EP0067526B1 - Turbine à vapeur fonctionnant à temperatures et pressions très élevées - Google Patents

Turbine à vapeur fonctionnant à temperatures et pressions très élevées Download PDF

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Publication number
EP0067526B1
EP0067526B1 EP19820302419 EP82302419A EP0067526B1 EP 0067526 B1 EP0067526 B1 EP 0067526B1 EP 19820302419 EP19820302419 EP 19820302419 EP 82302419 A EP82302419 A EP 82302419A EP 0067526 B1 EP0067526 B1 EP 0067526B1
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Prior art keywords
alloy
steam turbine
temperature
blades
rotor shaft
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German (de)
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EP0067526A1 (fr
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Katsumi Iijima
Masayuki Sukekawa
Seishin Kirihara
Norio Yamada
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Hitachi Ltd
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Hitachi Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

Definitions

  • This invention relates to steam turbines, and especially is concerned with a superhigh temperature and pressure steam turbine operating at a steam temperature of 600° to 650°C and under a steam pressure of 4000 to 5000 psi. (about 28000 to 35000 kPa.
  • Austenitic alloys are considered suitable from the point of view of strength as materials for the rotor and rotor blades operating under conditions of a steam pressure exceeding 4000 psi (about 28000 kPa) and a steam temperature in the range over 600°C.
  • these alloys carry the risks that, since various deposit phases are precipitated at high temperature, embrittlement thereof may be accelerated and their strength may be markedly lowered at elevated temperature.
  • GB-A-912,814 discloses an austenitic nickel-chromium-iron-base alloy which is said to be useful for gas turbine applications; mentioned are turbine wheels, buckets and bolting and structural applications (but not rotor shafts and blades).
  • the amount of manganese present is below 0.50%, and use of high manganese content is discouraged.
  • the 1000 hour creep rupture strength of the material is not given.
  • An object of this invention is to provide steam turbine including a turbine shaft having superior thermal fatigue resistant property at a -main steam temperature of 600° to 650°C.
  • Another object is to provide a superhigh temperature and pressure steam turbine of high reliability, particularly a steam turbine of the type described including a rotor shaft formed of austenitic forged steel-having high strength at elevated temperature, high ductility- atelavated temperature and low thermal embrittlement under the steam condition of a temperature range between 600°C and 650°C.
  • Still another object is to provide a steam turbine having a rotor shaft and rotor blades of high thermal fatigue resistant property under the steam condition .of a temperature range between 600° and 650°C.
  • the invention is set out in claim 1.
  • the blade sections of the rotor shaft are preferably equidistantly located axially of the rotor shaft in the casing and are preferably unsymmetrical at the center position with respect to the axial direction.
  • the outer casing member preferably has a substantially spherical external shape, and is preferably formed of Cr-Ni austenitic cast steel or Cr-Mo-V cast steel having a bainite structure.
  • the inner casing member is preferably formed of Cr-Ni austenitic cast steel.
  • the rotor shaft is preferably formed of an alloy which consists of the balance being iron plus unavoidable impurities. More preferably 0.2-0.3% vanadium is present.
  • the rotor blades of the superhigh temperature and pressure turbine according to the invention are preferably made of an alloy consisting by weight of the following elements in amounts within the following respective ranges the balance Fe and unavoidable impurities, and having a microstructure in which a y' phase is precipitated in austenite matrix.
  • the alloy of the rotor blades consists by weight of the balance being iron plus unavoidable impurities. More preferably 0.2 ⁇ 0,3% vanadium is present.
  • the alloy of the rotor shaft and also the alloy of the rotor blades of the superhigh temperature and pressure steam turbine according to the invention preferably have, calculated from the aforesaid chemical compositions, the following Ni equivalent and Cr equivalent:
  • the carbon content in the material of the rotor shaft that increases strength at elevated temeprature without reducing toughness nor thermal embrittlement is less than 0.04%, preferably 0.015 to 0.03%, and the carbon content of the preferred material of the rotor blades is 0.01-0.1 %, preferably between 0.04 and 0.07%.
  • the amount in the alloy for the rotor shaft 67 is chosen in the range 0,5 to 1,50%, while for the rotor blades it is preferably not more than 2%, more preferably between 0.5 and 1.5%.
  • This element is an important component for improving high temperature mechanical strength of the steel according to the invention, particularly creep rupture strength and thermal fatigue life thereof. More specifically, this element is conducive to formation of a stable austenite structure and increased high . temperature strength. However, in view of its high cost and the reduction of high temperature ductility and yield strength of the steel when its amount is too high, the amount of Ni present is limited between 20 and 30%, preferably between 24 and 28%.
  • this element is a deoxidizing component necessary for production.
  • the amount present is over 1.5%, however, the forgeability of the steel diminishes and its high temperature toughness is reduced.
  • the upper limit for the preferred blade alloy is 1.5 wt%, the amount being preferably between 0.3 and 1%.
  • the range 0.3 to 1% is chosen.
  • This element improves creep rupture strength by strengthening the austenite matrix and forming a carbide.
  • the steel has its high temperature ductility reduced and its workability deteriorates when the amount of the element is too large.
  • the amount is limited to between 0.5 and 3 wt%, preferably between 1 and 2%.
