EP2520680A2 - Feuillard d'acier à résistance mécanique élevée ayant une excellente résistance au traitement thermique post-soudage et son procédé de fabrication - Google Patents
Feuillard d'acier à résistance mécanique élevée ayant une excellente résistance au traitement thermique post-soudage et son procédé de fabrication Download PDFInfo
- Publication number
- EP2520680A2 EP2520680A2 EP10841182A EP10841182A EP2520680A2 EP 2520680 A2 EP2520680 A2 EP 2520680A2 EP 10841182 A EP10841182 A EP 10841182A EP 10841182 A EP10841182 A EP 10841182A EP 2520680 A2 EP2520680 A2 EP 2520680A2
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel sheet
- less
- pwht
- high strength
- steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- 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
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- 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
- C21D2211/004—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
- C21D2211/005—Ferrite
-
- 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
- C21D2211/009—Pearlite
-
- 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 invention relates to a steel sheet used for crude oil refining equipment, storage tanks, heat exchangers, reaction furnaces, condensers and the like in wet hydrogen sulfide environments, and more particularly, to a steel sheet having excellent strength and toughness even after performing a Post Weld Heat Treatment (PWHT) and a method for manufacturing the same.
- PWHT Post Weld Heat Treatment
- Post Weld Heat Treatment is carried out to eliminate stress generated during welding with the objects of stabilizing shape and size and preventing the deformation of a structure after welding if the steel is welded in addition to the above-mentioned thickening of steel.
- PWHT Post Weld Heat Treatment
- a steel sheet passing through the PWHT process for a lengthy period of time has a problem in that tensile strength of the steel sheet may be deteriorated due to coarsening in the structure of the steel sheet.
- a lengthy PWHT process causes a phenomenon in which strength and toughness of the steel sheet are lowered at the same time depending on softening of matrix structures and grain boundaries, growth of crystal grains, coarsening of carbides, and others.
- a means for preventing the deterioration of physical properties according to the above-mentioned long-time PWHT process disclosed in Japanese Patent Publication No. 1997-256037 enabled assurance time for PWHT up to 16 hours by the processes of performing heating and hot rolling on a slab comprising, by weight percent, 0.05 to 0.20% of C, 0.02 to 0.5% of Si, 0.2 to 2.0% of Mn, 0.005 to 0.10% of Al, and containing, if necessary, one or more selected from Cu, Ni, Cr, Mo, V, Nb, Ti, B and Ca, and rare-earth elements with the remainder being iron and unavoidable impurities, air cooling the hot rolled steel sheet at room temperature, and heating and slow cooling the air-cooled steel sheet at the transformation point of Ac1 to Ac3.
- An object of the present invention is to provide a high strength steel sheet having excellent Post Weld Heat Treatment (PWHT) resistance of which strength and toughness are not deteriorated even after performing PWHT for a lengthy period of time, and a method for manufacturing the same.
- PWHT Post Weld Heat Treatment
- the present invention provides a high strength steel sheet excellent in PWHT (Post Weld Heat Treatment) resistance having a composition comprising by weight percent: 0.1 to 0.3% of C; 0.15 to 0.50% of Si; 0.6 to 1.2% of Mn; 0.035% or less of P; 0.020% or less of S; 0.001 to 0.05% of Al; 0.01 to 0.35% of Cr; 0.005 to 0.2% of Mo; 0.005 to 0.05% of V; 0.001 to 0.05% of Nb; 0.001 to 0.05% of Ti; 0.0005 to 0.005% of Ca; 0.05 to 0.5% of Ni; one or more selected from the group consisting of 0.005 to 0.5% of Cu, 0.005 to 0.2% of Co and 0.005 to 0.2% of W; and Fe as well as unavoidable impurities, wherein the composition satisfies the following relational expression:
- the present invention provides a method for manufacturing the high strength steel sheet excellent in PWHT resistance, the method comprising:
- a steel sheet for pressure vessels which has strength of 500 MPa or more, of which strength and toughness are not deteriorated even after PWHT reaching 100 hours, and which is excellent in hydrogen-induced cracking resistance can be provided.
- weight percent (wt%) a composition range of the present invention
- the content of carbon (C) is preferably limited to a range of 0.1 to 0.3 wt%.
- C as an element for improving strength of a steel sheet, has problems that the strength of the steel sheet in a matrix phase is lowered with a C content of less than 0.1 wt%, and segregation is generated in the structure to deteriorate hydrogen-induced cracking resistance with a C content of more than 0.3 wt%.
