EP3812479B1 - R6 high toughness offshore mooring chain steel applicable to anchor moored positioning cathodic protection floating body and mooring chain thereof - Google Patents

R6 high toughness offshore mooring chain steel applicable to anchor moored positioning cathodic protection floating body and mooring chain thereof Download PDF

Info

Publication number
EP3812479B1
EP3812479B1 EP19925101.8A EP19925101A EP3812479B1 EP 3812479 B1 EP3812479 B1 EP 3812479B1 EP 19925101 A EP19925101 A EP 19925101A EP 3812479 B1 EP3812479 B1 EP 3812479B1
Authority
EP
European Patent Office
Prior art keywords
chain
toughness
grade
strength
mooring
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
EP19925101.8A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP3812479A4 (en
EP3812479A1 (en
Inventor
Jiang YIN
Xuejun Bao
Zhenwei Liu
Yun Bai
Xiaohong Xu
Ming Zhang
Haidong Fan
Yao Li
Hongli Li
De Chen
Guorong Zhu
Guoren HU
Tiehua YAO
Qiuhao GU
Yong Cui
Erxin HUANG
Xuewen Liu
Liangliang LI
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.)
Jiangyin Xingcheng Special Steel Works Co Ltd
Original Assignee
Jiangyin Xingcheng Special Steel Works Co Ltd
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 Jiangyin Xingcheng Special Steel Works Co Ltd filed Critical Jiangyin Xingcheng Special Steel Works Co Ltd
Publication of EP3812479A1 publication Critical patent/EP3812479A1/en
Publication of EP3812479A4 publication Critical patent/EP3812479A4/en
Application granted granted Critical
Publication of EP3812479B1 publication Critical patent/EP3812479B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
    • C21D9/505—Cooling thereof
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0087—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for chains, for chain links
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints

