EP3330390B1 - Nickel-chrom-legierung - Google Patents

Nickel-chrom-legierung Download PDF

Info

Publication number
EP3330390B1
EP3330390B1 EP17207317.3A EP17207317A EP3330390B1 EP 3330390 B1 EP3330390 B1 EP 3330390B1 EP 17207317 A EP17207317 A EP 17207317A EP 3330390 B1 EP3330390 B1 EP 3330390B1
Authority
EP
European Patent Office
Prior art keywords
alloy
nickel
chromium
heating
iron
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
EP17207317.3A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP3330390A1 (de
Inventor
Dietlinde Jakobi
Peter Karduck
Alexander Freiherr Von Richthofen
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.)
Schmidt and Clemens GmbH and Co KG
Original Assignee
Schmidt and Clemens GmbH and Co KG
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 Schmidt and Clemens GmbH and Co KG filed Critical Schmidt and Clemens GmbH and Co KG
Priority to EP19172613.2A priority Critical patent/EP3550045A1/de
Priority to PL17207317T priority patent/PL3330390T3/pl
Publication of EP3330390A1 publication Critical patent/EP3330390A1/de
Application granted granted Critical
Publication of EP3330390B1 publication Critical patent/EP3330390B1/de
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
    • 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
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • 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
    • C22C19/053—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 30% but less than 40%
    • 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