- the content of silicon (Si) is preferably limited to a range of 0.15 to 0.50 wt%.
- Si is an element that is effective in deoxidation and solid solution strengthening, and Si is an element that is added to obtain an effect of increasing the impact transition temperature.
- Si should be added in an amount of 0.15 wt% or more to accomplish such effects, there are problems that weldability is deteriorated, and an oxidation film is severely formed on the surface of the steel sheet if Si is added in an amount of more than 0.5 wt%.
- the content of manganese (Mn) is preferably limited to being within the range of 0.6 to 1.2 wt%.
- Mn is preferably controlled to the content of 1.2 wt% or less since Mn along with S forms MnS, an elongated nonmetallic inclusion, thereby deteriorating elongation at room temperature and low temperature toughness.
- the content of Mn is limited to being within the range of 0.6 to 1.2 wt% since it is difficult to secure proper strength due to the nature of the present invention if Mn is added to the content of less than 0.6 wt%.
- the content of aluminum (Al) is preferably limited to being within the range of 0.001 to 0.5 wt%.
- Al together with the above-mentioned Si is one of strong deoxidizers in the steelmaking process, and has problems that the deoxidation effect is insignificant with an Al content of less than 0.001 wt%, and the deoxidation effect is saturated and manufacturing costs increases if Al is added in an amount of more than 0.05 wt%.
- phosphorous (P) is an element that deteriorates low temperature toughness
- phosphorous (P) is preferably controlled to be within the range of 0.035 wt% or less since it costs excessively to eliminate phosphorous (P) in the steelmaking process.
- Sulfur (S) along with phosphorous (P) is also an element that adversely affects low temperature toughness, it is preferable to control sulfur (S) within the range of 0.020 wt% or less since it may cost excessively to eliminate sulfur (S) in the steelmaking process as in the case of phosphorous (P).
- the content of chromium (Cr) is preferably limited to being within the range of 0.01 to 0.35 wt%.
- Cr should be added in an amount of 0.01 wt% or more to obtain the strength increasing effect in the present invention since chromium (Cr) is an element that increases strength, it is preferable to control chromium (Cr) to the amount of 0.35 wt% or less since chromium (Cr) is a relatively expensive element, and chromium (Cr) causes manufacturing costss to be increased if chromium (Cr) is added in an amount of more than 0.35 wt%.
- Mo molybdenum
- Mo is an element that prevents cracking of the steel sheet due to sulfides as well as an element that is effective in increasing strength of the steel sheet as in the case of Cr.
- Mo should be added to the amount of 0.005 wt% or more to obtain the effects, it is preferable to limit the amount of Mo to 0.2 wt% or less since Mo is also a relatively expensive element and causes manufacturing costs to increase.
- V vanadium
- the content of vanadium (V) is preferably limited to being within the range of 0.005 to 0.05 wt%.
- V is an element that is effective in increasing the strength of the steel sheet as in the cases of Cr and Mo. Therefore, although V should be added in an amount of 0.005 wt% or more to promote the effect of increasing strength of the steel sheet, it is preferable to add V in an amount of 0.05 wt% or less since V is a relatively expensive element.
- the content of niobium (Nb) is preferably limited to being within the range of 0.001 to 0.05 wt%.
- Nb is an important element that exists in the state of solid solution within austenite to increase hardenability of austenite, and that is precipitated into carbonitrides (Nb(C,N)) matching the matrix to increase strength of the steel sheet.
- Nb should be added in an amount of 0.001 wt% or more to obtain the effects, it is preferable to limit the content of Nb to 0.05 wt% or less since Nb exists in the form of coarse precipitates in the continuous casting process and functions as a site of hydrogen induced cracking if Nb is added in a large amount.
- the content of titanium (Ti) is preferably limited to being within the range of 0.001 to 0.05 wt%.
- Ti like Nb is an important element that is precipitated into carbonitrides (Ti(C,N)) and increases strength of the steel sheet.
- Ti should be added in an amount of 0.001 wt% or more to obtain the effects, it is preferable to limit the content of Ti to 0.05 wt% or less since Ti exists in the form of coarse precipitates in the continuous casting process and functions as a site of hydrogen induced cracking if Ti is added in a large amount.
- the content of calcium (Ca) is preferably limited to being within the range of 0.0005 to 0.005 wt.%.