Definitions

  • the present application relates to alloy steel and ferrous metallurgical products for offshore engineering, in particular a grade R6 steel and chain for offshore mooring in the steel series for offshore mooring chain and the evaluation of its offshore environmental performance degradation resistance.
  • a mooring system is acquired for positioning and mooring with floating bodies in the process of the marine exploration, deep-sea oil and gas extraction, national defense construction and so on.
  • the main component of the mooring system is offshore mooring chain by the steel.
  • the offshore mooring chain can be classified into six grades called R3, R3S, R4, R4S, R5, and R6 according to its strength grading.
  • the tensile strength of the chains at all grades after overall quenching-tempering shall be equal or greater than 690 MPa, 770 MPa, 860 MPa, 960 MPa, 1000 MPa, and 1100 MPa respectively.
  • the grade R5 is the highest grade of the mooring chain produced and used at home and abroad by the first half of the year of 2018.
  • the long mooring chain for positioning can be divided into two types which are stud and studless for drilling type and production type of the floating bodies respectively.
  • the length of a single chain can reach several kilometers. Alloy steel bars of diameter 52-230 mm are used accordingly. All offshore mooring chain steels have an ultrahigh strength, as marine steel with a tensile strength above 690 MPa is ultrahigh-strength steel according to DNVGL.
  • the qualified mechanical properties and service performance of the offshore mooring chain are requisite in the offshore environment.
  • its toughness especially the toughness of the flash weld area, must be ensured for the safety and reliability for resisting wild winds and huge waves.
  • the chain is usually continuously treated in a special vertical furnace, i.e. the final performance of the chain is obtained after continuous quenching and tempering heat treatment.
  • the accessories are forged from the steel, and their final properties are obtained through intermittent heat treatment.
  • DNVGL has defined grade R6 chain as the extreme technology and performance of the offshore mooring chain since 2013, and the provisional standard was not be terminated until 2018. DNVGL officially announced a standards includeing the grade R6 chain, specifying the performance of the chain and the basic process requirements of the production of the chain steel in July 2018.
  • DNVGL also proposed an additional standard named Class programme-DNVGL-CP-0237, Edition July 2018, Offshore mooring chain and accessories which evaluates the EAC (environment assisted cracking) of grade R6 chain under CP (cathodic protection) conditions according to the standards of ASTM G129 and ASTM E1820.
  • the specific requirement is to carry out two tests: the one is SSRT with the applied potential of -850 mV, -1200 mV(saturated calomel electrode SCE) and strain rate of ⁇ 10 -5 /s; the other is the K IEAC test (fracture toughness type I in seawater) with CT (conpact tension) specimen, applied potential of -950 mV, -1050mV (SCE) and the test speed of ⁇ 6x10 -9 m/s in seawater. So as to evaluate the degradation resistance of grade R6 chain in the seawater environment.
  • the seawater environment is generally considered as the service forbidden zone for ultrahigh-strength steel with yield strength over 1000MPa.
  • the main way to lighten the chain is ultrahigh intensification. There is a restraining relationship each other between strength and toughness, and the same is true of the relationship between strength and deterioration resistance of service performance in the seawater environment. Once the strength is improved, there must be a decrease of toughness, plasticity and the degradation resistance in the seawater environment performance. But according to DNVGL, when the strength is increased, the toughness is increased instead of decreasing with its EAC evaluated at the same time.
  • DNVGL proposes the above additional requirements for the evaluation of EAC of the chain by impressed cathodic protection potential of the grade R6 chain for the sake of reliability. This is a new challenge in the research and development of the ultrahigh-strength chain.
  • Vanadium are the element for refining or strengthening effect in the form of VC in the invention.
  • the invention does not cover the technology to balance corrosion potential and cathodic protection potential to prevent embrittlement by hydrogen generation of the chain caused by cathodic overprotection, coping with new standard.
  • the content of evaluating the embrittlement by hydrogen generation caused by cathodic protection is added in the latest standards of DNVGL2018 under the premise of ensuring the mechanical properties of the chain. While the reliability of the chain mainly depends on the overall performance given by the steel.
  • the toughness of base and weld of the chain are reduced below the qualified line by coarse eutectic niobiumcarbide.
  • the air cooling process is impossible to be implemented in the continuous heat treatment production line to avoid the low-temperature phase transformation crack although this patent requires air cooling after heattritment.
  • retained austenite will decompose during the high-temperature tempering although austenite is beneficial to toughness and environmental performence.
  • the steel with high content of N has a greater driving force for precipitation, higher density of precipitation phase, and greater strengthening effect, than that with the low content of N.
  • the technical problem to be solved by the present invention is to propose a new manufacturing scheme of a grade R6 offshore mooring chain as well as its steel for use in anchoring and mooring floating bodies with cathodic protection.
  • the precipitation strengthening effect and the toughness and a low corrosion rate of the chain are improved on the premise of ensuring the hardenability and reduces the corrosion potential when the total contents of alloy and microalloy are narrowed, to curb the embrittlement by hydrogen generation due to the chains are received by cathodic overprotection passively.
  • the chemical composition by wt% are as follows: C 0.18 ⁇ 0.24, N 0.006 ⁇ 0.024, P 0.005 ⁇ 0.025,S ⁇ 0.005,Si 0.15 ⁇ 0.35, Mn 0.20 ⁇ 0.40, Cr 1.40 ⁇ 2.60, Ni 0.80 ⁇ 3.20, Mo 0.35 ⁇ 0.75, Cu ⁇ 0.50, Al ⁇ 0.02, Ti ⁇ 0.005, V 0.04 ⁇ 0.12, Nb 0.02 ⁇ 0.05, Ca 0.0005 ⁇ 0.004, O ⁇ 0.0015, H ⁇ 0.00015, the rest is Fe and unavoidable impurity elements.
  • the content of N in the chemical composition is 0.016-0.024.
  • the chain is made of round bars corresponding to the above chain steel.
  • the present invention further limits the content of C and N and the range of ⁇ M and ⁇ MM on the basis of the related product composition applied by two the Chinese invention patents whose publication numbers are CN103667953 B and CN106636928A .
  • the chain link is transformed into a composite bainite microstructure consisting of BU (upper bainite) with a small amount of BL (lower bainite) and M (martensite) during the cooling process after austenitizing.
  • BU upper bainite
  • BL lower bainite
  • M martensite
  • the phase transformation temperature of BU with Bs ⁇ 500°C is higher than that of the martensite with Ms of ⁇ 320°C.
  • the cooling crack sensitivity decreases with the increase of the phase transformation temperature.
  • the K IC data is obtained, and the EAC here is expressed as KIEACE, KIEAC 0 .
  • KQEAC of the weld zone of the chain is also tested for comparing the performance of the weld zone with that of the base.
