Rest Fe und unvermeidbare Verunreinigungen, die aus der Erstellung resultieren, dadurch gekennzeichnet, dass ein Halten besagter Legierung durchgeführt wird bei 950-1160°C in einer Atmosphäre, die wenigstens 100ppm Wasserstoff gemischt mit einem neutralen Gas enthält oder in reinem Wasserstoff, wobei sich besagtes Desensibilisieren durch die Tatsache äußert, dass man nach einer Zugprüfung an Luft bei 650 °C bei einer Geschwindigkeit von 10-3s-1 eine gemischt transgranulare, spröde und transgranulare, duktile Bruchfläche oder eine rein transgranulare, duktile Bruchfläche beobachtet.
  2. Verfahren gemäß Anspruch 1, dadurch gekennzeichnet, dass besagtes Behandeln zum Desensibilisieren gegen die Rissbildung durch die Umgebung zwischen 950 und 1010 °C durchgeführt wird.
  3. Verfahren gemäß Anspruch 1, dadurch gekennzeichnet, dass besagtes Behandeln zum Desensibilisieren gegen die Rissbildung durch die Umgebung zwischen 1010 und 1160 °C durchgeführt wird.
  4. Verfahren gemäß einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass besagtes Behandeln zum Desensibilisieren gegen die Rissbildung durch die Umgebung auf einem Halbzeug durchgeführt wird, das dazu bestimmt ist, nachfolgend ein Behandeln zu erfahren, das darauf abzielt, seine metallurgische Struktur zu verändern.
  5. Verfahren gemäß Anspruch 4, dadurch gekennzeichnet, dass besagtes Behandeln ein Glühbehandeln, Rekristallisationsbehandeln, Lösungsbehandeln oder Härtebehandeln ist, welches in einer nicht-oxidierenden Atmosphäre realisiert wird.
  6. Verfahren gemäß einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass das Behandeln zum Desensibilisieren gegen die Rissbildung durch die Umgebung auf einem Erzeugnis durchgeführt wird, das nachfolgend kein Behandeln mehr erfährt, das darauf abzielt, seine metallurgische Struktur zu verändern.
  7. Verfahren gemäß einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass man ein Bearbeiten und/oder ein Polieren der Legierung nach ihrem Desensibilisieren gegen die Rissbildung durch die Umgebung vornimmt.
  8. Verfahren gemäß einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass besagtes Behandeln zum Desensibilisieren in Anwesenheit einer Verbindung, die eine größere Gier nach Sauerstoff wie besagte Legierung zeigt, durchgeführt wird.
  9. Verfahren gemäß Anspruch 8, dadurch gekennzeichnet, dass besagte Verbindung ein Metall wie Al, Zr, Ti, Hf oder eine Legierung, die wenigstens eines dieser Metalle oder ein Element oder eine Verbindung von Elementen wie Mg, Ca enthält, ist.
  10. Verfahren gemäß Anspruch 9, dadurch gekennzeichnet, dass wenigstens während des Behandelns zum Desensibilisieren gegen die Rissbildung durch die Umgebung die Legierung basierend auf Ni in ein Band des besagten Metalls oder der besagten Legierung oder Verbindung, die eine größere Sauerstoffaffinität als besagte Legierung basierend auf Ni zeigt, eingewickelt ist.
  11. Verfahren gemäß Anspruch 9, dadurch gekennzeichnet, dass wenigstens während des Behandelns zum Desensibilisieren gegen die Rissbildung durch die Umgebung besagte Legierung basierend auf Ni in ein Gehäuse gesetzt wird, das eine oder mehrere Wände aus besagtem Metall oder besagter Legierung oder Verbindung, die eine größere Gier nach Sauerstoff als besagte Legierung basierend auf Ni zeigt, aufweist.
  12. Verfahren gemäß Anspruch 9, dadurch gekennzeichnet, dass wenigstens während des Behandelns zum Desensibilisieren gegen die Rissbildung durch die Umgebung besagte Legierung basierend auf Ni in ein Puder von besagtem Metall oder besagter Legierung oder Verbindung, die eine größere Gier nach Sauerstoff als besagte Legierung basierend auf Ni zeigt, gesetzt wird.