- Ca should be added in an amount of 0.0005 wt% or more such that Ca is produced into CaS to inhibit the formation of nonmetallic inclusions such as MnS.
- an upper limit value of the content is preferably limited to 0.005 wt% since Ca is reacted with O contained in steel to produce CaO that is a nonmetallic inclusion if the content of Ca exceeds 0.005 wt%.
- Ni nickel
- the content of nickel (Ni) is preferably limited to being within the range of 0.05 to 0.5 wt%. It is preferable to add Ni in an amount of 0.5 wt% or less since Ni is a relatively expensive element and causes manufacturing costs to increase although Ni should be added in an amount of 0.05 wt% or more to obtain the effect as an element that is most effective in improving low temperature toughness of the steel sheet.
- composition of the present invention comprises one or more selected from the group consisting of Cu, Co, and W.
- Copper (Cu) is preferably added in an amount of 0.005 to 0.5 wt%.
- Cu prevents strength of the steel sheet from deteriorating even after performing PWHT according to matrix strengthening by solution strengthening or e-Cu precipitation, and prevents strength and toughness of the steel sheet from deteriorating through matrix strengthening and recovery inhibition. It is preferable to add Cu within the range of 0.005 to 0.5 wt% since it is relatively expensive.
- Co Co is preferably added in an amount of 0.005 to 0.2 wt%. Co is preferably added in a range of 0.005 to 0.2 wt% since it is relatively expensive, although Co is an element that is effective in preventing softening of the matrix structure.
- Tungsten (W) is preferably added in an amount of 0.005 to 0.2 wt%.
- W is preferably added in an amount of 0.005 wt% or more since it has characteristics that can prevent strength and toughness of the steel sheet from deteriorating by forming WC or reducing a precipitation fraction of cementite, thereby preventing growth of cementite or coagulation inhibition of cementite. It is just more preferable to add W within a range of 0.005 to 0.2 wt% since W is relatively expensive.
- the Ca/S ratio is an essential composition ratio improving hydrogen induced cracking resistance of the steel sheet by spheroidizing MnS inclusions.
- the ratio is controlled to 1.0 or less since its effects are difficult to expect if the Ca/S ratio exceeds 1.0.
- the composition comprises Fe as well as unavoidable impurities as a remainder.
- the microstructure of the steel may be formed in a ferrite structure or a mixed structure of ferrite and pearlite.
- the structure may comprise up to 10 wt% of bainite although it is preferable that low temperature structure is not included in the above-mentioned structure if possible.
- the reason for controlling the structure in the above-stated form is that a steel sheet of the present invention should be excellent in a target hydrogen induced cracking resistance and should have proper strength and toughness.
- a banding index value (measured by ASTM E-1268) exhibiting how much the banding structure that is weak in hydrogen induced cracking has been formed is preferably 0.25 or less in order to secure hydrogen induced cracking resistance. Hydrogen induced cracking resistance is rapidly lowered in the microstructure if the banding index value exceeds 0.25.
- the center of a steel sheet in a thickness direction preferably has an average ferrite grain size of 50 ⁇ m or less since it is apprehended that strength and toughness of the steel sheet are deteriorated if the ferrite grains have excessive sizes.
- the crystal grain sizes do not have a lower limit, the crystal grain sizes may have 5 ⁇ m or more since it is generally difficult to obtain crystal grains of less than 5 ⁇ m from a target steel of the present invention.
- the manufacturing method according to the present invention comprises reheating a steel slab satisfying the above-mentioned composition range to a temperature range of 1050 to 1250°C since a solid solution of solute atoms is difficult if the reheating temperature is lower than 1050°C, and sizes of austenite crystal grains become too coarse to deteriorate properties of the steel sheet if the reheating temperature is more than 1250°C.
- the recrystallization controlled rolling is carried out by hot rolling the reheated steel slab at a no-recrystallization temperature or more.
- T nr the foregoing no-recrystallization temperature can be calculated by the following expression.
- T nr (°C) 887+464xC+890xTi+363xAl-357xSi+(6446xNb-644xNb 1/2 )+(732xV-230xV 1/2 )
- recrystallization controlled rolling is the most important variable, and the recrystallization controlled rolling is preferably performed by applying 10% or more of rolling reduction per each rolling pass in a temperature range of T nr to T nr + 100°C, thereby imparting a cumulative rolling reduction of 30% or more since a banding index value of 0.25 or less cannot be expected if the cumulative rolling reduction is less than 30%. Further, temperature of recrystallization controlled rolling is also limited to a control banding index, thereby inhibiting the band structure in the state that crystal grains have not become coarse.