  • petrochemicals require materials that are resistant to both temperature and corrosion and, in particular, have grown on the one hand from the hot product and, on the other hand, from the hot combustion gases of, for example, steam crackers.
  • Their coils are subject to external oxidizing aufstickenden combustion gases with temperatures up to 1100 ° C and more and in the interior at temperatures up to about 900 ° C and optionally also high pressure of a carburizing and oxidizing atmosphere.
  • the carburizing hydrocarbon atmosphere inside the pipes is associated with the danger that diffuses from there the carbon in the pipe material, the carbides in the material and increase from the existing carbide M 23 C 9 with increasing carburizing the carbon-rich carbide M 7 C 6 forms.
  • the consequence of this is internal stresses due to the increase in carbide volume associated with carbide formation or conversion as well as a reduction in the strength and toughness of the tubing material.
  • German patent specification describes 103 02 989 a nickel-chromium casting alloy also suitable as a material for coils of cracking and reforming furnaces with up to 0.8% carbon, 15 to 40% chromium, 0.5 to 13% iron, 1.5 to 7% aluminum, to 0, 2% silicon, to 0.2% manganese, 0.1 to 2.5% niobium, to 11% tungsten and molybdenum, to 1.5% titanium, 0.1 to 0.4% zirconium and 0.01 to 0 , 1% yttrium, balance nickel.
  • This alloy has proven itself in particular when used as a pipe material, although the practice continues to call for pipe materials with extended life.
  • Out JP 2004 052036A is an alloy with 0.1 to 0.6% carbon, 20 to 40% chromium, 1.5 to 4% aluminum, up to 3.0% silicon, up to 3.0% manganese, 20 to 65% nickel with the remainder iron which may also have 0.5 to 5% tungsten, 0.5 to 2% niobium, 0.5 to 5% molybdenum, 0.01 to 0.5% titanium and 0.01 to 0.5% zirconium.
  • the invention is therefore directed to a nickel-chromium alloy having improved durability under conditions such as cracking and reforming of hydrocarbons.
  • the solution to this problem consists in a nickel-chromium alloy with 0.4 to 0.6% carbon, 28 to 33% chromium, 15 to 25% iron, 2 to 6% aluminum, each up to 2% silicon and manganese, respectively up to 1.5% niobium and tantalum, each up to 1.0% tungsten, titanium and zirconium, each up to 0.5% yttrium and cerium, up to 0.5% molybdenum and up to 0.1% nitrogen remainder including nickel impurities caused by melting.
  • this alloy contains, individually or side by side, 17 to 22% iron, 3 to 4.5% aluminum, in each case 0.01 to 1% silicon, to 0.5% manganese, 0.5 to 1.0% niobium, bis 0.5 tantalum, to 0.6% tungsten, 0.001 to 0.5% titanium each, to 0.3% zirconium, to 0.3% yttrium, to 0.3% cerium, 0.01 to 0.5% Molybdenum and 0.001 to 0.1% nitrogen.
  • the alloy according to the invention is characterized in particular by its comparatively high contents of chromium and nickel and by a compelling carbon content within a comparatively narrow range.
  • the silicon improves the oxidation and carburization resistance.
  • the manganese also has a positive effect on the oxidation resistance and additionally on the weldability, deoxidizes the melt and stably binds off the sulfur:
  • Niobium improves creep strength, forms stable carbides and carbonitrides; It also serves as a mixed crystal hardener. Titanium and Tantalum improve creep strength. Even at very low levels, very finely divided carbides and carbonitrides form. At higher levels, titanium and tantalum act as mixed crystal hardeners.
  • Tungsten improves the creep rupture strength. Particularly at high temperatures, tungsten improves the strength by means of solid solution hardening, since the carbides partly dissolve at higher temperatures.
  • Cobalt also improves creep strength by means of solid solution hardening, zirconium through the formation of carbides, especially in conjunction with titanium and tantalum.
  • Yttrium and cerium obviously not only improve the oxidation resistance and especially the adhesion and growth of the Al 2 O 3 cover layer.
  • yttrium and cerium improve the creep resistance even at very low levels, since they stably bind the remaining free sulfur.
  • Low levels of boron also improve creep strength, prevent sulfur segregation, and retard aging by coarsening the M 23 C 6 carbides.
  • Molybdenum also improves the creep rupture strength, especially at high temperatures, by means of solid solution hardening. Especially because at high temperatures, the carbides partially go into solution.
  • the nitrogen improves the creep rupture strength by means of carbonitride formation, while hafnium, even at low levels, improves the oxidation resistance by means of better adhesion of the cover layer and has a positive effect on the creep rupture strength.
  • Phosphorous, sulfur, zinc, lead, arsenic, bismuth, tin and tellurium are among the impurities, their contents should therefore be as low as possible.
  • the alloy is particularly suitable as a casting material for components of petrochemical plants, for example for the production of coils for cracking and reforming furnaces, reformer tubes, but also as a material for iron ore direct reduction plants and for similarly stressed components.
  • these include furnace parts, radiant tubes for heating ovens, rolls for annealing furnaces, parts of Strip and strip casting plants, hoods and sleeves for annealing furnaces, parts of large diesel engines and shaped bodies for catalyst fillings.
  • the alloy is characterized by a high oxidation and carburization resistance as well as good creep strength and creep resistance.
  • the inner surface of cracking or reformer tubes is characterized by a catalytically inert, aluminum-containing oxide layer, thus preventing the formation of catalytic coke strands, known as carbon nanotubes.
  • the properties that characterize the material also remain with multiple burn-out of the coke which inevitably deposits on the inner wall of the pipes during cracking.
  • the alloy for producing centrifugally cast tubes if they are drilled with a contact pressure of 10 to 40 MPa, for example 10 to 25 MPa. In such a boring occurs due to the contact pressure to a cold deformation or work hardening of the pipe material in a near-surface zone with depths of, for example, 0.1 to 0.5 mm.
  • the cold-worked zone recrystallizes, resulting in a very fine-grained microstructure.
  • the recrystallization structure enhances the diffusion of the oxide-forming elements aluminum and chromium, which promotes the formation of a closed layer of high density and stability consisting primarily of alumina.
  • the resulting adherent aluminum-containing oxide forms a closed protective layer of the tube inner wall, which is largely free of catalytically active centers such as nickel or iron and even after a prolonged cyclic heat stress is still stable.
  • This aluminum-containing oxide layer prevents, in contrast to other pipe materials without such a cover layer, the penetration of oxygen into the base material and thus an internal oxidation of the pipe material.
  • the cover layer suppresses not only the carburizing of the pipe material, but also corrosion by impurities in the process gas.
  • the top layer consists mainly of Al 2 O 3 and the mixed oxide (Al, Cr) 2 O 3 and is largely inert to a catalytic coke formation. It is poor in elements that catalyze coke formation, such as iron and nickel.