  13. Verfahren gemäß einem der Ansprüche 1 bis 12, dadurch gekennzeichnet, dass die Legierung die Zusammensetzung in Gewichtsprozent hat: C ≤ 0,08%, Mn ≤ 0,35%, Si ≤ 0,35%, P ≤ 0,015%, S ≤ 0,015%, Ni = 50-55%, Cr = 17-21%, Co ≤ 1%, Al = 0,2-0,8%, Mo = 2,8-3,3%, Ti = 0,65-1,15%, B ≤ 0,006%, Cu ≤ 0,3%, Nb + Ta = 4,75-5,5%, der Rest Fe und unvermeidbare Verunreinigungen, die aus der Erstellung resultieren.
  14. Verfahren zum Herstellen eines Werkstücks aus einer Legierung basierend auf Nickel der Zusammensetzung in Gewichtsprozent: C ≤ 0,10%, Mn ≤ 0,5%, Si ≤ 0,5%, P ≤ 0,015%, S ≤ 0,015%, Ni > 40%, Cr = 12-40%, Co ≤ 10%, Al ≤ 5%, Mo = 0,1-15%, Ti ≤ 5%, B ≤ 0,01%, Cu ≤ 5%, W = 0,1-15%, Nb = 0-10%, Ta ≤ 10%, der Rest Fe und unvermeidbare Verunreinigungen, die aus der Erstellung resultieren, dadurch gekennzeichnet, dass es ein Wärmebehandeln zum Desensibilisieren der Legierung gegen die Rissbildung durch die Umgebung gemäß einem der Ansprüche 1 bis 12 aufweist.
  15. Werkstück, das aus einer Legierung basierend auf Nickel realisiert ist, dadurch gekennzeichnet, dass besagte Legierung ein Wärmebehandeln zum Desensibilisieren gegen die Rissbildung durch die Umgebung gemäß einem der Ansprüche 1 bis 13 erfahren hat, wobei sich besagtes Desensibilisieren durch die Tatsache äußert, dass man nach einer Zugprüfung an Luft bei 650 °C bei einer Geschwindigkeit von 10-3s-1 eine gemischt transgranulare, spröde und transgranulare, duktile Bruchfläche oder eine rein transgranulare, duktile Bruchfläche beobachtet.
  16. Werkstück gemäß Anspruch 15, dadurch gekennzeichnet, dass besagtes Werkstück ein Strukturelement zum Montieren eines Kernreaktorbrennelements ist.
  17. Werkstück gemäß Anspruch 16, dadurch gekennzeichnet, dass besagtes Werkstück eine Gitterfeder oder Systemhaltefeder oder eine Schraube ist.
  18. Werkstück gemäß einem der Ansprüche 15 bis 17, dadurch gekennzeichnet, dass es aus einer Legierung basierend auf Nickel der Zusammensetzung in Gewichtsprozent: C ≤ 0,08%, Mn ≤ 0,35%, Si ≤ 0,35%, P ≤ 0,015%, S ≤ 0,015%, Ni = 50-55%, Cr = 17-21%, Co ≤ 1%, Al = 0,2-0,8%, Mo = 2,8-3,3%, Ti = 0,65-1,15%, B ≤ 0,006%, Cu ≤ 0,3%, Nb + Ta = 4,75-5,5%, der Rest Fe und unvermeidbare Verunreinigungen, die aus der Erstellung resultieren, realisiert ist.
  19. Werkstück gemäß Anspruch 15, dadurch gekennzeichnet, dass besagtes Werkstück ein Element des Kühlkreislaufs eines Kernreaktors ist.
  20. Werkstück gemäß Anspruch 19, dadurch gekennzeichnet, dass besagtes Werkstück eine Rohrleitung oder ein Brennelementführungsstab oder eine Feder oder ein Wärmetauscher oder eine Schraube oder ein Bolzen oder jedes andere Bauteil aus der Legierung basierend auf Nickel ist, das in Kontakt mit dem Wärmeträgermedium ist.
  21. Werkstück gemäß Anspruch 15, dadurch gekennzeichnet, dass es sich um ein Halbzeug handelt, von dem ausgehend Erzeugnisse mittels eines Verfahrens zum Formen oder mittels Bearbeitens oder mittels Zuschneidens realisiert werden können.
