EP2402473A2 - Procédé de fabrication d'un composant monocristallin constitué d'un superalliage à base de nickel - Google Patents

Procédé de fabrication d'un composant monocristallin constitué d'un superalliage à base de nickel Download PDF

Info

Publication number
EP2402473A2
EP2402473A2 EP11171088A EP11171088A EP2402473A2 EP 2402473 A2 EP2402473 A2 EP 2402473A2 EP 11171088 A EP11171088 A EP 11171088A EP 11171088 A EP11171088 A EP 11171088A EP 2402473 A2 EP2402473 A2 EP 2402473A2
Authority
EP
European Patent Office
Prior art keywords
component
temperature
solution annealing
nickel
cast
Prior art date
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
EP11171088A
Other languages
German (de)
English (en)
Other versions
EP2402473B8 (fr
EP2402473A3 (fr
EP2402473B1 (fr
Inventor
Mohamed Nazmy
Claus Paul Gerdes
Andreas KÜNZLER
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Ansaldo Energia Switzerland AG
Original Assignee
Alstom Technology AG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Alstom Technology AG filed Critical Alstom Technology AG
Publication of EP2402473A2 publication Critical patent/EP2402473A2/fr
Publication of EP2402473A3 publication Critical patent/EP2402473A3/fr
Application granted granted Critical
Publication of EP2402473B1 publication Critical patent/EP2402473B1/fr
Publication of EP2402473B8 publication Critical patent/EP2402473B8/fr
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting

Definitions

  • the invention relates to the field of materials technology. It relates to a method for producing a single-crystal component consisting of a nickel-base superalloy or directionally solidified component having comparatively large dimensions. With the aid of the method according to the invention, particularly good properties, in particular very good fatigue strength, are achieved with low-cycle stress on the component.
  • Single-crystal components made of nickel-based superalloys have, among other things, a very good material strength at high stress temperatures, but also good corrosion and oxidation resistance as well as good creep resistance. Due to these properties, when using such materials z. As in gas turbines, the inlet temperature of the gas turbine can be increased, whereby the efficiency of the gas turbine plant increases.
  • the first type to which the present invention relates may be completely solution annealed so that the entire ⁇ 'phase is in solution.
  • This is the case for example for the known alloy CMSX4 with the following chemical composition (in% by weight): 5.6 Al, 9.0 Co, 6.5 Cr, 0.1 Hf, 0.6 Mo, 3 Re, 6.5 Ta, 1.0 Ti, 6.0 W, Rest Ni or the alloy PWA 1484 with the following chemical composition (in% by weight): 5 Cr, 10 Co, 6 W, 2 Mo, 3 Re, 8.7 Ta, 5.6 Al, 0.1 Hf and the known alloy MC2, which unlike the abovementioned alloys, it is not alloyed with rhenium and has the following chemical composition (in% by weight): 5 Co, 8 Cr, 2 Mo, 8 W, 5 Al, 1.5 Ti, 6 Ta, balance Ni.
  • a typical standard heat treatment for CMSX4, for example, is the following: solution annealing at 1320 ° C / 2h / shielding gas, fan cooling.
  • the second type of single crystal nickel base superalloys is not fully heat treatable, i.
  • the entire portion of the ⁇ '-phase in a solution annealing goes into solution, but only a certain part.
  • This is the case, for example, with the known superalloy CMSX186 having the following chemical composition (in% by weight): 0.07 C, 6 Cr, 9 Co, 0.5 Mo, 8 W, 3 Ta, 3 Re, 5.7 Al, 0.7 Ti, 1.4 Hf, 0.015 B, 0.005 Zr, remainder Ni and the alloy CMSX486 with the following chemical composition (in% by weight): 0.07 C, 0.015 B, 5.7 Al, 9.3 Co, 5 Cr, 1.2 Hf, 0.7 Mo, 3 Re, 4.5 Ta, 0.7 Ti, 8.6 W, 0.005 Zr, balance Ni.
  • the nickel-based superalloys of the second type are usually subjected to a two-stage heat treatment (aging process at lower temperatures), as at higher temperatures, as typically used in the alloys of the first type for solution annealing are already reached, the melting point start temperature, and thus the alloy begins to melt undesirable.
  • the creep resistance of the first type of nickel-base superalloys is usually higher than that of the second type, provided that the alloys belong to the same generation. This is mainly due to the fact that the dissolved ⁇ 'is the main source of recoverable strength.
  • Nickel-based superalloys for single-crystal components such as. B. off US 4,643,782 . EP 0 208 645 .
  • US 5,270,123 and US 7,115,175 B2 contain alloying, such as Re, W, Mo, Co, Cr, and ⁇ '-phase-forming elements, such as Al, Ta, and Ti.
  • the content of high-melting alloy elements (W, Mo, Re) in the basic matrix ( austenitic ⁇ phase) increases continuously with the increase of the stress temperature of the alloy.
  • small amounts of C, B, Hf and Zr are often present.
  • the alloys disclosed in the above references have a high creep strength, a comparatively good LCF (low cycle fatigue fatigue) and HCF (high cycle life fatigue) properties, and a high oxidation resistance.
  • the alloy CMSX-4 US 4,643,782 when used experimentally in a gas turbine at a temperature above 1000 ° C, a strong coarsening of the ⁇ '-phase, which is associated with an increase in the creeping speed of the alloy adversely.
  • a similar effect leading to the flocculation of the ⁇ '-phase also results from the solidification of nickel-based superalloys due to dendritic segregation. Especially in superalloys with a high proportion of slowly diffusing elements, such. As rhenium, the segregations of these elements can not be completely eliminated within an acceptable homogenization time. Since the ⁇ '-phase, which precipitates during cooling, has a smaller lattice constant than the ⁇ matrix and the ⁇ / ⁇ '-lattice offset in the dendrites is larger than in the interdendritic regions, internal stresses occur during this process the heat treatment, especially during cooling.
  • the process immediately following the casting step is carried out after a two-stage slow heating of the cast object at a final HIP temperature in the range of 1174 ° C (2145 ° F) to 1440 ° C (2625 ° F), wherein the hold time is 3.5 to 4.5 hours and the pressure is in the range of 89.6 MPa (13 ksi) to 113 MPa (16.5 ksi), that is, comparatively low.
  • the aim of the invention is to avoid the mentioned disadvantages of the prior art.
  • the invention is based on the object to provide a suitable method for the production, including heat treatment, of comparatively large single-crystal components or components with directionally solidified structure of known nickel-based superalloys, with which a microstructure can be adjusted that not for raft formation ⁇ '-phase and therefore leads to improved mechanical properties, in particular an improved fatigue life at low load cycles (LCF) of the components.
  • the method according to the invention it is possible to produce large single-crystal components or components with directionally solidified microstructure of known nickel-based superalloys, which on the one hand are free of pores and on the other hand have a microstructure in which the flocculation of the ⁇ 'phase is avoided. Therefore, the components thus produced have improved mechanical properties, in particular improved low cycle fatigue life (LCF) fatigue strength.