  • a durable oxide protective layer serves to condition, for example, the inner surface of steam cracker pipes after their installation when the relevant furnace is heated to its operating temperature.
  • This conditioning can be carried out as heating with interposed isothermal heat treatments in a furnace atmosphere, which is set during the heating according to the invention, for example in a very weakly oxidizing water vapor-containing atmosphere with an oxygen partial pressure of at most 10 -20 , preferably at most 10 -30 bar.
  • Particularly suitable is a protective gas atmosphere of 0.1 to 10 mol% of water vapor, 7 to 99.9 mol% of hydrogen and hydrocarbon individually or side by side and 0 to 88 mol% noble gases.
  • the atmosphere during the conditioning preferably consists of an extremely weakly oxidizing mixture of water vapor, hydrogen, hydrocarbons and noble gases in an amount such that the oxygen partial pressure of the mixture at a temperature of 600 ° C is less than 10 -20 bar, preferably less than 10 -30 bar is.
  • the initial heating of the tube interior after a previous mechanical removal of a surface layer, d. H. the separate heating of the resulting cold-formed surface zone is preferably carried out under very weak oxidizing inert gas in several phases each at a rate of 10 to 100 ° C / h initially to 400 to 750 ° C, preferably about 550 ° C at the inner surface of the tube.
  • This heating phase is followed by holding for one to fifty hours within the temperature range mentioned.
  • the heating takes place in the presence of a steam atmosphere as soon as the temperature has reached a value which precludes the formation of condensed water. Following this holding the tube is then brought to the operating temperature, for example to 800 to 900 ° C and is ready for operation.
  • the tube temperature gradually increases in the cracking operation as a result of the deposition of pyrolytic coke and finally reaches about 1000 ° C or even 1050 ° C on the inner surface.
  • the inner layer consisting essentially of Al 2 O 3 and to a small extent of (Al, Cr) 2 O 3 converts from a transition oxide such as ⁇ , ⁇ or ⁇ -Al 2 O 3 into stable ⁇ -aluminum oxide.
  • the tube has reached its operating state with its mechanically removed inner layer in a multi-stage, but preferably eintoxicityen method.
  • This precursor includes initial heating after abrading the inner surface to holding at 400 to 750 ° C.
  • the pipe thus pretreated can then be further processed in situ, for example in another manufacturing facility, starting from its cold state in the manner described above, that is to say in another factory. H. be brought to the operating temperature in the installed state.
  • the mentioned separate pre-treatment is not limited to tubes, but is also suitable for a partial or complete conditioning of surface zones of other workpieces, which are then treated according to their nature and use as in the invention or by other methods, but with a defined initial state.
  • alloy 9 experiences no internal oxidation even after more than 200 cycles of annealing at 1150 ° C for 45 minutes, whereas the two comparative alloys 12 and 13 show increasing weight loss after only a few cycles as a result of catastrophic oxidation.
  • the alloy 9 is also characterized by a high carburization resistance; because, according to the diagram of FIG. 2, it has the lowest weight gain after all three carburizing treatments, compared with the conventional alloys 12 and 13, due to the low weight gain.
  • FIGS. 3a and 3b show that the creep strength of the nickel alloy 11 is even better in a substantial range than in the case of the two comparative alloys 12 and 13.
  • the exception here is the alloy 15, which is not covered by the invention because of its low iron content. however, with their much lower oxidation, carburization and coking resistance.
  • FIGS. 5 and 6 Examples of the surface condition of the tube interior of furnace tubes with the composition of the alloy 8 are shown in FIGS. 5 and 6.
  • the FIGS Figure 6 (Experiment 7 according to Table II) shows the superiority of a surface after a conditioning according to the invention in comparison to the Figure 5 , which relates to a not according to the invention conditioned surface (Table II, Experiment 2).
  • FIG. 7 Shown in Figures 7 (Alloy 14) and 8 are shallow areas in cross section.
  • the samples were heated to 950 ° C and then subjected to 10 crack cycles of 10 hours each in an atmosphere of water vapor, hydrogen and hydrocarbons. After each cycle, the sample tubes were burned out for one hour to remove the coke deposits.
  • the micrograph of the image 7 in the form of the dark areas shows the large-area and thus bulky result of internal oxidation on the inside of a tube in a conventional nickel-chromium casting alloy compared to the micrograph of the image 8 of the alloy 9, which is virtually none Internal oxidation, although both samples were similarly subjected to multiple cyclic treatment from cracking on the one hand and removal of the carbon deposits on the other.
  • Figure 11 relates to an SEM top view of the conventional sample shown in Figure 7 in section; Due to the missing cover layer, it shows a catastrophic oxidation and a corresponding catastrophic formation of catalytic coke in the form of carbon nanotubes.
  • the stability of the oxide layer on an alloy according to the invention is particularly clear from the course of the aluminum concentration over the depth of the edge zone after ten cracking phases with respective removal of the coke deposits by burnout in an intermediate phase when the diagrams according to FIGS. 9 and 10 are compared of the image 9 in the near-surface region due to the local failure of the protective overcoat and then onset of strong internal aluminum oxidation of the material is depleted of aluminum, the aluminum concentration in the diagram of the image 10 moves approximately at the initial level of the casting material. This clearly shows the importance of a continuous, dense and in particular firmly adhering inner aluminum-containing oxide layer in the tubes according to the invention.
  • the stability of the aluminum-containing oxide layer was also investigated by long-term tests in a laboratory plant under process-related conditions.
  • the samples of alloys 9 and 11 were heated to 950 ° C. under steam and then subjected to cracking at this temperature three times each for 72 hours; they were then subjected to burnout at 900 ° C for four hours each.
  • Image 12 shows the closed aluminum-containing oxide layer after the three crack cycles and beyond how the aluminum-containing oxide layer covers the material itself over chromium carbides in the surface. It can be seen that chromium carbides present on the surface are completely covered by the aluminum-containing oxide layer.
  • the inventive nickel-chromium-iron alloy is characterized, for example, as a pipe material after removal of the inner surface under mechanical pressure and a subsequent multi-stage in situ heat treatment for conditioning the inner surface by a high oxidation, corrosion and especially high Creep rupture and creep resistance.
EP17207317.3A 2008-10-13 2009-10-13 Nickel-chrom-legierung Active EP3330390B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP19172613.2A EP3550045A1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung
PL17207317T PL3330390T3 (pl) 2008-10-13 2009-10-13 Stop niklowo-chromowy