  22. Werkstück gemäß Anspruch 21, dadurch gekennzeichnet, dass es sich um eine Platte oder ein Band oder einen Draht oder eine Stange oder einen Rohling handelt.
EP07871802.0A 2006-12-29 2007-12-06 Verfahren für rissdesensibilisierung mittels legierungsumgebung auf nickelbasis, hauptsächlich für ein kernbrennstabbündel und für einen kernreaktor sowie aus derartig verarbeiteter legierung hergestelltes teil Active EP2126152B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR0611538A FR2910912B1 (fr) 2006-12-29 2006-12-29 Procede de traitement thermique de desensibilisation a la fissuration assistee par l'environnement d'un alliage a base nickel, et piece realisee en cet alliage ainsi traitee
PCT/FR2007/002006 WO2008081118A2 (fr) 2006-12-29 2007-12-06 Procede de traitement thermique de desensibilisation a la fissuration assistee par l'environnement d'un alliage a base nickel, notamment pour assemblage de combustible de reacteur nucleaire et pour reacteur nucleaire, et piece realisee en cet alliage ainsi traite

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR3150816A1 (fr) * 2023-07-07 2025-01-10 Framatome Procédé de fabrication d’un composant de réacteur nucléaire et composant de réacteur nucléaire ainsi obtenu

Families Citing this family (42)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE533124C2 (sv) * 2008-05-28 2010-06-29 Westinghouse Electric Sweden Spridare för kärnbränslestavar
JP2010138476A (ja) * 2008-12-15 2010-06-24 Toshiba Corp ジェットポンプビームおよびその製造方法
FR2941962B1 (fr) * 2009-02-06 2013-05-31 Aubert & Duval Sa Procede de fabrication d'une piece en superalliage a base de nickel, et piece ainsi obtenue.
US20120051963A1 (en) * 2010-08-30 2012-03-01 General Electric Company Nickel-iron-base alloy and process of forming a nickel-iron-base alloy
US9062354B2 (en) 2011-02-24 2015-06-23 General Electric Company Surface treatment system, a surface treatment process and a system treated component
DE102011106222A1 (de) * 2011-06-07 2012-12-13 Rwe Power Ag Dampferzeugerbauteil sowie Verfahren zur Herstellung eines Dampferzeugerbauteil
CA2839831C (en) * 2011-06-29 2016-12-13 Nippon Steel & Sumitomo Metal Corporation Producing method of heat-exchanger tube for steam generator for use in nuclear power plant and heat-exchanger tube for steam generator
DE102011054718B4 (de) * 2011-10-21 2014-02-13 Hitachi Power Europe Gmbh Verfahren zur Erzeugung einer Spannungsverminderung in errichteten Rohrwänden eines Dampferzeugers
US20130126056A1 (en) * 2011-11-18 2013-05-23 General Electric Company Cast nickel-iron-base alloy component and process of forming a cast nickel-iron-base alloy component
US20130287580A1 (en) * 2012-04-27 2013-10-31 General Electric Company Stress corrosion cracking resistance in superalloys
DE102012011162B4 (de) 2012-06-05 2014-05-22 Outokumpu Vdm Gmbh Nickel-Chrom-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
DE102012011161B4 (de) * 2012-06-05 2014-06-18 Outokumpu Vdm Gmbh Nickel-Chrom-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
US20140035211A1 (en) * 2012-08-01 2014-02-06 Baker Hughes Incorporated Corrosion-resistant resilient member