- the temperature is lower than a no-recrystallization temperature range (T nr ) since austenite is flattened into a pancake such that the banding index value is increased.
- T nr a no-recrystallization temperature range
- temperature is excessively high since crystal grains have excessive sizes.
- a cooled hot-rolled steel sheet is heat-treated.
- the heat treatment is held under conditions of a temperature range of 850°C to 950°C and a time period of 1.3xt + (10 to 30) in minutes, wherein t is thickness (mm) of steel. It is difficult to secure strength of the steel sheet since it is difficult to resolve solute atoms for solid solution if the heat treatment is conducted at a temperature of less than 850°C, whereas low temperature of the steel sheet is deteriorated since crystal grains are grown if the heat treatment is conducted at a temperature of more than 950°C.
- the heat treatment holding time is limited since homogenization of the structure is difficult if the holding time is less than 1.3xt + 10 minutes (t is thickness (mm) of steel), and productivity is deteriorated if the holding time is more than 1.3*t + 30 in minutes (t is thickness (mm) of steel).
- the held steel sheet is cooled to a cooling rate of 0.1 to 10 °C/sec based on the central part of the steel sheet since there are high possibilities that coarsening of ferrite grains may be generated during cooling at a cooling rate of 0.1 °C/sec or less, and an excessive second phase (10 % or more of bainite fraction) may be generated at a cooling rate of 10 °C/sec or more.
- the foregoing cooling rate is controlled to adjust an average ferrite grain size in the central part of the steel sheet to 50 ⁇ m or less.
- PWHT is required in a steel sheet of the present invention manufactured through the heat treatment process in order to eliminate residual stress by the welding process added during fabrication of pressure vessels.
- strength and toughness of the steel sheet are generally deteriorated after performing PWHT on a steel sheet for a lengthy period of time
- the steel sheet manufactured by the present invention has a merit that welding work is possible without a large drop in strength or toughness of the steel sheet even when the steel sheet is subjected to PWHT at an ordinary PWHT temperature of 600°C to 640°C for a lengthy period of time of up to 100 hours.
- the steel sheet of the present invention has a tensile strength of 450 MPa or more even after performing PWHT for 100 hours, and satisfies a Charpy impact energy value of 50 J or more at - 50°C.
- the following table 1 exhibits chemical components of inventive steels and comparative steels respectively.
- Steel slabs having the same compositions as shown in the table 1 were manufactured by conducting rolling, heat treatment and cooling under conditions of steel sheet thicknesses and reheating temperatures of the table 2.
- yield strengths, tensile strengths and crack length ratios (CLR) of the steel sheets were examined, and the examination results were shown in the following table 2.
- inventive steels satisfying compositions and manufacturing conditions have strength and toughness values that are not lowered although the PWHT time reaches 50 to 100 hours.
- strength and toughness values of the comparative steels are substantially deteriorated than those of the inventive steels as the PWHT time is extended to 50 hours or more although the comparative steels show strength and toughness levels that are almost equal to those of the inventive steels if the PWHT time is small when comparing the comparative steels with the invention steels.
- the inventive steels are far excellent in the CLR (Crack Length Ratio) (%) exhibiting hydrogen induced cracking resistance under the H2S gas (Sour Gas) atmosphere.
- the inventive steels are excellent in the CLR (Crack Length Ratio) because the Banding Index showing the homogenization extent of microstructures formed in a composite structure of ferrite and pearlite is controlled to a lower value of 0.25 or less.