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE102008051014A DE102008051014A1 (de) 2008-10-13 2008-10-13 Nickel-Chrom-Legierung
EP09744619.9A EP2350329B1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung
PCT/EP2009/007345 WO2010043375A1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung

Related Parent Applications (2)

Application Number Title Priority Date Filing Date
EP09744619.9A Division EP2350329B1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung
PCT/EP2009/007345 Previously-Filed-Application WO2010043375A1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung

Related Child Applications (2)

Application Number Title Priority Date Filing Date
EP19172613.2A Division-Into EP3550045A1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung
EP19172613.2A Division EP3550045A1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung

Publications (2)

Publication Number Publication Date
EP3330390A1 EP3330390A1 (de) 2018-06-06
EP3330390B1 true EP3330390B1 (de) 2019-08-28

Family

ID=41491665

Family Applications (3)

Application Number Title Priority Date Filing Date
EP19172613.2A Withdrawn EP3550045A1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung
EP17207317.3A Active EP3330390B1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung
EP09744619.9A Active EP2350329B1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung

Family Applications Before (1)

Application Number Title Priority Date Filing Date
EP19172613.2A Withdrawn EP3550045A1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP09744619.9A Active EP2350329B1 (de) 2008-10-13 2009-10-13 Nickel-chrom-legierung

Country Status (20)

Country Link
US (2) US9249482B2 (es)
EP (3) EP3550045A1 (es)
JP (4) JP2012505314A (es)
KR (4) KR102064375B1 (es)
CN (1) CN102187003B (es)
BR (2) BRPI0920279B1 (es)
CA (1) CA2740160C (es)
DE (1) DE102008051014A1 (es)
EA (1) EA020052B1 (es)
ES (2) ES2747898T3 (es)
HU (2) HUE046718T2 (es)
IL (1) IL212098A (es)
MX (1) MX2011003923A (es)
MY (1) MY160131A (es)
PL (2) PL3330390T3 (es)
PT (2) PT2350329T (es)
TR (1) TR201802979T4 (es)
UA (1) UA109631C2 (es)
WO (1) WO2010043375A1 (es)
ZA (1) ZA201102259B (es)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2019034845A1 (en) 2017-08-15 2019-02-21 Paralloy Limited ALLOY RESISTANT TO OXIDATION

