EP3077558B1 - Nickel-based alloy, method and use - Google Patents

Nickel-based alloy, method and use Download PDF

Info

Publication number
EP3077558B1
EP3077558B1 EP14830602.0A EP14830602A EP3077558B1 EP 3077558 B1 EP3077558 B1 EP 3077558B1 EP 14830602 A EP14830602 A EP 14830602A EP 3077558 B1 EP3077558 B1 EP 3077558B1
Authority
EP
European Patent Office
Prior art keywords
max
nickel
based alloy
product
alloy
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.)
Active
Application number
EP14830602.0A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP3077558A1 (en
Inventor
Luca FORONI
Raimondo MONTANI
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.)
Foroni SpA
Original Assignee
Foroni SpA
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 Foroni SpA filed Critical Foroni SpA
Publication of EP3077558A1 publication Critical patent/EP3077558A1/en
Application granted granted Critical
Publication of EP3077558B1 publication Critical patent/EP3077558B1/en
Active 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
    • 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
    • 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
    • C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%

Definitions

  • US5000914 discloses a precipitation-hardening type Ni-based alloy exhibiting improved resistance to stress corrosion cracking, having a chemical composition comprising Ni 58.5%, Cr 23%, Mo6.1%, Fe 7.3%, Nb 4.52%, Mn 0.01%, P 0.002%, S 0.002%, Ti ⁇ 0.01%, C 0.002%, Si 0.31%, Al 0.20%, N 0.14%, which has been hot worked, solution annealed, water quenched, aged and heat treated, and having a yield strength of >900 MPa and sulfide stress cracking resistance.
  • the present invention lies thus in the above context, proposing to provide a method of manufacture and nickel-based alloys able to overcome the drawbacks spoken of in relation to the prior art.
  • alloys which the present invention relates to are able to combine a number of desirable features, discussed below, which to date have been deemed to be substantially mutually irreconcilable.
  • Such objectives are achieved by a manufacturing method of a nickel-based alloy comprising the steps of:
  • the hardening metal phases of the nickel-based alloy are precipitated in a uniform manner in the grains of the latter.
  • the hardening metal phases ( ⁇ ' and ⁇ ") precipitate eminently in steps ii) and iv), and the ageing steps have been selected in such a way as to have the maximum precipitation rate of said phases.
  • the hardening metal phases may continue to precipitate but no longer at an optimal rate while the carbide phases (also referred to as “carbides” in this description), and optionally the undesired intermetallic phases, may have high precipitation rates during this process.
  • the nickel-based alloy comprises hardening phases ⁇ ' and ⁇ " precipitated in an essentially non-intergranular position, and carbides precipitated in a discontinuous manner at least along the boundary of the aforesaid grains.
  • the alloy produced using the aforesaid method is subject to the phenomenon of intergranular corrosion in an extremely limited, if not non-existent manner, at least compared to the alloys currently used.
  • the Fe may be present in a percentage of about 5-15_or about 5-12.
  • step i) comprises substeps of forging the nickel-based alloy at a temperature of approximately 1000-1160°C and then solution treating said mass at a temperature of approximately 1030-1080°C.
  • the sub-step of solution treating is followed by a cooling step in water before step ii), or by a rapid cooling of an equivalent type.
  • step iii) by itself already constitutes a product of industrial interest and with its own market.
  • this method could comprise a step of separating the product of step iii), and a step of transforming a first part of the separated product into a first finished product, e.g. with lower performances, and/or a step of storing said separated product.
  • step v not all the forged and solution treated metal mass starting the process needs necessarily to lead to the product of step v), but a part thereof could be withdrawn at the end of step iii), and be transformed as indicated above, or even simply stored.
  • the step iii) product could be characterised by a yield strength, measured at ambient temperature, equal to or greater than approximately 827 MPa.
  • the method may comprise a step of sending to step iv) (and subsequently to step v)) a second part of the aforesaid separated product at step iii), to obtain a second product, e.g. of higher performances, made of the nickel-based alloy.