  • the method has the advantage that it is relatively easy to implement.
  • step A) It is advantageous if the determination of the dendrite arm spacing ( ⁇ ) according to step A) takes place by metallographic means. This is relatively easy to implement and can be done, for example, in advance of the process using appropriate samples.
  • the quenching rate (v1) of solution annealing temperature (T 1 ) to room temperature is greater than 70 ° C / min, because then extremely fine uniformly distributed ⁇ '-particles are obtained in the ⁇ -matrix.
  • the nickel-base superalloys CMSX4 known from the prior art with the following chemical composition (in% by weight) were used: 5.6 Al, 9.0 Co, 6.5 Cr, 0.1 Hf, 0.6 Mo, 3 Re, 6.5 Ta, 1.0 Ti, 6.0 W, balance Ni.
  • the component such as a gas turbine bucket
  • the component was poured into its mold.
  • dendritic segregations arise due to the composition, in particular the comparatively high Re content.
  • Rhenium is a very slowly diffusing element, therefore these segregations can not be completely eliminated within an acceptable homogenization time in the subsequent solution annealing process.
  • the ⁇ '-phase which precipitates during cooling, has a smaller lattice constant than the ⁇ -matrix and the ⁇ / ⁇ '-lattice offset in the dendrites is larger than in the interdendritic regions, internal stresses are formed during the heat treatment, especially during cooling. This leads to a degradation in the ⁇ '-microstructure, in that the initially cubic form of ⁇ 'changes into a stretched form of ⁇ '. This is accompanied by the deterioration of mechanical properties, eg. B. fatigue strength at low load cycles.
  • the dendrite arm spacing ⁇ in different, for example, the critical areas of the cast Component determined. This can z. Example, carried out by metallographic means, which may already be determined in advance of the process, this distance on the basis of corresponding pre-cast samples.
  • the slowest diffusion element in the composition of the respective nickel base superalloy is identified to determine the diffusion coefficient D.
  • this element is rhenium, as already explained above.
  • this element is Mo.
  • the required time t is calculated at which the component at solution annealing temperature T 1 , which is lower on the one hand than the starting melt temperature T mi , and on the other hand high enough to in the necessary heat treatment window must be held so that the microsegregation of this slowest diffusion element is reduced to ⁇ 5%.
  • Fig. 1 is the time-temperature diagram of the subsequent to the casting process treatment method for producing the single crystal component from the above superalloy shown schematically.
  • the solution annealing (process step D)) of the cast component in the present embodiment thus comprises heating the component to the above solution annealing temperature T 1 of 1290-1310 ° C, holding at this temperature with the time t calculated above (4-6 h) and a rapid quenching from the solution annealing temperature T 1 to room temperature at a rate v1 ⁇ 50 ° C / min, in order to obtain very fine uniformly distributed ⁇ 'particles in the ⁇ matrix after quenching (Scheme Fig. 2a ).
  • the quenching rate is greater than 70 ° C / min, because then a microstructure is obtained with extremely fine uniformly distributed ⁇ '-particles in the ⁇ -matrix.
  • a two-stage precipitation treatment for precipitating the ⁇ '-phase is carried out at lower temperatures T 2 and T 3 in comparison to T 1 (method step E)), wherein in the first stage of the precipitation treatment a HIP method with one pressure p greater than 160 MPa and a cooling rate v2 ⁇ 50 ° C / min is applied.
  • the final temperature of the HIP process in the present embodiment is 1150 ° C, the holding time 4-6 h.
  • the applied final pressure during the HIP process is relatively high, it is greater than the internal stresses caused by the inhomogeneities in the microstructure.
  • this method step advantageously closes any micropores present in the microstructure and, on the other hand, eliminates stresses which are caused by the rapid cooling of the solution annealing temperature T 1 to room temperature or by any residual inhomogeneities in the microstructure. This prevents directional flocculation of the ⁇ 'phase by the formation of the aforementioned cubic ⁇ ' particles in the ⁇ matrix.
  • the microstructure present after the HIP-treatment step consists of fine uniformly distributed cubic ⁇ '-particles in the ⁇ -matrix and is schematically in ⁇ 001> orientation in Fig. 2b shown.
  • the realization of the first stage of method step D) is possible in several variants. Corresponding time-temperature or pressure-temperature diagrams for the HIP process are schematically in the 3 a) to 3 c) shown.
  • the single-crystal component / directionally solidified component is heated to a temperature T 3 of 870 ° C., held at this temperature T 3 for 16-20 h and then cooled to room temperature at a cooling rate v3 of approx. 50 ° C./minute ,
  • the end structure according to the present invention formed after this last treatment step is schematically for the ⁇ 001> orientation in FIG Fig. 2c shown.
EP11171088.5A 2010-06-30 2011-06-22 Procédé de fabrication d'un composant monocristallin constitué d'un superalliage à base de nickel Not-in-force EP2402473B8 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CH01058/10A CH703386A1 (de) 2010-06-30 2010-06-30 Verfahren zur Herstellung einer aus einer Nickel-Basis-Superlegierung bestehenden Einkristallkomponente.