  • the chain of the present invention is made of round bar having the corresponding chemical composition, and the round bar is processed in sequence by chain making, flash butt welding, and heat treatment to obtain the final product, wherein the heat treatment include high-temperature quenching with ⁇ 980°Cand tempering with 600°C to 690°C. Quenching and tempering are cooled with water less than 50°C.
  • Round bar is made from continuous casting bloom or ingot having corresponding chemical composition, and in sequence by heating, blooming, rolling and slow cooling, in which the heating temperature is more than 1230°C, so that nitride and carbonitride are all dissolved in austenite; in the cooling process, due to the combination of micro-alloying elements MM and the limit of C+N, the precipitation sequence of nitride and carbonitride is TiN-AlN-NbCN- MCN.
  • the nitride and carbonitride are controlled to be precipitated in the sequence of TiN-AlN-NbCN-MCN on the basis of the general technology, that is smelting-bloom continuous casting-blooming with high temperature heating-intermediate billet heating-forging or rolling-chain making-flash butt welding-heat treatment, and so on.
  • the solubility product of [Nb][C+N] is smaller, the effect of inhibiting the growth of austenite grain of NbCN is stronger than that of NbC, and the existence of NbCN (and solid solution of Nb) allows the temperature of the chain to increase from ⁇ 920°C to ⁇ 980°C before quenching.
  • Carrying out example (invention example) 1-4 and contrast example 3 are about the process wherein continuous casting bloom with the size of 390 ⁇ 510mm are rolled into the round bars with a diameter of 120mm, while contrast example 1, 2 and 4 are about the process that 420kg test ingots are forged into round bars with a diameter of 95mm, and then the round bars are processed in sequence by blanking, heating, bending, flash welding, forming chain and heat treatment (quenching + tempering) to obtain the finished chain.
  • the performance data is the average value of the results of three groups of specimens. Numerical treatment of the third place after the decimal point: ⁇ 4 discard and ⁇ 6 into 1.
  • Loading test Zwick 50kN testing machine, made by Zwick Co., Germany; prefabricated fatigue crack: MTS 810 (100kN) electro-hydraulic servo testing machine system, made by MTS, Co., America; corrosion test device: seawater corrosion test container, equipped with slow tension and compact tension fixture; potentiostat: CHI660D electrochemical workstation, Shanghai Chenhua Instrument Co., China; pH value of artificial seawater is 8.2 ⁇ 7.0; 25 °C. See Figure 5-8for specimens and tests.
  • EAC test is additionally required for the grade R6 chain.
  • the SSRT and KIEAC (CT) test is included to evaluate EAC resistance.
  • the SSRT test is carried out with no potential, potential of -850 mV, -1200 mV (SCE) and axial cylindrical smooth specimen in dry atmosphere and artificial seawater.
  • the CT test is carried out with potential of -950, -1050 mV (SCE) and in artificial seawater.
  • Z E /Z 0 and KQEAC 0 / KQEAC E indicate the degradation degree of EAC resistance.
  • Z 0 and Z E refer to the results of the reduction of area of SSRT without and with potential respectively.
  • the potential is not added or added to -950 mV and -1200 mV (SCE).
  • KQEAC 0 and KQEAC E refer to the results of CT test without and with potential respectively.
  • the CT specimen was precharged hydrogen for 48 hours.
  • Tensile speed ⁇ 6 ⁇ 10 -9 m/s.
  • KQEAC 0 /KQEAC E refers to the degradation degree of EAC resistance in the carrying out example and the contrast examples.
  • KIC data is obtained, and here KIEAC 0 and KIEAC E refer to the results of the CT test without and with potential respectively.
  • chain making and simulated quenching-tempering are carried out first, then EAC test is carried out by sampling.
  • KQEAC of the weld zone of the chain is also tested for the comparison of the performance of the weld zone and the base.
  • Carrying out example (invention example) 1-4 all conform to the range of the composition limitation of the present invention.
  • the limited TiN and AlN combined with a small content of N are first precipitated in the cooling process of continuous casting bloom, according to the solubility product from small to large, which ensures the subsequent precipitation of NbCN and VCN.
  • the heat temperature is more than 1230°C, the continuous casting bloom is forged and rolled, AlN, NbCN, VCN, M3C and M2C was first all dissolved in austenite, and then precipitated during cooling.
  • TiN, NbCN, and AlN do not dissolve when the chain is quenched at 980°C, which hinders the growth of austenite grain.
  • NbCN which is still insoluble at 1150°C, is used as the main precipitate to hinder the growth of austenite grain.
  • M3C, M2C, and VCN are fully solid solution with a high-temperature quenching at 980°C, and then precipitated again during a high-temperature tempering.
  • the quenching-tempering steel is strengthened by fine and dense VCN, so as to make up for the loss of strengthening effect caused by reducing the total content of alloy in the present invention.
  • KIEAC E /KIEAC 0 0.85
  • KIEAC E and KIEAC 0 meet the plane strain condition and KIC criterion. This is the first KIEAC data of grade R6 steel obtained in the world.
  • the potential measured after immersion in seawater for 80 hours is used as the corrosion potential under laboratory conditions.
  • the difference between corrosion potential and applied potential is overprotection potential.
  • the overprotection potential to - 850mV(SCE) in In the carrying out example 1 and 3 is about 200 and 232mV (SCE) respectively, which are within the allowable range.
  • the overprotection potential to -1200mV (SCE) is about 550 and 580mv (SCE) respectively, which is hard to bear.
  • the carrying out example 1, 2 is compared with the contrast example 4, the strength is increased by 62-75 MPa by adopting similar quenching-tempering treatment, which shows that the strengthening effect of VCN is better than that of VC.
  • Ms is low, and it is sensitive to cooling crack; N has a low content, N is exhausted by first precipitated NbCN, and is not enough to form AlN.
  • the impact value is 61J, which barely conform with the standard, but the tensile strength is as low as 1080 MPa, which is unqualified.
  • the total content of alloy exceeds the scope of the invention.
  • the difference between -850 mV and its corrosion potential of -520 mV, that is, the overprotection potential is about 330 mV (SCE).
  • SCE corrosion potential
  • SSRT test show a tendency of embrittlement.
  • the content of Nb is as high as 0.07, and NbCN is precipitated before AlN.
  • Ms is low, it is sensitive to cooling crack; with the increase of Al and Ti, the total content of micro-alloy elements exceeds the scope of the invention. Due to the consumption of N, N was exhausted when NbCN was precipitated. There are only VC, no VCN. The yield ratio is 0.96 and greater than regulation 0.95. The strengthening and toughening effects are not obvious when the quenching temperature is at 980°C. Impact toughness is unqualified.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Prevention Of Electric Corrosion (AREA)
EP19925101.8A 2019-04-16 2019-05-16 R6 high toughness offshore mooring chain steel applicable to anchor moored positioning cathodic protection floating body and mooring chain thereof Active EP3812479B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201910306407.XA CN110144516B (zh) 2019-04-16 2019-04-16 一种适用于锚泊定位阴极保护浮体的r6级高强韧性海洋系泊链钢及其系泊链
PCT/CN2019/087168 WO2020211137A1 (zh) 2019-04-16 2019-05-16 一种适用于锚泊定位阴极保护浮体的r6级高强韧性海洋系泊链钢及其系泊链