Families Citing this family (49)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102008051014A1 (de) * 2008-10-13 2010-04-22 Schmidt + Clemens Gmbh + Co. Kg Nickel-Chrom-Legierung
DE102012011162B4 (de) 2012-06-05 2014-05-22 Outokumpu Vdm Gmbh Nickel-Chrom-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
DE102012011161B4 (de) * 2012-06-05 2014-06-18 Outokumpu Vdm Gmbh Nickel-Chrom-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
US9377245B2 (en) 2013-03-15 2016-06-28 Ut-Battelle, Llc Heat exchanger life extension via in-situ reconditioning
US9540714B2 (en) 2013-03-15 2017-01-10 Ut-Battelle, Llc High strength alloys for high temperature service in liquid-salt cooled energy systems
US10017842B2 (en) 2013-08-05 2018-07-10 Ut-Battelle, Llc Creep-resistant, cobalt-containing alloys for high temperature, liquid-salt heat exchanger systems
US9435011B2 (en) 2013-08-08 2016-09-06 Ut-Battelle, Llc Creep-resistant, cobalt-free alloys for high temperature, liquid-salt heat exchanger systems
EP3070184B1 (en) * 2013-11-12 2018-06-13 Nippon Steel & Sumitomo Metal Corporation Ni-Cr ALLOY MATERIAL AND OIL WELL SEAMLESS PIPE USING SAME
US9683280B2 (en) 2014-01-10 2017-06-20 Ut-Battelle, Llc Intermediate strength alloys for high temperature service in liquid-salt cooled energy systems
DE102014001329B4 (de) 2014-02-04 2016-04-28 VDM Metals GmbH Verwendung einer aushärtenden Nickel-Chrom-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001330B4 (de) 2014-02-04 2016-05-12 VDM Metals GmbH Aushärtende Nickel-Chrom-Kobalt-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
US11674212B2 (en) 2014-03-28 2023-06-13 Kubota Corporation Cast product having alumina barrier layer
JP6247977B2 (ja) * 2014-03-28 2017-12-13 株式会社クボタ アルミナバリア層を有する鋳造製品
ES2549704B1 (es) 2014-04-30 2016-09-08 Abengoa Hidrógeno, S.A. Tubo reactor de reformado con vapor de agua
US9683279B2 (en) 2014-05-15 2017-06-20 Ut-Battelle, Llc Intermediate strength alloys for high temperature service in liquid-salt cooled energy systems
US9605565B2 (en) 2014-06-18 2017-03-28 Ut-Battelle, Llc Low-cost Fe—Ni—Cr alloys for high temperature valve applications
WO2016023745A1 (de) * 2014-08-13 2016-02-18 Basf Se Verfahren zur herstellung von ethylenhaltigem spaltgas und spaltrohr zur verwendung in dem verfahren
CN104404349A (zh) * 2014-11-03 2015-03-11 无锡贺邦金属制品有限公司 镍铬合金压铸件
CN104404338A (zh) * 2014-11-04 2015-03-11 无锡贺邦金属制品有限公司 一种镍铬基合金冲压件
CN104404343A (zh) * 2014-11-04 2015-03-11 无锡贺邦金属制品有限公司 镍铬合金冲压件
RU2581337C1 (ru) * 2015-06-10 2016-04-20 Акционерное общество "Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения" АО "НПО "ЦНИИТМАШ" Жаропрочный сплав на основе никеля для литья деталей горячего тракта газотурбинных установок, имеющих равноосную структуру
CN105755321A (zh) * 2016-03-31 2016-07-13 苏州睿昕汽车配件有限公司 汽车柴油机高强度活塞材料的制备方法
EP3287535A1 (de) * 2016-08-22 2018-02-28 Siemens Aktiengesellschaft Sx-nickel-legierung mit verbesserten tmf-eigenschaften, rohmaterial und bauteil
DE102016012907A1 (de) 2016-10-26 2018-04-26 Schmidt + Clemens Gmbh + Co. Kg Tieflochbohrverfahren sowie Werkzeug für eine Tieflochbohrmaschine und Tieflochbohrmaschine
US11612967B2 (en) 2016-11-09 2023-03-28 Kubota Corporation Alloy for overlay welding and reaction tube
JP6335247B2 (ja) * 2016-11-09 2018-05-30 株式会社クボタ 内面突起付反応管
WO2018088069A1 (ja) * 2016-11-09 2018-05-17 株式会社クボタ 肉盛溶接用合金、溶接用粉末及び反応管
JP6335248B2 (ja) * 2016-11-09 2018-05-30 株式会社クボタ 肉盛溶接用合金及び溶接用粉末
IL269775B2 (en) 2017-04-07 2024-04-01 Schmidt Clemens Gmbh Co Kg Pipeline and device for thermal splitting of hydrocarbons
FI3384981T3 (fi) 2017-04-07 2024-04-04 Schmidt Clemens Gmbh Co Kg Putki ja laite hiilivetyjen termiseen krakkaukseen
DE102017003409B4 (de) 2017-04-07 2023-08-10 Schmidt + Clemens Gmbh + Co. Kg Rohr und Vorrichtung zum thermischen Spalten von Kohlenwasserstoffen
CA3075483C (en) 2017-09-12 2022-07-05 Exxonmobil Chemical Patents Inc. Aluminum oxide forming heat transfer tube for thermal cracking
JP6422608B1 (ja) 2017-11-06 2018-11-14 株式会社クボタ 耐熱合金及び反応管
CN107739896A (zh) * 2017-11-28 2018-02-27 宁波市鄞州龙腾工具厂 一种拖车组件
KR101998979B1 (ko) * 2017-12-07 2019-07-10 주식회사 포스코 고온변형 저항성 및 균열 저항성이 우수한 복사관용 Ｃｒ-Ｎｉ계 합금 및 그 제조방법
JP7016283B2 (ja) * 2018-04-25 2022-02-04 株式会社クボタ 耐高温腐食性を有する耐熱合金、溶接用粉末及び外周面に肉盛溶接層を具える配管
FR3082209B1 (fr) 2018-06-07 2020-08-07 Manoir Pitres Alliage austenitique avec haute teneur en aluminium et procede de conception associe
CN109112327B (zh) * 2018-11-08 2019-09-03 青岛新力通工业有限责任公司 一种抗氧化耐热合金及制备方法
US20220017827A1 (en) * 2018-12-20 2022-01-20 Exxonmobil Chemical Patents Inc. Erosion Resistant Alloy for Thermal Cracking Reactors
CN110016602B (zh) * 2019-04-22 2020-06-02 陕西科技大学 一种Laves相Cr2Nb基高温合金
WO2021087133A1 (en) * 2019-11-01 2021-05-06 Exxonmobil Chemical Patents Inc. Bimetallic materials comprising cermets with improved metal dusting corrosion and abrasion/erosion resistance
JP2021127517A (ja) 2020-02-14 2021-09-02 日本製鉄株式会社 オーステナイト系ステンレス鋼材
US11413744B2 (en) 2020-03-03 2022-08-16 Applied Materials, Inc. Multi-turn drive assembly and systems and methods of use thereof
CN111850348B (zh) * 2020-07-30 2021-11-09 北京北冶功能材料有限公司 一种高强高韧镍基高温合金箔材及其制备方法
CN112853155A (zh) * 2021-01-08 2021-05-28 烟台玛努尔高温合金有限公司 具有优异高温耐腐蚀性和抗蠕变性的高铝奥氏体合金
US11866809B2 (en) 2021-01-29 2024-01-09 Ut-Battelle, Llc Creep and corrosion-resistant cast alumina-forming alloys for high temperature service in industrial and petrochemical applications
US11479836B2 (en) 2021-01-29 2022-10-25 Ut-Battelle, Llc Low-cost, high-strength, cast creep-resistant alumina-forming alloys for heat-exchangers, supercritical CO2 systems and industrial applications
CN113073234B (zh) * 2021-03-23 2022-05-24 成都先进金属材料产业技术研究院股份有限公司 镍铬系高电阻电热合金及其制备方法
CN113444950B (zh) * 2021-07-08 2022-04-29 烟台新钢联冶金科技有限公司 一种硅钢高温加热炉用铬基高氮合金垫块及其制备方法