Publications (4)

Publication Number Publication Date
EP2402473A2 true EP2402473A2 (fr) 2012-01-04
EP2402473A3 EP2402473A3 (fr) 2013-10-30
EP2402473B1 EP2402473B1 (fr) 2017-04-26
EP2402473B8 EP2402473B8 (fr) 2017-07-26

Family

ID=42938589

Family Applications (1)

Application Number Title Priority Date Filing Date
EP11171088.5A Not-in-force EP2402473B8 (fr) 2010-06-30 2011-06-22 Procédé de fabrication d'un composant monocristallin constitué d'un superalliage à base de nickel

Country Status (4)

Country Link
US (1) US8435362B2 (fr)
EP (1) EP2402473B8 (fr)
JP (1) JP5787643B2 (fr)
CH (1) CH703386A1 (fr)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105689719A (zh) * 2016-02-17 2016-06-22 西南交通大学 一种合金液滴沉积的冷却速率计算方法
EP3211111A3 (fr) * 2016-02-24 2017-11-29 MTU Aero Engines GmbH Procédé de traitement thermique pour des composants constitués de super-alliages à base de nickel
CN110760770A (zh) * 2019-10-30 2020-02-07 西安交通大学 单晶镍基高温合金冷变形后的热处理方法
WO2022208004A1 (fr) * 2021-04-02 2022-10-06 Safran Superalliage a base de nickel, aube monocristalline et turbomachine

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013167513A1 (fr) 2012-05-07 2013-11-14 Alstom Technology Ltd Procédé de fabrication d'éléments en superalliages monocristallins (sx) ou solidifiés de manière directionnelle (ds)
DE102013008396B4 (de) 2013-05-17 2015-04-02 G. Rau Gmbh & Co. Kg Verfahren und Vorrichtung zum Umschmelzen und/oder Umschmelzlegieren metallischer Werkstoffe, insbesondere von Nitinol
JP6528926B2 (ja) * 2014-05-21 2019-06-12 株式会社Ihi 原子力施設の回転機器
WO2018111566A1 (fr) * 2016-12-15 2018-06-21 General Electric Company Procédés de traitement pour articles en superalliage et articles associés
CN113930697B (zh) * 2021-09-23 2022-09-27 鞍钢集团北京研究院有限公司 一种750-850℃级变形高温合金的热处理方法
CN114038522A (zh) * 2021-11-18 2022-02-11 成都先进金属材料产业技术研究院股份有限公司 Gh5188合金均匀化热处理工艺的确定方法
CN114737081B (zh) * 2022-04-06 2023-03-24 暨南大学 一种具有分层微观结构的Ni-Al-Ti基高温合金及其制备方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0208645A2 (fr) 1985-06-10 1987-01-14 United Technologies Corporation Compositions en monocristal de superalliage à haute résistance mécanique
US4643782A (en) 1984-03-19 1987-02-17 Cannon Muskegon Corporation Single crystal alloy technology
US5270123A (en) 1992-03-05 1993-12-14 General Electric Company Nickel-base superalloy and article with high temperature strength and improved stability
US5435861A (en) 1992-02-05 1995-07-25 Office National D'etudes Et De Recherches Aerospatiales Nickel-based monocrystalline superalloy with improved oxidation resistance and method of production
US7115175B2 (en) 2001-08-30 2006-10-03 United Technologies Corporation Modified advanced high strength single crystal superalloy composition