  • step iv) the separated and/or stored product may be subjected to step iv) at a different time from step iii), for example as a result of an order for the nickel-based alloy.
  • the nickel-based alloy is characterised by a yield strength, measured at ambient temperature, equal to or greater than about 950-970 MPa, preferably greater than or equal to 970 MPa.
  • the alloy having lower performances will be considered such only in relation to the higher performance alloy, and preferably limited to the yield strength parameter only. This does not mean that the "lower" alloy from this point of view, might not be better if compared relative to other factors, for example in relation to the anti-corrosion properties.
  • step ii said step is specifically used in order to minimise the precipitation of carbides and other unwanted phases at the grain boundaries.
  • Step ii) is conducted at a temperature (defined as "higher”) of about 720-780°C for about 3-8 hours, or for about 3-6 hours.
  • Step iv) is conducted at a temperature (defined as "lower”) of about 600-640°C for about 4-10 hours.
  • cooling steps iii) and/or v) could be performed in air at room temperature, preferably up to about an ambient temperature of the respective products.
  • ambient temperature a temperature external to the strongly heated ambient in which the ageing steps ii) and iv) are conducted.
  • ambient temperature could refer to the temperature outside the furnace used to perform the aforesaid ageing heat treatments, more precisely at the cooling planes situated inside the production plant.
  • the ambient temperature could be the temperature of the production plant, changing greatly depending on the season of the year in which the production takes place and/or on the latitude of the production site in which the aforesaid method takes place.
  • the aforesaid objective is also resolved by a nickel-based alloy obtained through the steps of:
  • the nickel-based alloy comprises metal hardening phases precipitated uniformly throughout its grains.
  • the nickel-based alloy comprises hardening phases ⁇ ' and ⁇ " precipitated in an essentially non-intergranular position, and carbides precipitated in a discontinuous manner at least along the boundary of said grains.
  • step iii) and iv) interspersed by step iii) promote the precipitation of the hardening phases ⁇ ' and ⁇ " in a uniform and preferably fine manner, minimising the precipitation carbides and unwanted intermetallic phases at the grain boundary.
  • Said alloy is characterised in that it comprises hardening phases ⁇ ' and ⁇ " precipitated essentially in a non-intergranular position, advantageously evenly and preferably finely, and carbides precipitated discontinuously at least at the boundary of said grains.
  • the latter alloy could be obtained using the method according to any of the embodiments illustrated above.
  • preferred or advantageous variants of said alloy could comprise any manufacturing step deductible from the aforesaid description.
  • the alloy of the present invention is preferably usable for making equipment and pipes for the chemical or petrol industries.
  • Example 1 Means for implementing the method.
  • the nickel-based alloy which the invention relates to is preferably melted in an electric arc furnace, refined in A.O.D. (Argon Oxygen Decarburization) so as to obtain an intense desulphurisation, thorough deoxidisation and a very restricted analytical range of compositions to ensure repeatability of the mechanical and corrosion properties.
  • A.O.D. Aral Oxygen Decarburization
  • the refining process could be completed by at least one of the following operations:
  • the ingots obtained after V.A.R. or E.S.R. remelting may be subjected to appropriate homogenisation heat treatment and then transformed into blooms through use of a forging press, for example having two integrated, fully automated manipulators programmable both for the entity and deformation rate for each cycle.
  • the blooms, after intermediate grinding, could be transformed into billets/bars through the use of a hydraulic press with four synchronised hammers, for example with dual manipulator and/or new concept RCD (Round Continuous Deforming) rolling mill. These last two systems could also be automated and programmable.
  • the heat-processing plants designed ad hoc for long products (in particular having a extension length substantially greater than the width or thickness, such as pipes or bars), make it possible to work within narrow temperature ranges so as to have a good control of the grain uniformity and avoid the precipitation of deleterious phases especially for resistance corrosion in the environments in which the products, made from the alloy according to the invention, are intended for use.