Family Cites Families (31)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR929727A (fr) 1944-02-24 1948-01-06 William Jessop Ans Sons Ltd Acier au nickel-chrome à caractère austénitique
US2564498A (en) * 1949-08-26 1951-08-14 Gen Electric Preparation of alloys
DE1096040B (de) 1953-08-11 1960-12-29 Wiggin & Co Ltd Henry Verfahren zur Herstellung einer Nickellegierung hoher Kriechfestigkeit bei hohen Temperaturen
US3306736A (en) 1963-08-30 1967-02-28 Crucible Steel Co America Austenitic stainless steel
DE2105750C3 (de) 1971-02-08 1975-04-24 Battelle-Institut E.V., 6000 Frankfurt Verwendung einer Chrombasislegierung zur Herstellung von Feingußoder FormguBkörhern
JPS5040099B1 (es) * 1971-03-09 1975-12-22
JPS5631345B2 (es) 1972-01-27 1981-07-21
GB2017148B (en) 1978-03-22 1983-01-12 Pompey Acieries Nickel chromium iron alloys possessing very high resistantance to carburization at very high temperature
FR2429843A2 (fr) 1978-06-29 1980-01-25 Pompey Acieries Alliages refractaires a base de nickel et de chrome, possedant une resistance tres elevee a la carburation a tres haute temperature
US4388125A (en) * 1981-01-13 1983-06-14 The International Nickel Company, Inc. Carburization resistant high temperature alloy
JPS57131348A (en) * 1981-02-09 1982-08-14 Nippon Steel Corp Heat and wear resistant build-up welding material
JPS5837160A (ja) 1981-08-27 1983-03-04 Mitsubishi Metal Corp 継目無鋼管製造用熱間傾斜圧延機のガイドシユ−用鋳造合金
AU547863B2 (en) * 1981-09-02 1985-11-07 Exxon Research And Engineering Company Heat resistant, alumina forming (ni+cr) based oxidation and carburisation resistant alloy
JPS6353234A (ja) 1986-08-22 1988-03-07 Toshiba Corp 耐熱・高強度構造部材
US4787945A (en) * 1987-12-21 1988-11-29 Inco Alloys International, Inc. High nickel chromium alloy
JPH02263895A (ja) 1989-04-03 1990-10-26 Sumitomo Metal Ind Ltd 耐コーキング性に優れたエチレン分解炉管およびその製造方法
US5306358A (en) 1991-08-20 1994-04-26 Haynes International, Inc. Shielding gas to reduce weld hot cracking
DE19524234C1 (de) * 1995-07-04 1997-08-28 Krupp Vdm Gmbh Knetbare Nickellegierung
JPH09243284A (ja) * 1996-03-12 1997-09-19 Kubota Corp 内面突起付き熱交換用管
CA2175439C (en) * 1996-04-30 2001-09-04 Sabino Steven Anthony Petrone Surface alloyed high temperature alloys
DK173136B1 (da) * 1996-05-15 2000-02-07 Man B & W Diesel As Bevægeligt vægelement i form af en udstødsventilspindel eller et stempel i en forbrændingsmotor.
KR100372482B1 (ko) * 1999-06-30 2003-02-17 스미토모 긴조쿠 고교 가부시키가이샤 니켈 베이스 내열합금
JP3644532B2 (ja) 1999-07-27 2005-04-27 住友金属工業株式会社 熱間加工性、溶接性および耐浸炭性に優れたＮｉ基耐熱合金
JP4256614B2 (ja) 2002-01-31 2009-04-22 三菱重工業株式会社 高クロム−高ニッケル系耐熱合金
JP2004052036A (ja) 2002-07-19 2004-02-19 Kubota Corp 耐浸炭性にすぐれる加熱炉用部材
US20050131263A1 (en) 2002-07-25 2005-06-16 Schmidt + Clemens Gmbh + Co. Kg, Process and finned tube for the thermal cracking of hydrocarbons
JP4415544B2 (ja) 2002-12-17 2010-02-17 住友金属工業株式会社 高温強度に優れた耐メタルダスティング金属材料
DE10302989B4 (de) * 2003-01-25 2005-03-03 Schmidt + Clemens Gmbh & Co. Kg Verwendung einer Hitze- und korrosionsbeständigen Nickel-Chrom-Stahllegierung
JPWO2005078148A1 (ja) 2004-02-12 2007-10-18 住友金属工業株式会社 浸炭性ガス雰囲気下で使用するための金属管
DE102006053917B4 (de) 2005-11-16 2019-08-14 Ngk Spark Plug Co., Ltd. Für Verbrennungsmotoren benutzte Zündkerze
DE102008051014A1 (de) * 2008-10-13 2010-04-22 Schmidt + Clemens Gmbh + Co. Kg Nickel-Chrom-Legierung