  • This element is an important component for improving the high temperature oxidization property of the material according to the invention. As shown in Fig. 1(b), no satisfactory effect is achieved if the amount is under 10%. When the amount is over 20%, embrittlement increases after prolonged holding at elevated temperature. The amount is thus preferably between '14 and 17%.
  • this element Besides being used as a deoxidizing agent, this element has the effect of hardening alloys by the precipitation thereof. However, when its amount exceeds 3%, the element reduces the ductility and toughness of the steel and accelerates notch deterioration. To increase the high temperature strength of the steel, it is necessary that the amount of this element be not less than 0.5%. Preferably the amount is between 1.5 and 2.5%. For the alloy of the blades, the range preferred is 1.5 to 3%.
  • Aluminium is added as a deoxidizing agent in the amount of 0.1-0.5%, preferably in the amount of 0.15-0.4%.
  • This element is combined with titanium to cause precipitation of an intermetallic compound, to thereby increase high temperature strength.
  • the amount is too great, it tends to reduce strength.
  • the amount thereof is limited to between 0.1-0.5%.
  • This element has the effects of markedly strengthening grain boundary and providing high temperature ductility.
  • workability deteriorates when the amount is too large.
  • the amount is limited to between 0.002 and 0.01 %, preferably between 0.004 and 0.008%.
  • the amount is in the range 0.004 to 0.008%.
  • This element is optionally added to improve creep strength. When the amount thereof is below 0.05%, no satisfactory effect is achieved. When the amount is over 0.5%, however, ductility and toughness are both adversely affected. The amount is preferably between 0.2 and 0.3%.
  • Fig. 7a shows the relation between the nickel equivalent (% Ni+30x% C+0.5x% Mn) regarding an austenite heat resisting steel now in use and the 1000 hour creep rupture strength obtained at 650°C. As shown, an increase in the nickel equivalent is accompanied by an improvement in creep rupture strength. This relation tends to be saturated when the nickel equivalent is about 35%. If the 1000 hour creep rupture strength at 650°C used as a target is made to agree with the scatter band value of 26-34 kg/mm 2 (1000 hour creep rupture strength at 550°C) now used for the currently used material, then the optimum value of the nickel equivalent is between 23 and 29%. (1 kg/mm 2 can be written as 1 MPa).
  • FIG. 7b shows the relation between the chromium content and the increment for high temperature oxidation.
  • Fig. 7b shows that the chromium content should be not less than 12% if its addition is to have any effect in oxidization resistance at elevated temperature.
  • Fig. 7c shows the result obtained with the relation shown in Fig. 7b and the optimum range of the aforesaid nickel equivalent as inserted in Shefla's diagram.
  • the upper limit of the chromium equivalent is set corresponding to the nickel equivalent on condition that a stable austenite structure is obtained, then the value is 7/10x(% nickel equivalent)+9 (see Fig. 7c) according to Shefla's diagram.
  • the hatching in Fig. 7c indicates the nickel equivalent and chromium equivalent as limited by the invention.
  • the alloys used in the present invention it is preferred to effect melting by use of argon-oxygen blowing decarburization process or vacuum decarburization process.
  • Fig. 1 is a sectional view showing the essential portions of one embodiment of the superhigh temperature and pressure steam turbine in conformity with the invention, in which steam is introduced through a main steam line 1 into the turbine and is jetted in a predetermined direction by static blades 3 attached to an inner casing member 2 to thereby rotate rotor blades 5 mounted on a rotor shaft 4. After doing work, the steam flows through a gap between an outer casing member 6 and the inner casing member 2 and then is exhausted through a cooled steam outlet port 7, an exhaust outlet port 8 and an auxiliary exhaust outlet port 9. The exhausted steam is forwarded to a next steam turbine operating at a lower temperature. 10 is the center of each bearing of the rotor shaft 4. 11 and 12 are a gland and a intermediate gland leak outlet port respectively. 13 is a nozzle box. Arrows indicate the direction of flow of the steam.
  • Table 1 shows the chemical composition of alloys for rotor shafts used in experiments. Alloys 1 to 3 are according to the present invention. Alloy 4 is for comparison. Each of the alloys 1 to 4 is prepared by the steps of vacuum arc melting, forging, solid-solution treatment of holding it at 980°C for one hour with water-cooling thereafter, and aging treatment of holding at 720°C for 16 hours with air-cooling being effected thereafter, while each of the conventional alloys for comparison is prepared by the steps of vacuum are melting, forging and succeeding necessary treatments shown hereinbelow.
  • the alloys used in the present invention have a microstructure in which a y' phase is precipitated in the austenite matrix.
  • Conventional Cr-Mo-V steel serving as a comparative material was cooled by air-blowing after heating at 970°C for 15 hours, and then reheated at 670°C for 48 hours before being cooled in the furnace.
  • 12 Cr steel also serving as another comparative material was cooled by spraying of water in atomized particles after heating at 1050°C for 24 hours, and then subjected to tempering at 650°C for 20 hours. These steel alloys were subjected to V-notch Charpy impact tests and creep rupture tests.
  • Fig. 2 shows the results of impact tests conducted on the influences of the amount of C on thermal embrittlement by heating at 650°C for 1500 hours.
  • the results show that, whereas absorbed energy of non-heat treated blanks is substantially constant irrespective of the amount of C, the absorbed energy reduces as the amount of C increases in the material heated at 650°C for 1500 hours, showing a marked thermal embrittlement in material with high C content.
  • the values of absorbed energy at 20°C for 12 Cr steel and Cr-Mo-V steel which are now in use for producing rotors are specified as not less than 1.1 kg-m and 0.69 kg-m respectively.