  • Example 2 Comparison of the nickel-based alloy of the invention with traditional alloys currently used.
  • the nickel-based alloy of the present invention after heat transformation in the temperature range 1000-1160°C and solution treatment in the range 1030-1080°C, typically has the mechanical features shown in Figure 1 .
  • the nickel-based alloy of the present invention (called "AF.955"), after solution treatment as in the above paragraph, if aged in the temperature range 720-780°C for 3-8 hours and air cooled (or equivalent cooling, or in case of faster cooling) typically has the mechanical features specified in Figure 2 and the resistance data to intergranular corrosion and pitting referred to in Figures 6-7-8 .
  • the alloy after a second ageing at 600°-640°C for a time ranging from 4-10 hours, followed by air cooling, presents the mechanical characteristics specified in Figure 3 , and the resistance to intergranular corrosion and pitting referred to Figures 6-7-8 .
  • Figures 4-5 shows the chemical composition and characteristic mechanical properties of the alloys most commonly used in the numerous environments encountered in the oil and natural gas extraction industry.
  • the 3 grades (Gr. 3) differ from the 3HS grades (Gr.3HS) only in the methods (temperatures/times) of the thermal ageing treatment.
  • the 3 grades (Gr.3) relate to a nickel-based alloy subjected to a single ageing step and subsequent cooling as per steps ii) and iii) mentioned above.
  • the 3HS grades (Gr.3HS) relate to an alloy which has also undergone the second steps of ageing and cooling - namely also steps iv) and v).
  • Figures 6-7-8-9-10 provide information on the resistance capacity of the materials in the laboratory corrosion tests compared to the alloy of the invention.
  • Figures 11A-11B show the metallography of the alloy AF.955 (at 100X and 500X magnifications) before step ii), namely at the end of forging and solution treating of the metal mass only.
  • Figures 11C-11D show the metallography - again at the aforesaid magnifications - of the aforesaid step iii) product, i.e. following the first ageing and subsequent air cooling step.
  • Figures 11E-11F lastly show metallographies corresponding to the previous ones, relative to the alloy AF.955 at the end of step v).
  • Figures 12A-12F and Figures 13A-13F show a metallography respectively of the alloy N07718 and of the alloy N07716 corresponding to the aforementioned Figures (after solution treating, 12A-12B for the alloy N07718 and 13A-13B for the alloy N07716; after a first type of ageing for each alloy Gr. 3 (12C-12D and 13C-13D) and after a second ageing for Gr.3HS for each alloy (12E-12F and 13E-13F).
  • the method and nickel alloys of the present invention make it possible to brilliantly resolve the drawbacks spoken of in relation to the prior art.
  • the method and the nickel alloys of the present invention are substantially free of intergranular metal phase precipitates, in particular of carbides, so that the corrosion phenomenon at the grain boundary is dramatically reduced, if not substantially absent compared to the prior art.
  • the alloy of the present invention has greater mechanical and traction resistance properties, and in particular lengthening and pinch point data, than the metal alloys it was compared to, a considerable resistance to corrosion under stress and very low hydrogen embrittlement with elongation at rupture characteristics still high enough to guarantee safe use of the alloy in environments in which nascent hydrogen may develop.
  • a clear temporal separation between the precipitation phases makes it possible to obtain different alloys of different types, markedly different in performance.
  • step iii) product proves to be optimal for certain industrial applications.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Forging (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
  • Physical Or Chemical Processes And Apparatus (AREA)
  • Powder Metallurgy (AREA)
EP14830602.0A 2013-12-05 2014-12-05 Nickel-based alloy, method and use Active EP3077558B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
IT000061A ITVA20130061A1 (it) 2013-12-05 2013-12-05 Lega invecchiante base nichel contenente cromo, molibdeno, niobio, titanio; avente alte caratteristiche meccaniche ed elevata resistenza alla corrosione in ambienti aggressivi che si possono incontrare nei pozzi per l'estrazione di petrolio e gas nat
PCT/IB2014/066645 WO2015083133A1 (en) 2013-12-05 2014-12-05 Nickel-based alloy, method and use