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4328045A (en) * 1978-12-26 1982-05-04 United Technologies Corporation Heat treated single crystal articles and process
IL80227A (en) * 1985-11-01 1990-01-18 United Technologies Corp High strength single crystal superalloys
US5820700A (en) * 1993-06-10 1998-10-13 United Technologies Corporation Nickel base superalloy columnar grain and equiaxed materials with improved performance in hydrogen and air
US5695821A (en) * 1995-09-14 1997-12-09 General Electric Company Method for making a coated Ni base superalloy article of improved microstructural stability
JP3184882B2 (ja) * 1997-10-31 2001-07-09 科学技術庁金属材料技術研究所長 Ｎｉ基単結晶合金とその製造方法
EP1398393A1 (fr) * 2002-09-16 2004-03-17 ALSTOM (Switzerland) Ltd Méthode de régenération des propriétés
JP4885530B2 (ja) * 2005-12-09 2012-02-29 株式会社日立製作所 高強度高延性Ｎｉ基超合金と、それを用いた部材及び製造方法
JP4719583B2 (ja) * 2006-02-08 2011-07-06 株式会社日立製作所 強度、耐食性及び耐酸化特性に優れた一方向凝固用ニッケル基超合金及び一方向凝固ニッケル基超合金の製造方法
EP1900839B1 (fr) * 2006-09-07 2013-11-06 Alstom Technology Ltd Procédé pour le traitement thermique de superalliages à base de Ni

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4643782A (en) 1984-03-19 1987-02-17 Cannon Muskegon Corporation Single crystal alloy technology
EP0208645A2 (fr) 1985-06-10 1987-01-14 United Technologies Corporation Compositions en monocristal de superalliage à haute résistance mécanique
US5435861A (en) 1992-02-05 1995-07-25 Office National D'etudes Et De Recherches Aerospatiales Nickel-based monocrystalline superalloy with improved oxidation resistance and method of production
US5270123A (en) 1992-03-05 1993-12-14 General Electric Company Nickel-base superalloy and article with high temperature strength and improved stability
US7115175B2 (en) 2001-08-30 2006-10-03 United Technologies Corporation Modified advanced high strength single crystal superalloy composition

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
PESSAH-SIMONETTI, P. CARON, T. KHAN: "Effect of long-term prior aging on tensil behaviour of high-performance single crystal superalloy", JOURNAL DE PHYSIQUE IV, COLLOQUE C7, vol. 3, November 1993 (1993-11-01)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105689719A (zh) * 2016-02-17 2016-06-22 西南交通大学 一种合金液滴沉积的冷却速率计算方法
EP3211111A3 (fr) * 2016-02-24 2017-11-29 MTU Aero Engines GmbH Procédé de traitement thermique pour des composants constitués de super-alliages à base de nickel
CN110760770A (zh) * 2019-10-30 2020-02-07 西安交通大学 单晶镍基高温合金冷变形后的热处理方法
CN110760770B (zh) * 2019-10-30 2020-10-23 西安交通大学 单晶镍基高温合金冷变形后的热处理方法
WO2022208004A1 (fr) * 2021-04-02 2022-10-06 Safran Superalliage a base de nickel, aube monocristalline et turbomachine
FR3121453A1 (fr) * 2021-04-02 2022-10-07 Safran Superalliage a base de nickel, aube monocristalline et turbomachine

Also Published As

Publication number Publication date
JP2012012705A (ja) 2012-01-19
EP2402473B8 (fr) 2017-07-26
US20120000577A1 (en) 2012-01-05
CH703386A1 (de) 2011-12-30
EP2402473A3 (fr) 2013-10-30
JP5787643B2 (ja) 2015-09-30
EP2402473B1 (fr) 2017-04-26
US8435362B2 (en) 2013-05-07