  • the thermal embrittlement resistant property of each alloy used as a material of the turbine shaft in the present invention is larger than those of the conventional 12% Cr steel and Cr-Mo-V steel.
  • Fig. 3 shows an operation pattern of the severest condition for conventional steam turbines that is operated at a steam temperature of 566°C, that is, the starting-up and shutting-down of the turbine is repeated every 12 hours.
  • the rotor shaft would be subjected to harsh low cycle fatigue due to high stress at the time of startup and shutdown as shown.
  • the rotor shaft unlike the rotor blades, would be subjected to harsh low cycle fatigue due to the combined actions of thermal stress and centrifugal stress because a rise in temperature is gradual in the rotor. Also, it would be subjected to creep due to centrifugal forces in steady-state operation.
  • working stress represents thermal stress combined with centrifugal stress.
  • Table 2 shows the results of tension tests, creep rupture tests and low cycle fatigue tests conducted on the steels 1 and 2 according to the invention at 650°C and on the steel of the prior art at 550°C. It will be seen in the table that the material according to the invention is equal to or higher than the Cr-Mo-V steel in tensile strength and 0.2% yield strength, and that the rate of elongation thereof is 1.5 to 1.75 times as high as in the Cr-Mo-V steel. Creep rupture strength is 1.1 to 1.20 times as high in the material according to the invention as in the Cr-Mo-V steel and low cycle fatigue is equal to or slightly higher in the former than in the latter in spite of the difference of test temperature.
  • the results of the low cycle fatigue tests represent the number of repetitions continued until rupture occurs at a strain rate of 0.1 %/second and strain amounts of 1.0% and 0.65% without holding of the strain (that is, in the same manner as shown in Fig. 4c).
  • the material according to the invention which is used at a temperature of 650°C meets requirements regarding mechanical strength required in the case of Cr-Mo-V steel used at present at 550°C.
  • the material described above can be used for forming the rotor shaft of a superhigh temperature and pressure steam turbine operating at a steam temperature of 600°-650°C and under a steam pressure of 4000-5000 psi (about 28000 to 35000 kPa).
  • Table 3 shows the chemical composition (wt%) of various materials for forming the rotor blades used in the super-high temperature and pressure steam turbine according to the preferred aspect of the invention.
  • Each material has been obtained by performing vacuum arc melting, forging, and grain size regulation into a range of ASTM G.S. 2.5 ⁇ 4 was effected by holding it at 1050°C for 3 hours. Then each material was water-cooled to room temperature in the same manner as in Example 1 after having been subjected to solid solution treatment of holding it at 899°C for 2 hours. Then, each material was subjected to aging treatments of two steps, i.e.
  • the first step was holding it at 760°C for 16 hours with air-cooling thereafter and the second step was holding it at 718°C for 6 hours with air-cooling thereafter.
  • the blanks obtained by processing the materials through the aforesaid treatments had a microstructure having a y' phase precipitated in the austenite matrix.
  • the blanks were machined to provide test pieces of predetermined dimensions.
  • the blades of a steam turbine are directly subjected to the jetted steam, so that their temperatures rise relatively quickly after the steam turbine is actuated and becomes equal to that of steam. Meanwhile a rise in the temperature of the rotor shaft is relatively slow after the commencement of actuation of the steam turbine because it has a high thermal capacity and austenite steel has a low thermal conductivity.
  • the relatively large difference in temperature between the blades and rotor shaft exists for a substantial period of time.
  • the working stress (thermal stress plus centrifugal stress) to which the rotor shaft is subjected is very high at starting-up or shutting-down (or when transferring to idling) as shown in Fig. 3, with the result that the thermal fatigue suffered by the blades is relatively lower than that suffered by the rotor shaft.
  • the amount of C for the materials of the blades is limited between 0.01 and 0.1 %, preferably between 0.04 and 0.07%.
  • Fig. 4a shows a conceptual pattern of a relation between temperature and strain (stress) to which the surface of the rotor is subjected in the steam turbine of superhigh temperature and pressure according to the invention having the blades referred to hereinabove and the rotor shaft described by referring to Example 1.
  • the operation conditions shown in Fig. 4a were converted to a trapezoidal strain cycle (constant temperature) with strain-holding (Fig.- 4b), and a tension-compression triangular wave form (constant temperature) without -strain-holding- (Fig. 4c).
  • The. aforesaid conversion has been made on the basis of the hypothesis that there is a correlation between a thermal fatigue phenomenon (varying temperature) and a low cycle fatigue phenomenon (constant temperature).
  • Fig. 5 is a diagram showing the results of high temperature low cycle fatigue tests conducted by controlling strain or gauge length at a strain rate of 0.1 %/sec and at a temperature of 650°C. As shown, it will be seen that the materials of the invention containing 0.002-0.008% B has about twice as long service life as a conventional material containing no B in a low cycle region having a strain range of 0.5-1.2%, indicating that the addition of B has the effect of improving thermal fatigue resistant property.
  • Fig. 6 shows the influences exerted on fatigue life by the amount of B at a temperature of 650°C and a strain speed of 0.1%/sec in a strain region of 1.0%.
  • fatigue life has a peak in the vicinity of 0.006% B and is about twice as long as that of material containing B in an amount outside the range of the invention.
  • the preferred blades for steam turbines according to the invention have a superior thermal fatigue resistant property and a prolonged service life.