Publications (2)

Publication Number Publication Date
EP3077558A1 EP3077558A1 (en) 2016-10-12
EP3077558B1 true EP3077558B1 (en) 2017-08-23

Family

ID=50033733

Family Applications (1)

Application Number Title Priority Date Filing Date
EP14830602.0A Active EP3077558B1 (en) 2013-12-05 2014-12-05 Nickel-based alloy, method and use

Country Status (7)

Country Link
US (1) US20180171456A1 (ja)
EP (1) EP3077558B1 (ja)
JP (1) JP6571103B2 (ja)
AU (1) AU2014358718B2 (ja)
ES (1) ES2644391T3 (ja)
IT (1) ITVA20130061A1 (ja)
WO (1) WO2015083133A1 (ja)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105543748B (zh) * 2015-12-30 2018-10-02 无锡透平叶片有限公司 一种Nimonic101镍基合金的热处理方法
ITUA20163944A1 (it) * 2016-05-30 2017-11-30 Nuovo Pignone Tecnologie Srl Process for making a component of a turbomachine, a component obtainable thereby and turbomachine comprising the same / Processo per ottenere un componente di turbomacchina, componente da esso ottenibile e turbomacchina che lo comprende
JP6829830B2 (ja) * 2016-11-11 2021-02-17 大同特殊鋼株式会社 Ｆｅ−Ｎｉ基合金及びその製造方法
IT201800004541A1 (it) * 2018-04-16 2019-10-16 Procedimento per la produzione di una superlega e superlega ottenuta con il procedimento
CN111187999B (zh) * 2020-02-17 2020-12-08 河北工业大学 一种增强多晶Ni-Cr-Al基合金抗燃气腐蚀性能的热处理方法
CN113088761B (zh) * 2021-02-21 2022-08-05 江苏汉青特种合金有限公司 一种超高强度耐蚀合金及制造方法

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB612181A (en) * 1946-05-16 1948-11-09 Mond Nickel Co Ltd Improvements relating to the heat treatment of heat-resisting alloys and of articlesor parts made therefrom
GB734210A (en) * 1952-12-09 1955-07-27 Rolls Royce Improvements relating to processes of manufacturing turbine blades from heat-resisting alloys
US3372068A (en) * 1965-10-20 1968-03-05 Int Nickel Co Heat treatment for improving proof stress of nickel-chromium-cobalt alloys
US4379120B1 (en) * 1980-07-28 1999-08-24 Crs Holdings Inc Sulfidation resistant nickel-iron base alloy
JPS57123948A (en) * 1980-12-24 1982-08-02 Hitachi Ltd Austenite alloy with stress corrosion cracking resistance
JPS61119641A (ja) * 1984-11-16 1986-06-06 Sumitomo Metal Ind Ltd 高耐食性Ｎｉ基合金およびその製造法
US5000914A (en) * 1986-11-28 1991-03-19 Sumitomo Metal Industries, Ltd. Precipitation-hardening-type ni-base alloy exhibiting improved corrosion resistance
JPS63137133A (ja) * 1986-11-28 1988-06-09 Sumitomo Metal Ind Ltd 高耐食性析出硬化型Ｎｉ基合金
US9017490B2 (en) * 2007-11-19 2015-04-28 Huntington Alloys Corporation Ultra high strength alloy for severe oil and gas environments and method of preparation
US8313593B2 (en) * 2009-09-15 2012-11-20 General Electric Company Method of heat treating a Ni-based superalloy article and article made thereby
US20120003728A1 (en) * 2010-07-01 2012-01-05 Mark Allen Lanoue Scalable Portable Sensory and Yield Expert System for BioMass Monitoring and Production

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
ES2644391T3 (es) 2017-11-28
AU2014358718A1 (en) 2016-07-07
ITVA20130061A1 (it) 2015-06-06
AU2014358718B2 (en) 2018-06-28
US20180171456A1 (en) 2018-06-21
JP6571103B2 (ja) 2019-09-04
JP2017503085A (ja) 2017-01-26
WO2015083133A1 (en) 2015-06-11
EP3077558A1 (en) 2016-10-12