Publications (3)

Publication Number Publication Date
EP3812479A1 EP3812479A1 (en) 2021-04-28
EP3812479A4 EP3812479A4 (en) 2021-07-07
EP3812479B1 true EP3812479B1 (en) 2021-11-17

Family

ID=67589817

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19925101.8A Active EP3812479B1 (en) 2019-04-16 2019-05-16 R6 high toughness offshore mooring chain steel applicable to anchor moored positioning cathodic protection floating body and mooring chain thereof

Country Status (6)

Country Link
US (1) US20210285069A1 (pt)
EP (1) EP3812479B1 (pt)
CN (1) CN110144516B (pt)
BR (1) BR112021008711B1 (pt)
RU (1) RU2763365C1 (pt)
WO (1) WO2020211137A1 (pt)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111172473A (zh) * 2020-02-24 2020-05-19 江苏利淮钢铁有限公司 一种d型锚链末端卸扣用钢
AR124169A1 (es) * 2020-11-30 2023-02-22 Dalmine Spa Composición de acero, artículo forjado y método de fabricación de un recipiente de presión sin costura para gas comprimido
CN114369759A (zh) * 2021-12-20 2022-04-19 江苏亚星锚链股份有限公司 一种耐低温锚链
CN116179939A (zh) * 2022-10-31 2023-05-30 上海茵矩材料科技有限公司 一种高环境裂纹抗力的系泊链钢及系泊链

