EP2423342A1 - Geschmiedete Legierung für Dampfturbinen und Dampfturbinenrotor damit - Google Patents

Geschmiedete Legierung für Dampfturbinen und Dampfturbinenrotor damit Download PDF

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Publication number
EP2423342A1
EP2423342A1 EP11178329A EP11178329A EP2423342A1 EP 2423342 A1 EP2423342 A1 EP 2423342A1 EP 11178329 A EP11178329 A EP 11178329A EP 11178329 A EP11178329 A EP 11178329A EP 2423342 A1 EP2423342 A1 EP 2423342A1
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EP
European Patent Office
Prior art keywords
steam turbine
heat treatment
crystal grain
forged alloy
grain size
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Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP11178329A
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English (en)
French (fr)
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EP2423342B1 (de
Inventor
Hironori Kamoshida
Shinya Imano
Jun Sato
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Hitachi Ltd
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Hitachi Ltd
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Publication of EP2423342A1 publication Critical patent/EP2423342A1/de
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Publication of EP2423342B1 publication Critical patent/EP2423342B1/de
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
    • F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
    • F01D5/12—Blades
    • F01D5/28—Selecting particular materials; Particular measures relating thereto; Measures against erosion or corrosion
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2220/00—Application
    • F05D2220/30—Application in turbines
    • F05D2220/31—Application in turbines in steam turbines