Similar Documents

Publication Publication Date Title
EP2402473B1 (fr) Procédé de fabrication d'un composant monocristallin constitué d'un superalliage à base de nickel
DE3023576C2 (fr)
DE4440229C2 (de) Verfahren zum Herstellen von gegen Rißbildung widerstandsfähigen hochfesten Superlegierungsgegenständen
DE2749080A1 (de) Einkristallsuperlegierungsgegenstand auf nickelbasis und verfahren zu seiner herstellung
DE19624055A1 (de) Nickel-Basis-Superlegierung
DE102004056582B4 (de) Legierung auf der Basis von Titanaluminiden
WO2014124626A1 (fr) Alliage nickel-cobalt
EP1900839B1 (fr) Procédé pour le traitement thermique de superalliages à base de Ni
DE3234083A1 (de) Waermebehandelter einkristall-gegenstand aus einer superlegierung auf nickelbasis
DE112013003971T5 (de) Nickelbasierte einkristalline Superlegierung
CH695497A5 (de) Nickel-Basis-Superlegierung.
EP1420075B1 (fr) Superalliage à base de nickel
EP1451382A1 (fr) Procede de production d'un superalliage a base de nickel
EP3091095B1 (fr) Superalliage à base de nickel sans rhénium à faible densité
EP2354261B1 (fr) Superalliage à base de nickel ayant un comportement de dégradation amélioré
DE2649529A1 (de) Umformbare legierung auf kobalt- nickel-chrom-basis und verfahren zu seiner herstellung
DE19617093C2 (de) Wärmebehandlungsverfahren für Werkstoffkörper aus Nickel-Basis-Superlegierungen
DE3542882C2 (fr)
DE2821524C2 (de) Verfahren zur Wärmebehandlung eines einkristallinen Körpers aus einer Nickel-Superlegierung
EP2451986B2 (fr) Superalliage a base de nickel
DE3731598C1 (de) Verfahren zur Waermebehandlung von Nickel-Gusslegierungen
DE69934158T2 (de) Verfahren und Herstellung einer gerichtet erstarrten Gusslegierung auf Nickelbasis
DE102004029833A1 (de) Nickelbasis-Superlegierung und Einkristall-Gussstücke
EP0398121B1 (fr) Procédé de fabrication de grains basaltiques grossiers orientés longitudinalement dans un superalliage à base de nickel durci par dispersion d'oxyde
DE2642202A1 (de) Mehrstufige waermebehandlung fuer superlegierungen

Legal Events

Date Code Title Description
AK Designated contracting states

Kind code of ref document: A2

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

PUAL Search report despatched

Free format text: ORIGINAL CODE: 0009013

AK Designated contracting states

Kind code of ref document: A3

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 19/05 20060101ALI20130924BHEP

Ipc: C22F 1/10 20060101AFI20130924BHEP

Ipc: C30B 33/02 20060101ALI20130924BHEP

17P Request for examination filed

Effective date: 20131206

RBV Designated contracting states (corrected)

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: GENERAL ELECTRIC TECHNOLOGY GMBH

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20161125

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

RIN1 Information on inventor provided before grant (corrected)

Inventor name: KUENZLER, ANDREAS

Inventor name: GERDES, CLAUS PAUL

Inventor name: NAZMY, MOHAMED YOUSSEF

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

GRAT Correction requested after decision to grant or after decision to maintain patent in amended form

Free format text: ORIGINAL CODE: EPIDOSNCDEC

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 887955

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170515

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

RAP2 Party data changed (patent owner data changed or rights of a patent transferred)

Owner name: ANSALDO ENERGIA SWITZERLAND AG

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502011012099

Country of ref document: DE

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20170621

Year of fee payment: 7

Ref country code: GB

Payment date: 20170620

Year of fee payment: 7

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20170426

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170727

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170726

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20170731

Year of fee payment: 7

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170826

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170726

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502011012099

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20180228

26N No opposition filed

Effective date: 20180129

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170630

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170622

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170630

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170622

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170630

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20170630

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 887955

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170622

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170630

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170622

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502011012099

Country of ref document: DE

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20180622

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180622

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180622

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190101

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20110622

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170426

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170426