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS54115618A (en) * 1978-02-28 1979-09-08 Kawasaki Steel Co Steel for high tensile large diameter chain
RU2085610C1 (ru) * 1994-04-05 1997-07-27 Центральный научно-исследовательский институт конструкционных материалов "Прометей" Феррито-перлитная литейная сталь
US6852175B2 (en) * 2001-11-27 2005-02-08 Exxonmobil Upstream Research Company High strength marine structures
CN101161843A (zh) 2007-11-21 2008-04-16 广州珠江钢铁有限责任公司 一种提高v-n微合金化高强度钢钒合金利用率的方法
CN101519751B (zh) * 2008-02-27 2011-06-15 宝山钢铁股份有限公司 一种高性能海洋系泊链钢及其制造方法
CN103667953B (zh) * 2013-11-28 2016-09-28 江苏亚星锚链股份有限公司 一种低环境裂纹敏感性超高强韧性海洋系泊链钢及其制造方法
KR101657421B1 (ko) * 2015-09-22 2016-09-13 현대제철 주식회사 체인강 및 이의 제조방법
KR101654684B1 (ko) * 2015-12-11 2016-09-06 주식회사 세아베스틸 저온 충격인성이 우수한 고강도 무어링 체인강 및 그 제조방법
CN105624566A (zh) * 2016-01-05 2016-06-01 江阴兴澄特种钢铁有限公司 高强度、低热处理敏感性的r5级系泊链钢及其制造方法
CN106636928A (zh) * 2016-11-12 2017-05-10 殷匠 一类海洋系泊链钢及其系泊链的热处理方法

Also Published As

Publication number Publication date
EP3812479A4 (en) 2021-07-07
CN110144516A (zh) 2019-08-20
WO2020211137A1 (zh) 2020-10-22
BR112021008711B1 (pt) 2022-11-29
RU2763365C1 (ru) 2021-12-28
US20210285069A1 (en) 2021-09-16
CN110144516B (zh) 2020-12-01
EP3812479A1 (en) 2021-04-28
BR112021008711A2 (pt) 2021-11-16

Similar Documents

Publication Publication Date Title
EP3812479B1 (en) R6 high toughness offshore mooring chain steel applicable to anchor moored positioning cathodic protection floating body and mooring chain thereof
CN107177797B (zh) 油气田用130ksi、135ksi级别耐蚀钻具钢及其制造方法
EP3795710A1 (en) Hot-rolled thick h-beam with yield strength grade of 500 mpa and preparation method therefor
EP2728030B1 (en) Thick-walled high-strength seamless steel pipe with excellent sour resistance for pipe for pipeline, and process for producing same
JP6012189B2 (ja) 低温における優れた靭性および硫化物応力腐食亀裂抵抗をもつ高強度の鋼管
US11186885B2 (en) High-strength seamless steel pipe for oil country tubular goods, and production method for high-strength seamless steel pipe for oil country tubular goods
US10000833B2 (en) Thick, tough, high tensile strength steel plate and production method therefor
US11352679B2 (en) Medium-manganese steel product for low-temperature use and method for the production thereof
EP3631021B1 (en) Method for producing a steel part and corresponding steel part
EP3425079B1 (en) Steel material and oil-well steel pipe
US20200347480A1 (en) Steel reinforcing bar and production method therefor
JP7364962B2 (ja) 鋼材
CN1108397C (zh) 高强度、高韧性、耐腐蚀系泊链用钢及其生产工艺
CN112251672B (zh) 焊接性能优良的低屈强比eh690钢板及其制造方法
US10550962B2 (en) Steel material and oil-well steel pipe
EP3719149A1 (en) High-hardness steel product and method of manufacturing the same
EP3269837B1 (en) Micro alloyed steel and method for producing the same
CN115717214B (zh) 一种沿海大气环境炼化管道用钢及其制备方法
CN111607747A (zh) 一种海底用抗硫化氢腐蚀x70级管线钢及其生产方法
EP3385398A1 (en) High-strength bolt
CN115287531B (zh) 770MPa直缝焊接钢管用钢及其制造方法
JP2001107139A (ja) 耐遅れ破壊特性および海浜耐候性に優れるボルト部品の製造方法
CN116657035A (zh) 一种铁路货车用高强、耐低温yq500nqr1钢生产制备方法
CN117904541A (zh) 一种屈服强度≥345Mpa的时效强化低温容器钢及生产方法
CN113430457A (zh) 一种1300MPa级高延伸率低延迟开裂敏感性热成形钢及其生产方法