  • Materials were subjected to vacuum arc melting, forging and regulating of grain size under the same conditions as described in Example 1. Then the materials were subjected to solid solution treatment and aging under the heat treating conditions shown in Table 7, and machined to produce materials for blades and rotor shafts.
  • the materials Nos. 10 and 11 are those used for producing blades, and the materials Nos. 12 and 13 are those used for producing rotor shafts.
  • Tables 5 and 6 show the results of creep rupture tests and fatigue tests conducted on these materials, respectively.
  • the strain and stress caused on the surfaces of the rotors when a steam turbine is operated are such that transient compressive (tensile) strain due to thermal stress occurs at the time of starting-up (or shutting down) at a point A, and tensile stress acts due to centrifugal forces when the operation proceeds to a steadystate condition, so that the operation condition becomes such state as shown at points B and C in the steadystate. Therefore the strain cycle was assessed experimentally from low cycle fatigue based on the triangular waves for the starting-up and shutting-down and from creep rupture strength for steadystate operation.
  • Fig. 8 shows the results of extrapolation of the creep rupture strength of 105 hours conducted by the Rollson-Mirror process.
  • the materials Nos. 10, 11, 12 and 13 covered by the claims of the invention have strength of about 133 MPa at 650°C which is similar to mean creep rupture strength of 127 MPa of the conventional Cr-Mo-V steel tested at 550°C for comparison.
  • Fig. 9 shows the results of high temperature low cycle fatigue tests effected by controlling strain of gauge length, at a strain rate of 0.1 %/sec. The results show that in the entire strain range the fatigue life of the materials according to the present invention at 650°C is equal to or longer than that of the Cr-Mo-V steel at 550°C.
  • Fig. 10 is a microscopic photograph at a magnification 1000x of the No. alloy having a microstructure in which a y' phase is precipitated in the austenite matrix.
  • the alloy according to the invention has high temperature strength required of the materials for the blades and the rotor operating at a steam temperature of 600°-650°C and is suitable for use as materials for the rotor blades and the rotor.
  • Figs. 11 and 12 show a relation between aging temperature and tensile strength and another relation between aging temperature and creep rupture time at 650°C regarding the above-described alloys of the present invention, respectively.
  • low aging temperature not more than 740°C is preferred for obtaining improved creep rupture strength and tensile strength.
  • the amount of carbon does not have much influence regarding the enhancement of mechanical strength; however, the lower the amounts carbon and titanium in the alloys, the higher the elongation and reduction of area thereof become.
  • Table 9 shows the chemical composition of another alloy for the rotor shaft 4 of a superhigh temperature and pressure steam turbine according to the invention.
  • Raw materials for constituting the aforesaid composition were subjected to vacuum induction melting under a vacuum of 10 -3 to produce electrodes of about 1000 mm in diameter.
  • the electrodes were remelted by an electro-slag-remelting process (ESR) by use of flux consisting of CaF 2 of 55%, A1 2 0 3 of 35% and Ti0 2 of 10% and cast into columnar ingots.
  • ESR electro-slag-remelting process
  • the ingots were diffusion-annealed at a temperature of 1100°-1500°C and forged at a temperature below 1050°C to produce a columnar blank of 850 mm in diameter and 6000 mm in length.
  • the blank was held for 3 hours at a temperature of 1050°C to control the grain size into a range of ASTM G.S. 2.5-4 while rotating the blank at a rate of 3 times per one minute.
  • the blank After subjecting the blank to solution treatment by holding same at a temperature in the range between 900 and 1000°C for 1 hour, it was water-cooled by jetting water thereagainst while vertically holding and rotating it at a rate of three revolutions per minute to room temperature. Thereafter, the blank was held at a temperature between 700° and 730°C for 16 hours to effect aging while rotating it in the same manner, to provide a microstructure in which a y' phase is precipitated in austenite matrix. The blank was then machined to obtain a rotor shaft having predetermined dimensions shown in Fig. 13. Specimens for experiments were taken from the left hand end of the rotor shaft as shown in Fig. 13 and were subjected to the tests of tensile strength and creep rupture strength, with the result that there were obtained strength and elongation both substantially similar to those of the specimen No. 17 described above.
  • Table 10 shows the chemical composition (wt%) of a blade used in a superhigh temperature and pressure steam turbine of the present invention.
  • Raw materials for constituting this chemical composition were subjected to vacuum induction melting to produce electrodes (600 mm in diameter) for ESR.
  • the electrodes were remelted by ESR process by use of flux consisting of CaF 2 of 50%, CaO of 25%, Ti0 2 of 15% and A1 2 0 3 of 10%, and the molten metal was cast into blanks. Then, each of the blanks was heat-treated to control the grain size thereof. After that, there was effected the solution heat treatment of holding the blank at 899°C for 2 hours and of water-cooling thereafter.
  • the blank was subjected to aging treatment of two steps, i.e., in the first step the blank was held at 760°C for 16 hours with air-cooling being effected thereafter and in the second step the blank was held at 718°C for 6 hours with air-cooling thereafter, so that there was obtained a blank having microstructure in which y' phase is precipitated in austenite matrix.
  • Such blank was subjected to mechanical working to obtain the blade having predetermined dimensions. Specimens were picked from the blade, which specimens were subjected to the test of evaluating tensile strength, creep rupture strength and high temperature lower cycle fatigue resistant property, with the result that there were obtained values in a degree approximately similar to those of the specimen No. 1 shown in Table 2.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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Claims (5)