JP5743161B2 (ja) * 2012-09-24 2015-07-01 株式会社日本製鋼所 耐Ｍｇ溶損特性に優れた被覆構造材
US9377245B2 (en) 2013-03-15 2016-06-28 Ut-Battelle, Llc Heat exchanger life extension via in-situ reconditioning
US9540714B2 (en) 2013-03-15 2017-01-10 Ut-Battelle, Llc High strength alloys for high temperature service in liquid-salt cooled energy systems
KR101507898B1 (ko) * 2013-04-10 2015-04-08 한국원자력연구원 니켈계 초내열 합금 및 이의 제조방법
CN103866174B (zh) * 2013-06-06 2016-01-27 陕西钛普稀有金属材料有限公司 一种高强度镍钼镁三元合金及其制备工艺
CN103290298B (zh) * 2013-06-06 2016-02-10 陕西钛普稀有金属材料有限公司 一种钽铌钼镍镁合金及其制备工艺
CN103290297B (zh) * 2013-06-06 2015-07-15 陕西钛普稀有金属材料有限公司 一种含锆钼镁合金及其制备工艺
US10017842B2 (en) 2013-08-05 2018-07-10 Ut-Battelle, Llc Creep-resistant, cobalt-containing alloys for high temperature, liquid-salt heat exchanger systems
US9435011B2 (en) 2013-08-08 2016-09-06 Ut-Battelle, Llc Creep-resistant, cobalt-free alloys for high temperature, liquid-salt heat exchanger systems
CN103526124B (zh) * 2013-10-28 2015-10-21 江西省萍乡市三善机电有限公司 一种新型高耐热涡轮增压器密封环及其制备方法
US9683280B2 (en) 2014-01-10 2017-06-20 Ut-Battelle, Llc Intermediate strength alloys for high temperature service in liquid-salt cooled energy systems
DE102014001329B4 (de) 2014-02-04 2016-04-28 VDM Metals GmbH Verwendung einer aushärtenden Nickel-Chrom-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001330B4 (de) 2014-02-04 2016-05-12 VDM Metals GmbH Aushärtende Nickel-Chrom-Kobalt-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
EP3431222B1 (de) * 2014-04-04 2020-01-22 Special Metals Corporation Schweissgut sowie verfahren zur herstellung eines schweissguts
US9683279B2 (en) 2014-05-15 2017-06-20 Ut-Battelle, Llc Intermediate strength alloys for high temperature service in liquid-salt cooled energy systems
US9605565B2 (en) 2014-06-18 2017-03-28 Ut-Battelle, Llc Low-cost Fe—Ni—Cr alloys for high temperature valve applications
CN106498236B (zh) * 2016-10-26 2017-11-10 济宁市北辰金属材料有限公司 一种玻璃纤维生产用合金坩埚及其制备方法
CN106756246B (zh) * 2016-10-31 2019-04-19 重庆材料研究院有限公司 一种核场废液处理用耐腐蚀合金材料及其制备方法
EP3636785B1 (de) * 2017-06-08 2021-10-13 Nippon Steel Corporation Rohr aus ni-basierter legierung in nuklearer qualität
CN107322003B (zh) * 2017-06-29 2019-07-09 厦门朋鹭金属工业有限公司 一种制备低杂质含量钨粉的工业方法
TWI657147B (zh) * 2017-12-20 2019-04-21 國家中山科學研究院 一種高應力鎳基合金
CN108441707B (zh) * 2018-03-30 2020-06-23 四川六合特种金属材料股份有限公司 一种高强度含钨系镍基高温合金材料及其制备方法和应用
DE102020106433A1 (de) 2019-03-18 2020-09-24 Vdm Metals International Gmbh Nickel-Legierung mit guter Korrosionsbeständigkeit und hoher Zugfestigkeit sowie Verfahren zur Herstellung von Halbzeugen
CN110273085B (zh) * 2019-04-15 2022-01-07 上海大学 反应堆乏燃料贮运用富钆镍基合金材料及其制备方法
CN110396624B (zh) * 2019-08-13 2021-04-09 上海大学 核屏蔽用富硼镍钨基合金材料及其制备方法
CN110373573B (zh) * 2019-08-13 2021-06-04 上海大学 核屏蔽用富钆镍钨基合金材料及其制备方法
CN110643858B (zh) * 2019-11-08 2020-10-30 中国科学院上海应用物理研究所 镍基高温合金抗碲腐蚀性能提升方法及镍基高温合金
CN114247899A (zh) * 2021-12-13 2022-03-29 金川集团股份有限公司 不产生裂纹的SLM成形Inconel 738合金的热处理方法
CN119082553B (zh) * 2024-11-08 2025-03-25 上海核工程研究设计院股份有限公司 一种耐辐照脆化镍基合金及其制造方法与应用

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3368883A (en) * 1965-07-29 1968-02-13 Du Pont Dispersion-modified cobalt and/or nickel alloy containing anisodiametric grains