Similar Documents

Publication Publication Date Title
EP3077558B1 (en) Nickel-based alloy, method and use
US20200048750A1 (en) Ni-Based Alloy Product and Method for Producing Same, and Ni-Based Alloy Member and Method for Producing Same
CA3057342C (en) Thermo-mechanical processing of nickel-base alloys
CN102719761B (zh) 轮盘锻件及制造工艺
WO2018092204A1 (ja) ニッケル基合金高温部材の製造方法
KR20170029631A (ko) 고강도 오스테나이트계 스테인레스 강 및 그의 제조 방법
US20100316525A1 (en) TiAl-BASED ALLOY, PROCESS FOR PRODUCING SAME, AND ROTOR BLADE USING SAME
JP5995157B2 (ja) マルテンサイト系析出強化型ステンレス鋼の製造方法
JP2009517546A (ja) 熱間工具鋼及び当該鋼から製造される部品、部品を製造する方法及び部品の使用
CN105506457A (zh) 低温锻钢制造方法及其产品
CN103276296A (zh) 一种马氏体不锈钢环形锻件及其制造方法
CN106756509B (zh) 一种耐高温合金结构钢及其热处理工艺
JP6575756B2 (ja) 析出強化型ステンレス鋼の製造方法
US5415712A (en) Method of forging in 706 components
CN106566953A (zh) 一种耐腐蚀合金锻件及其生产方法
CN109207697A (zh) 超低碳高锰钼不锈钢及其制备方法
CN105734344B (zh) 一种综合高温性能优异的镍基合金及其生产工艺
JP6185347B2 (ja) Ｎｉ基超耐熱合金の分塊用中間素材及びその製造方法、Ｎｉ基超耐熱合金の製造方法
CN104611612A (zh) 提高热连轧Ti6Al4V合金持久寿命的预处理工艺
JP5382518B2 (ja) チタン材
CN104148555A (zh) 1Cr14Mn14Ni不锈钢环形件的锻造成形方法
JP2013185249A (ja) 鉄合金
TW201814059A (zh) 析出強化型鎳基合金及其製造方法
CN116875915A (zh) 马氏体时效钢、马氏体时效钢的制备方法以及电子设备
CN117802297A (zh) 提高含钒马氏体沉淀硬化不锈钢屈服强度比值的方法

Legal Events

Date Code Title Description
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

17P Request for examination filed

Effective date: 20160608

AK Designated contracting states

Kind code of ref document: A1

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

DAX Request for extension of the european patent (deleted)
GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20170426

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

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

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 921426

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170915

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602014013659

Country of ref document: DE

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2644391

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20171128

REG Reference to a national code

Ref country code: NO

Ref legal event code: T2

Effective date: 20170823

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 4

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20170823

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 921426

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170823

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

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: 20170823

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: 20170823

Ref country code: AT

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: 20170823

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: 20170823

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: 20171223

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: 20171123

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: 20170823

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: 20170823

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: 20171124

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: 20170823

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

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: 20170823

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: 20170823

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602014013659

Country of ref document: DE

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: 20170823

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: 20170823

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: 20170823

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: CH

Ref legal event code: PL

26N No opposition filed

Effective date: 20180524

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: 20170823

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

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 NON-PAYMENT OF DUE FEES

Effective date: 20171205

Ref country code: LU

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

Effective date: 20171205

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20171231

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

Ref country code: IE

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

Effective date: 20171205

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

Ref country code: LI

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

Effective date: 20171231

Ref country code: CH

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

Effective date: 20171231

Ref country code: BE

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

Effective date: 20171231

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

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: 20170823

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: 20141205

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

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: 20170823

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170823

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: 20170823

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: 20170823

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: 20170823

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: 20170823

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230602

P02 Opt-out of the competence of the unified patent court (upc) changed

Effective date: 20230818

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

Ref country code: GB

Payment date: 20231220

Year of fee payment: 10

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

Ref country code: SE

Payment date: 20231220

Year of fee payment: 10

Ref country code: NO

Payment date: 20231222

Year of fee payment: 10

Ref country code: IT

Payment date: 20231220

Year of fee payment: 10

Ref country code: FR

Payment date: 20231221

Year of fee payment: 10

Ref country code: FI

Payment date: 20231221

Year of fee payment: 10

Ref country code: DE

Payment date: 20231214

Year of fee payment: 10

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

Ref country code: ES

Payment date: 20240129

Year of fee payment: 10