1. Turbine à vapeur fonctionnant à températures et pressions très élevées comprenant un carter, des aubes dans ledit carter pour recevoir des jets de vapeur pour provoquer la rotation, et un arbre de rotor supportant lesdites aubes en vue de leur rotation, ledit carter comportant un élément de carter interne muni d'aubes fixes fixées à lui pour guider les jets de vapeur et un élément de carter externe enfermant l'élément de carter interne, ledit arbre de rotor étant constitué d'un alliage forgé formé des éléments suivants dont les quantités exprimées en poids se trouvent dans les plages suivantes:
Figure imgb0032
le reste étant du Fe et des impuretés inévitables, et possédant-une microstructure dans laquelle une phase y' est précipitée dans une matrice d'austénite, l'alliage ayant été soumis à un traitement de vieillissement, ce par quoi le rotor possède une résistance au fluage en 1000 heures de 26-34 kg/mm2 à 650°C.
2. Turbine à vapeur selon la revendication 1, dans laquelle lesdites aubes sont constituées d'un alliage comprenant les éléments suivants dont les quantités exprimées en poids se trouvent dans les plages suivantes:
Figure imgb0033
le reste étant du Fe et des impuretés inévitables et possédant une microstructure dans laquelle une phase y' est précipitée dans une matrice d'austénite.
3. Turbine à vapeur selon la revendication 1 ou la revendication 2 dans laquelle l'équivalent Ni dudit alliage dont est constitué l'arbre de rotor est compris entre 23 et 29, l'équivalent Ni étant
Figure imgb0034
et son équivalent Cr donné par
Figure imgb0035
est compris entre
Figure imgb0036
l'alliage étant un acier austénitique forgé.
4. Turbine à vapeur selon l'une quelconque des revendications 1 à 3, dans laquelle ledit alliage dudit arbre de rotor est constitué en poids de:
Figure imgb0037
le reste étant du fer plus des impuretés inévitables.
5. Turbine à vapeur selon les revendications 2 ou 3, dans laquelle ledit alliage desdites aubes est constitué en poids de:
Figure imgb0038
le reste étant du fer plus des impuretés inévitables.
EP19820302419 1981-05-13 1982-05-12 Turbine à vapeur fonctionnant à temperatures et pressions très élevées Expired EP0067526B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP7083481A JPS57188656A (en) 1981-05-13 1981-05-13 Rotor shaft for steam turbine
JP70834/81 1981-05-13