CN1007910B (zh) * 1987-05-19 1990-05-09 机械工业委员会哈尔滨焊接研究所 新型代钴镍基耐磨堆焊合金
US5047093A (en) * 1989-06-09 1991-09-10 The Babcock & Wilcox Company Heat treatment of Alloy 718 for improved stress corrosion cracking resistance
US5164270A (en) 1990-03-01 1992-11-17 The United States Of America As Represented By The Department Of Energy Iron-based alloys with corrosion resistance to oxygen-sulfur mixed gases
US5184270A (en) * 1990-06-13 1993-02-02 Abb Power T&D Company, Inc. Internal arc gap for secondary side surge protection and dissipation of a generated arc
US5346563A (en) * 1991-11-25 1994-09-13 United Technologies Corporation Method for removing sulfur from superalloy articles to improve their oxidation resistance
US5244515A (en) * 1992-03-03 1993-09-14 The Babcock & Wilcox Company Heat treatment of Alloy 718 for improved stress corrosion cracking resistance
JP3094778B2 (ja) * 1994-03-18 2000-10-03 株式会社日立製作所 軽水炉用燃料集合体とそれに用いられる部品及び合金並びに製造法
US5922148A (en) * 1997-02-25 1999-07-13 Howmet Research Corporation Ultra low sulfur superalloy castings and method of making
US6332937B1 (en) * 1997-09-25 2001-12-25 Societe Nationale d'Etude et de Construction de Moteurs d'Aviation “SNECMA” Method of improving oxidation and corrosion resistance of a superalloy article, and a superalloy article obtained by the method
JP2000053492A (ja) 1998-08-07 2000-02-22 Hitachi Ltd 単結晶物品とその製造方法及び用途
JP2001107196A (ja) * 1999-10-07 2001-04-17 Sumitomo Metal Ind Ltd 耐溶接割れ性と耐硫酸腐食性に優れたオーステナイト鋼溶接継手およびその溶接材料
JP4042362B2 (ja) * 2000-08-11 2008-02-06 住友金属工業株式会社 Ｎｉ基合金製品とその製造方法
EP1777313B1 (de) * 2004-06-30 2012-08-01 Sumitomo Metal Industries, Ltd. Rohr aus ni-basislegierungsmaterial und herstellungsverfahren dafür
JP4304499B2 (ja) * 2004-10-13 2009-07-29 住友金属工業株式会社 原子力プラント用Ｎｉ基合金材の製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
SARIOGLU S ET AL: "The Effects of reactive element additions, sulfur removal and specimen thickness on the oxidation behaviour of alumina-forming NI-and-Fe-Base alloys", MATERIALS SCIENCE F, TRANS TECH PUBLICATIONS LTD- SWITZERLAND, CH, vol. 251-254, 1 May 1996 (1996-05-01), pages 405 - 412, XP009086234, ISSN: 0255-5476 *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR3150816A1 (fr) * 2023-07-07 2025-01-10 Framatome Procédé de fabrication d’un composant de réacteur nucléaire et composant de réacteur nucléaire ainsi obtenu
WO2025012095A1 (fr) * 2023-07-07 2025-01-16 Framatome Procédé de fabrication d'un composant de réacteur nucléaire et composant de réacteur nucléaire ainsi obtenu

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WO2008081118A3 (fr) 2008-08-21
US8470106B2 (en) 2013-06-25
JP5268942B2 (ja) 2013-08-21
KR20090110298A (ko) 2009-10-21
US20100116383A1 (en) 2010-05-13
KR20140114455A (ko) 2014-09-26
ES2771352T3 (es) 2020-07-06
WO2008081118A2 (fr) 2008-07-10
FR2910912A1 (fr) 2008-07-04
ZA200904415B (en) 2010-10-27
TW200840877A (en) 2008-10-16
JP2010515041A (ja) 2010-05-06
CN101600814B (zh) 2011-11-16
EP2126152A2 (de) 2009-12-02
FR2910912B1 (fr) 2009-02-13

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