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

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

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

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: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20201208

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

A4 Supplementary search report drawn up and despatched

Effective date: 20210604

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/02 20060101AFI20210528BHEP

Ipc: C22C 38/04 20060101ALI20210528BHEP

Ipc: C22C 38/06 20060101ALI20210528BHEP

Ipc: C22C 38/42 20060101ALI20210528BHEP

Ipc: C22C 38/44 20060101ALI20210528BHEP

Ipc: C22C 38/46 20060101ALI20210528BHEP

Ipc: C22C 38/48 20060101ALI20210528BHEP

Ipc: C22C 38/50 20060101ALI20210528BHEP

Ipc: C21D 8/06 20060101ALI20210528BHEP

Ipc: C21D 1/18 20060101ALI20210528BHEP

Ipc: C22C 38/12 20060101ALI20210528BHEP

Ipc: C22C 38/16 20060101ALI20210528BHEP

Ipc: C22C 38/18 20060101ALI20210528BHEP

Ipc: C22C 38/22 20060101ALI20210528BHEP

Ipc: C22C 38/24 20060101ALI20210528BHEP

Ipc: C22C 38/26 20060101ALI20210528BHEP

Ipc: C22C 38/40 20060101ALI20210528BHEP

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

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/40 20060101ALI20210809BHEP

Ipc: C22C 38/26 20060101ALI20210809BHEP

Ipc: C22C 38/24 20060101ALI20210809BHEP

Ipc: C22C 38/22 20060101ALI20210809BHEP

Ipc: C22C 38/18 20060101ALI20210809BHEP

Ipc: C22C 38/16 20060101ALI20210809BHEP

Ipc: C22C 38/12 20060101ALI20210809BHEP

Ipc: C21D 1/18 20060101ALI20210809BHEP

Ipc: C21D 8/06 20060101ALI20210809BHEP

Ipc: C22C 38/50 20060101ALI20210809BHEP

Ipc: C22C 38/48 20060101ALI20210809BHEP

Ipc: C22C 38/46 20060101ALI20210809BHEP

Ipc: C22C 38/44 20060101ALI20210809BHEP

Ipc: C22C 38/42 20060101ALI20210809BHEP

Ipc: C22C 38/06 20060101ALI20210809BHEP

Ipc: C22C 38/04 20060101ALI20210809BHEP

Ipc: C22C 38/02 20060101AFI20210809BHEP

INTG Intention to grant announced

Effective date: 20210830

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

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

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

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: 602019009419

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1448111

Country of ref document: AT

Kind code of ref document: T

Effective date: 20211215

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

REG Reference to a national code

Ref country code: NO

Ref legal event code: T2

Effective date: 20211117

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20211117

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1448111

Country of ref document: AT

Kind code of ref document: T

Effective date: 20211117

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

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: 20211117

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: 20211117

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: 20211117

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: 20220217

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: 20211117

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: 20220317

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: 20211117

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: 20220317

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: 20211117

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: 20211117

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: 20211117

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: 20211117

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: 20220218

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: 20211117

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: 20211117

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: 20211117

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: 20211117

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: 20211117

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: 20211117

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: 20211117

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602019009419

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

26N No opposition filed

Effective date: 20220818

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: 20211117

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602019009419

Country of ref document: DE

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20220531

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: 20211117

Ref country code: LU

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

Effective date: 20220516

Ref country code: LI

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

Effective date: 20220531

Ref country code: CH

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

Effective date: 20220531

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: 20220516

Ref country code: FR

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

Effective date: 20220531

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

Effective date: 20211117

Ref country code: DE

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

Effective date: 20221201

Ref country code: BE

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

Effective date: 20220531

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

Ref country code: NO

Payment date: 20230414

Year of fee payment: 5

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: 20211117

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: 20211117

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

Ref country code: GB

Payment date: 20240313

Year of fee payment: 6