Definitions

  • the present invention relates to a NiFe-based forged alloy used for components of a steam turbine (for example, rotor) operating at a main steam temperature of 675°C or higher.
  • a Ni-based alloy (USC141) shown in JP-09-157779-A has a low linear expansion coefficient among Ni-based alloys and also has a good creep strength among candidate materials intended to be used for steam turbines of 700°C class.
  • an Fe-based alloy shown in JP-2005-2929-A is a material in which manufactuability for large steel ingot and creep strength are made compatible by reducing Nb as a segregation element and increasing Al as a ⁇ ' phase forming element. Therefore, the Fe-based alloy is expected for application to large components of steam turbines, for example, rotors.
  • Characteristics of materials are greatly different depending on the material structure even if the material composition is identical. As the crystal grain size increases, a problem occurs that the creep strength increases but the fatigue property decreases.
  • the present invention intends to provide a forged alloy for a steam turbine of good creep property and fatigue property, and a rotor for the steam turbine using the forged alloy described above.
  • a forged alloy for a steam turbine according to the invention comprises 15 to 45 wt% of Fe, 14 to 18 wt% of Cr, 1.0 to 1.8 wt% of Ti, 1.0 to 2.0 wt% of Al, 1.25 to 3.0 wt% of Nb, 0.05% or less of C+N and the balance of Ni, wherein the crystal grain size number after heat treatment of the forged alloy is 0 to 2, and the heat treatment includes a plurality of solution heat treatments in different temperature ranges.
  • the present invention can provide a forged alloy for a steam turbine of good creep property and fatigue property, and a rotor for the steam turbine using the forged alloy described above.
  • the present inventors have investigated the effect of the crystal grain size (crystal particle diameter) of materials on the creep strength and the fatigue property.
  • the crystal particle diameter (crystal grain size) is made coarser by increasing the solution temperature in a ⁇ ' phase than usual.
  • the creep strength and the fatigue property were investigated by using NiFe forged alloys with the crystal grain size Numbers of 0 to 2. As a result, it has been found that creep rupture time is increased about six times as usual under the same creep condition. Further, no remarkable lowering has been observed for the fatigue property under identical low cycle fatigue test conditions.
  • NiFe-based forged alloy according to this invention will be described.
  • Al of 1.0% by weight or more needs to be incorporated for compensating lowering of strength due to decrease in Nb and improving the structural stability.
  • the Al content is defined as 2.0 wt% or less.
  • Ti is an element for precipitating the ⁇ ' phase and stabilizing Ni 3 Ti at high temperatures, excess content is not preferred and it is defined as 1.0 to 1.8 % by weight.
  • C and N are defined as 0.05% by weight or less as the total for C and N in order to suppress refinement of crystal grains attributable to increase of NbC as described above.
  • Fe is defined as 15 to 45% by weight in order to suppress precipitation of ⁇ phase and ⁇ phase which are deleterious precipitation phases.
  • Nb is an element for stabilizing the ⁇ ' phase. Since insufficient content of Nb cannot provide effective strength whereas excessive content results in worsening of segregation property, Nb is defined as 1.25 to 3.0% by weight.
  • Cr may promote precipitation of the ⁇ phase as a deleterious precipitation phase when contained in excess but it is defined as 14 to 18% by weight for obtaining oxidation resistance.
  • the NiFe-based super alloy of the invention comprises the ingredients described above and the balance of Ni.
  • elements present in the starting material or intruding in the production process may sometimes be contained as impurities. Since intrusion of some impurities cannot be avoided, they are referred to as inevitable impurity.
  • the NiFe-based forged alloy comprising the composition described above is subjected to a 2-step solution heat treatment.
  • a solution heat treatment at a first step is performed at 1020°C to 1100°C for 1 to 10 hours.
  • 1020°C coarsening of crystal grains does not proceed, or long-time heat treatment is required, which is not practical.
  • 1100°C the coarsening rate of the crystal grains increases, which makes control for the crystal particle size difficult.
  • the solution heat treatment at a second step is performed at 965°C to 995°C for 1 to 4 hours.
  • the temperature range may be at such a temperature as applied generally as the solution heat treatment for Ni-based alloy of this type.
  • the temperature is defined to the range described above, with an aim of precipitating only carbides without precipitation of the ⁇ ' phase and preventing carbides from continuously precipitating at the crystal grain boundary upon age-hardening heat treatment.
  • the temperature for the age-hardening heat treatment may be a temperature at which the age-hardening heat treatment is applied generally for the NiFe-based forged alloys of this type.
  • the age-hardening treatment is performed preferably twice in which the first step is performed at 825 to 855°C within 10 hours and the second treatment is performed at a lower temperature of 710 to 740°C for 10 to 48 hours.
  • the crystal grain size (crystal particle diameter) after the heat treatment is a crystal grain size number in Japanese Industrial Standards (JIS), which is in a range of 0 to 2 and, preferably, 1 to 2.
  • JIS Japanese Industrial Standards
  • a smaller value means a larger crystal grain size.
  • VIM vacuum induction melting
  • ESR electroslug remelting
  • Table 1 shows the composition of a test specimen.
  • Table 1 Composition of Test Specimen (wt%) C Si Mn P S Ni Cr Al Ti Nb Fe N B 0.02 0.05 0.02 ⁇ 0.003 0.0003 40.90 15.49 1.34 1.48 2.00 38.4 0.0032 0.0055
  • test specimens obtained were subjected to the solution heat treatment twice under the temperature conditions shown in Table 2 and age-hardening heat treatment, and then the crystal gain size number of the test specimens was measured.
  • the crystal grain size number was measured according to JIS G0551.
  • the first step solution heat treatment was performed at 1020°C for 3 hours, 1060°C for 3 hours, and 1100°C for 3 hours, respectively and then the second step solution heat treatment was performed at 980°C for 2 hours. Subsequently, the age-hardening heat treatment was performed at 840°C for 8 hours and 740° for 24 hours.
  • the first step solution heat treatment was performed at 1140°C for 3 hours and 1140°C for one hour, respectively, and then the second step solution heat treatment was performed at 980°C for 2 hours. Subsequently, age-hardening heat treatment was performed at 840°C for 8 hours and 740°C for 24 hours.
  • the first step solution heat treatment was not performed and only the second step heat treatment was performed. Then, an age-hardening heat treatment was performed at 840°C for 8 hours and at 740°C for 24 hours.
  • the crystal grain size number after the heat treatment could be 0 to 2.
  • Fig. 1 is a graph showing a relationship between the crystal grain number and the creep rupture time.
  • the creep conditions are 700°C and 733 MPa.
  • the rupture time is 200 hours when the grain size is controlled by defining the crystal grain size number to 3 or less. As shown in Fig. 1 , the rupture time tends to be longer as the crystal grain size number is smaller.
  • Fig. 2 shows results of a low cycle fatigue test for test specimens.
  • Fig. 2 is a graph showing a relation between the crystal grain size number and the number of cycles in low cycle fatigue rupture.
  • the strain range is 0.8% at 700°C.
  • the number of cycles stays substantially flat when the crystal grain number is 1 or greater, and tends to lower somewhat when the crystal grain number is 0, and the number of rupture cycles is greatly lowered when the number is less than 0.
  • the crystal grain size number be 2 or less for the creep strength and it is preferred that the crystal grain size number be preferably 0 or more and, more preferably, 1 or more for the fatigue property.
  • the fatigue property can be improved without decrease in creep strength.
  • the material of the invention has the characteristics described above, it is suitable for components of the steam turbines (for example, a rotor) in the steam turbine power generation plants that provide a main steam temperature of 675°C or higher.
  • a steam turbine generally comprises a high pressure turbine (or medium pressure turbine) and a low pressure turbine.
  • a high pressure turbine or medium pressure turbine
  • iron type materials are used even in a steam turbine at a steam temperature of 700°C class, since the steam temperature is 600°C or lower in a low pressure turbine whose temperature is lowered.
  • a high pressure turbine or a medium pressure turbine for use in some steam turbines is subjected to a steam temperature of 700°C or higher, Ni-based or NiFe-based alloy is used for rotors, blades, casing bolts of the turbines.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
EP20110178329 2010-08-26 2011-08-22 Geschmiedete Legierung für Dampfturbinen und Dampfturbinenrotor damit Not-in-force EP2423342B1 (de)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2010188982A JP5633883B2 (ja) 2010-08-26 2010-08-26 蒸気タービン用鍛造合金、それを用いた蒸気タービンロータ