Non-Patent Citations (1)

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

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2019034845A1 (en) 2017-08-15 2019-02-21 Paralloy Limited ALLOY RESISTANT TO OXIDATION

Also Published As

Publication number Publication date
HUE046718T2 (hu) 2020-03-30
CN102187003B (zh) 2013-11-06
KR102029019B1 (ko) 2019-10-07
MX2011003923A (es) 2011-05-03
BRPI0920279B1 (pt) 2020-09-15
MY160131A (en) 2017-02-28
EA020052B1 (ru) 2014-08-29
KR102080674B1 (ko) 2020-02-24
BR122016030244A2 (pt) 2017-08-29
PL2350329T3 (pl) 2018-05-30
EP2350329A1 (de) 2011-08-03
EP2350329B1 (de) 2017-12-20
PT3330390T (pt) 2019-10-24
WO2010043375A1 (de) 2010-04-22
ES2747898T3 (es) 2020-03-12
CA2740160A1 (en) 2010-04-22
IL212098A (en) 2017-10-31
JP2018131690A (ja) 2018-08-23
KR102064375B1 (ko) 2020-01-09
KR20110079881A (ko) 2011-07-11
PL3330390T3 (pl) 2020-05-18
IL212098A0 (en) 2011-06-30
US9249482B2 (en) 2016-02-02
ES2661333T3 (es) 2018-03-28
JP2012505314A (ja) 2012-03-01
CA2740160C (en) 2016-07-12
JP2017128815A (ja) 2017-07-27
KR101738390B1 (ko) 2017-05-22
KR20190112208A (ko) 2019-10-02
JP6486532B2 (ja) 2019-03-20
HUE037289T2 (hu) 2018-08-28
EA201170560A1 (ru) 2011-12-30
US20160108501A1 (en) 2016-04-21
JP6320590B2 (ja) 2018-05-09
DE102008051014A1 (de) 2010-04-22
EP3330390A1 (de) 2018-06-06
US20110272070A1 (en) 2011-11-10
US10053756B2 (en) 2018-08-21
KR20170058442A (ko) 2017-05-26
ZA201102259B (en) 2011-11-30
CN102187003A (zh) 2011-09-14
UA109631C2 (xx) 2015-09-25
PT2350329T (pt) 2018-03-08
JP2014185397A (ja) 2014-10-02
EP3550045A1 (de) 2019-10-09
TR201802979T4 (tr) 2018-03-21
KR20190137965A (ko) 2019-12-11

Similar Documents

Publication Publication Date Title
EP3330390B1 (de) Nickel-chrom-legierung
DE10302989B4 (de) Verwendung einer Hitze- und korrosionsbeständigen Nickel-Chrom-Stahllegierung
DE60004737T2 (de) Hitzebeständige Nickelbasislegierung
DE60224277T2 (de) Metallwerkstoff mit guter beständigkeit gegen metal dusting
EP2855723B1 (de) Nickel-chrom-aluminium-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit
EP2855724B1 (de) Nickel-chrom-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit
DE3046412A1 (de) Verfahren zur hochtemperaturbehandlung von kohlenwasserstoffhaltigen materialien
DE102019216995A1 (de) Lagerbauteil mit einem metallischen Grundkörper und einer Beschichtung mit legiertem Stahl
DE102018107248A1 (de) Verwendung einer nickel-chrom-eisen-aluminium-legierung
CH666288A5 (de) Matrize aus stahl, verfahren zu deren herstellung und deren verwendung.
DE19629977A1 (de) Austenitische Nickel-Chrom-Stahllegierung
WO2020094285A1 (de) Gehärtetes bauteil umfassend ein stahlsubstrat und eine korrosionsschutzbeschichtung, entsprechendes bauteil zur herstellung des gehärteten bauteils sowie herstellverfahren und verwendung
DE60124936T2 (de) Geschichtete Oberflächenbeschichtung auf nichtrostendem Stahl und Verfahren zu deren Herstellung
DE4035114C2 (de) Fe-Cr-Ni-Al Ferritlegierungen
EP1630243B1 (de) Verfahren zum Herstellen eines Bauteils
DE10255372A1 (de) Verwendung Quasi-Kristalliner Aluminiumlegierungen bei Anwendungen in der Raffination und der Petrochemie
DE1533429C3 (de) Verwendung einer Chrom-Nickel-Kobalt-Stahllegierung als korrosionsbeständiger Werkstoff
DE3121782C2 (de) Verwendung einer austenitischen Chrom-Nickel-Stahllegierung für Wärmetauscherkomponenten
WO2010009718A2 (de) Bauteil bestehend aus einem unlegierten oder niedriglegierten stahl, verfahren zum schutz dieser bauteile gegen coke-abscheidung bzw. metal-dusting
DE102022110383A1 (de) Verwendung einer Nickel-Eisen-Chrom-Legierung mit hoher Beständigkeit in aufkohlenden und sulfidierenden und chlorierenden Umgebungen und gleichzeitig guter Verarbeitbarkeit und Festigkeit
DE102022110384A1 (de) Verwendung einer Nickel-Eisen-Chrom-Legierung mit hoher Beständigkeit in hoch korrosiven Umgebungen und gleichzeitig guter Verarbeitbarkeit und Festigkeit
EP0041601B1 (de) Verwendung einer Eisen-Nickel-Chrom-Legierung für Gegenstände mit hoher Zeitstandfestigkeit, Korrosionsbeständigkeit und grosser Gefügestabilität
DE3306540A1 (de) Verfahren und legierungen zur herstellung geschmiedeter bestandteile fuer gasgekuehlte hochtemperaturreaktoren
DE4409004A1 (de) Hitzebeständiger Mehrschichtverbundwerkstoff