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Publication Number Publication Date
EP0067526A1 EP0067526A1 (fr) 1982-12-22
EP0067526B1 true EP0067526B1 (fr) 1986-11-26

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DE (1) DE3274468D1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7238005B2 (en) 2003-07-30 2007-07-03 Kabushiki Kaisha Toshiba Steam turbine power plant

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3424314B2 (ja) * 1994-02-24 2003-07-07 大同特殊鋼株式会社 耐熱鋼
US8435435B2 (en) * 2006-03-30 2013-05-07 Zf Friedrichshafen Ag Method of making a multilayered duplex material article
DE102020213539A1 (de) * 2020-10-28 2022-04-28 Siemens Energy Global GmbH & Co. KG Legierung, Rohteil, Bauteil aus Austenit sowie ein Verfahren

Family Cites Families (6)

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Publication number Priority date Publication date Assignee Title
FR1087022A (fr) * 1953-09-08 1955-02-18 Armco Int Corp Procédé de fabrication d'alliages et produits en résultant
US3065067A (en) * 1959-01-21 1962-11-20 Allegheny Ludlum Steel Austenitic alloy
GB965585A (en) * 1961-01-23 1964-07-29 Carpenter Steel Co Age-hardenable austenitic chromium-nickel-titanium steel
GB999439A (en) * 1962-05-10 1965-07-28 Allegheny Ludlum Steel Improvements in or relating to an austenitic alloy
FR2225536B1 (fr) * 1973-04-12 1976-04-09 Creusot Loire
US4129462A (en) * 1977-04-07 1978-12-12 The United States Of America As Represented By The United States Department Of Energy Gamma prime hardened nickel-iron based superalloy

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7238005B2 (en) 2003-07-30 2007-07-03 Kabushiki Kaisha Toshiba Steam turbine power plant
US7850424B2 (en) 2003-07-30 2010-12-14 Kabushiki Kaisha Toshiba Steam turbine power plant

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JPS57188656A (en) 1982-11-19
EP0067526A1 (fr) 1982-12-22

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