Publications (2)

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EP2423342A1 true EP2423342A1 (de) 2012-02-29
EP2423342B1 EP2423342B1 (de) 2013-06-12

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JP (1) JP5633883B2 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2706126A1 (de) * 2012-09-06 2014-03-12 Hitachi Ltd. Nickelbasislegierungsgeschmiedete Legierung und Gasturbine damit

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5657964B2 (ja) * 2009-09-15 2015-01-21 三菱日立パワーシステムズ株式会社 高強度Ｎｉ基鍛造超合金及びその製造方法
JP6016016B2 (ja) * 2012-08-09 2016-10-26 国立研究開発法人物質・材料研究機構 Ｎｉ基単結晶超合金
JP5599850B2 (ja) * 2012-08-24 2014-10-01 株式会社日本製鋼所 耐水素脆化特性に優れたＮｉ基合金および耐水素脆化特性に優れたＮｉ基合金材の製造方法
JP6805583B2 (ja) * 2016-07-04 2020-12-23 大同特殊鋼株式会社 析出型耐熱Ｎｉ基合金の製造方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH09157779A (ja) 1995-10-05 1997-06-17 Hitachi Metals Ltd 低熱膨張Ｎｉ基超耐熱合金およびその製造方法
EP1486578A1 (de) * 2003-06-13 2004-12-15 Hitachi Ltd. Dampfturbinenrotor und Dampfturbinenanlage
EP1892307A1 (de) * 2006-08-25 2008-02-27 Hitachi, Ltd. Ni-Fe-basierte Knetsuperlegierung mit ausgezeichneter Hochtemperaturfestigkeit und -biegsamkeit, Verfahren zu ihrer Herstellung, und Dampfturbinenrotor
EP2298946A2 (de) * 2009-09-15 2011-03-23 Hitachi Ltd. Hochfeste Knett-Superlegierung auf Nickelbasis und Verfahren zur Herstellung

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH09157779A (ja) 1995-10-05 1997-06-17 Hitachi Metals Ltd 低熱膨張Ｎｉ基超耐熱合金およびその製造方法
EP1486578A1 (de) * 2003-06-13 2004-12-15 Hitachi Ltd. Dampfturbinenrotor und Dampfturbinenanlage
JP2005002929A (ja) 2003-06-13 2005-01-06 Hitachi Ltd 蒸気タービンロータおよび蒸気タービンプラント
EP1892307A1 (de) * 2006-08-25 2008-02-27 Hitachi, Ltd. Ni-Fe-basierte Knetsuperlegierung mit ausgezeichneter Hochtemperaturfestigkeit und -biegsamkeit, Verfahren zu ihrer Herstellung, und Dampfturbinenrotor
EP2298946A2 (de) * 2009-09-15 2011-03-23 Hitachi Ltd. Hochfeste Knett-Superlegierung auf Nickelbasis und Verfahren zur Herstellung

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2706126A1 (de) * 2012-09-06 2014-03-12 Hitachi Ltd. Nickelbasislegierungsgeschmiedete Legierung und Gasturbine damit
US9617856B2 (en) 2012-09-06 2017-04-11 Mitsubishi Hitachi Power Systems, Ltd. Ni base forged alloy and gas turbine utilizing the same

Also Published As

Publication number Publication date
JP2012046787A (ja) 2012-03-08
JP5633883B2 (ja) 2014-12-03
EP2423342B1 (de) 2013-06-12

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