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

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

Free format text: STATUS: THE APPLICATION HAS BEEN PUBLISHED

AC Divisional application: reference to earlier application

Ref document number: 2350329

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): 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 SE SI SK SM TR

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

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20180622

RBV Designated contracting states (corrected)

Designated state(s): 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 SE SI SK SM TR

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

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20180907

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

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

Free format text: STATUS: GRANT OF PATENT IS INTENDED

TPAC Observations filed by third parties

Free format text: ORIGINAL CODE: EPIDOSNTIPA

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

INTG Intention to grant announced

Effective date: 20181030

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

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

Free format text: STATUS: EXAMINATION IS IN PROGRESS

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

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

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTC Intention to grant announced (deleted)
INTG Intention to grant announced

Effective date: 20190404

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

Owner name: SCHMIDT + CLEMENS GMBH + CO. KG

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

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

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AC Divisional application: reference to earlier application

Ref document number: 2350329

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): 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 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

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502009015933

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1172490

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190915

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: RO

Ref legal event code: EPE

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: NL

Ref legal event code: FP

REG Reference to a national code

Ref country code: PT

Ref legal event code: SC4A

Ref document number: 3330390

Country of ref document: PT

Date of ref document: 20191024

Kind code of ref document: T

Free format text: AVAILABILITY OF NATIONAL TRANSLATION

Effective date: 20191001

REG Reference to a national code

Ref country code: NO

Ref legal event code: T2

Effective date: 20190828

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: 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: 20190828

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: 20190828

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: 20191228

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: 20190828

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: 20191129

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2747898

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20200312

REG Reference to a national code

Ref country code: HU

Ref legal event code: AG4A

Ref document number: E046718

Country of ref document: HU

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

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: 20190828

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: 20190828

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

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: 20190828

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: 20190828

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: 20200224

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: 20190828

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502009015933

Country of ref document: DE

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

PG2D Information on lapse in contracting state deleted

Ref country code: IS

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

Ref country code: LU

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

Effective date: 20191013

Ref country code: LI

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

Effective date: 20191031

Ref country code: CH

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

Effective date: 20191031

26N No opposition filed

Effective date: 20200603

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: 20190828

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: 20191013

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: 20190828

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: 20190828

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: 20190828

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

Ref country code: BE

Payment date: 20221020

Year of fee payment: 14

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

Effective date: 20230513

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

Ref country code: PL

Payment date: 20230928

Year of fee payment: 15

Ref country code: NL

Payment date: 20231023

Year of fee payment: 15

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

Ref country code: GB

Payment date: 20231025

Year of fee payment: 15

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

Ref country code: ES

Payment date: 20231117

Year of fee payment: 15

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

Ref country code: TR

Payment date: 20231005

Year of fee payment: 15

Ref country code: SE

Payment date: 20231025

Year of fee payment: 15

Ref country code: RO

Payment date: 20231004

Year of fee payment: 15

Ref country code: PT

Payment date: 20230929

Year of fee payment: 15

Ref country code: NO

Payment date: 20231023

Year of fee payment: 15

Ref country code: IT

Payment date: 20231031

Year of fee payment: 15

Ref country code: HU

Payment date: 20231005

Year of fee payment: 15

Ref country code: FR

Payment date: 20231023

Year of fee payment: 15

Ref country code: FI

Payment date: 20231023

Year of fee payment: 15

Ref country code: DE

Payment date: 20231120

Year of fee payment: 15

Ref country code: CZ

Payment date: 20231002

Year of fee payment: 15

Ref country code: BG

Payment date: 20231019

Year of fee payment: 15

Ref country code: AT

Payment date: 20231019

Year of fee payment: 15

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

Ref country code: BE

Payment date: 20231023

Year of fee payment: 15