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)
- Heat Treatment Of Steel (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020090132129A KR101322067B1 (ko) | 2009-12-28 | 2009-12-28 | 용접 후 열처리 저항성이 우수한 고강도 강판 및 그 제조방법 |
PCT/KR2010/009225 WO2011081350A2 (fr) | 2009-12-28 | 2010-12-22 | Feuillard d'acier à résistance mécanique élevée ayant une excellente résistance au traitement thermique post-soudage et son procédé de fabrication |
Publications (3)
Publication Number | Publication Date |
---|---|
EP2520680A2 true EP2520680A2 (fr) | 2012-11-07 |
EP2520680A4 EP2520680A4 (fr) | 2014-11-19 |
EP2520680B1 EP2520680B1 (fr) | 2016-10-26 |
Family
ID=44226971
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP10841182.8A Revoked EP2520680B1 (fr) | 2009-12-28 | 2010-12-22 | Feuillard d'acier à résistance mécanique élevée ayant une excellente résistance au traitement thermique post-soudage et son procédé de fabrication |
Country Status (5)
Country | Link |
---|---|
EP (1) | EP2520680B1 (fr) |
JP (1) | JP5657026B2 (fr) |
KR (1) | KR101322067B1 (fr) |
CN (1) | CN102782169B (fr) |
WO (1) | WO2011081350A2 (fr) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2014201760A (ja) * | 2013-04-01 | 2014-10-27 | Jfeスチール株式会社 | 耐食性に優れる原油タンク用鋼材および原油タンク |
EP3395984A4 (fr) * | 2015-12-22 | 2018-12-26 | Posco | Tôle d'acier présentant une excellente résistance au traitement thermique après soudage pour récipient sous pression à basse température et son procédé de fabrication |
EP3561111A4 (fr) * | 2016-12-22 | 2019-10-30 | Posco | Tôle d'acier épaisse ayant une excellente résistance à l'impact cryogénique et son procédé de fabrication |
EP3733904A4 (fr) * | 2017-12-26 | 2021-03-03 | Posco | Matériau en acier présentant une excellente résistance à la fissuration induite par l'hydrogène et son procédé de préparation |
US11578376B2 (en) | 2016-12-23 | 2023-02-14 | Posco Co., Ltd | Steel for pressure vessels having excellent resistance to hydrogen induced cracking and manufacturing method thereof |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR101417231B1 (ko) * | 2011-12-28 | 2014-07-08 | 주식회사 포스코 | 저온인성 및 인장특성이 우수한 압력용기용 극후강판 및 그 제조 방법 |
CN104195465A (zh) * | 2014-07-24 | 2014-12-10 | 安徽广源科技发展有限公司 | 一种耐低温耐腐蚀用合金钢及其制造方法 |
CN104109801B (zh) * | 2014-07-30 | 2016-04-27 | 宝山钢铁股份有限公司 | 高韧性、抗pwht软化脆化的钢板及其制造方法 |
CN105671436B (zh) * | 2016-02-05 | 2017-10-03 | 山东钢铁股份有限公司 | 抗高温pwht软化的低焊接裂纹敏感系数原油储罐用高强韧性钢板及其制造方法 |
KR102280641B1 (ko) * | 2019-10-22 | 2021-07-22 | 주식회사 포스코 | 고온 용접후열처리 저항성이 우수한 압력용기용 강판 및 그 제조방법 |
CN112813353B (zh) * | 2021-01-29 | 2022-05-27 | 日钢营口中板有限公司 | 一种超高温spwht高韧性正火容器用钢及制造方法 |
US11656169B2 (en) | 2021-03-19 | 2023-05-23 | Saudi Arabian Oil Company | Development of control samples to enhance the accuracy of HIC testing |
US11788951B2 (en) | 2021-03-19 | 2023-10-17 | Saudi Arabian Oil Company | Testing method to evaluate cold forming effects on carbon steel susceptibility to hydrogen induced cracking (HIC) |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH11131177A (ja) * | 1997-08-29 | 1999-05-18 | Nippon Steel Corp | 溶接後熱処理の省略可能な中常温圧力容器用鋼板およびその製造方法 |
JP2006045672A (ja) * | 2004-07-07 | 2006-02-16 | Jfe Steel Kk | 高張力鋼板の製造方法および高張力鋼板 |
US20090025839A1 (en) * | 2005-03-04 | 2009-01-29 | Nippon Steel Corporation | High tensile strength, refractory steel having excellent weldability and gas cuttability and method for producing same |
JP2009041073A (ja) * | 2007-08-09 | 2009-02-26 | Sumitomo Metal Ind Ltd | 溶接部からの延性き裂発生に対する抵抗性に優れる高張力鋼溶接継手およびその製造方法 |
WO2009119368A1 (fr) * | 2008-03-28 | 2009-10-01 | 株式会社神戸製鋼所 | Tôle d'acier à haute résistance qui présente une excellente résistance au recuit de détente et une excellente ténacité de joint à basse température |
Family Cites Families (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6179745A (ja) * | 1984-09-28 | 1986-04-23 | Nippon Steel Corp | 溶接継手熱影響部靭性のすぐれた鋼材の製造法 |
JP3795949B2 (ja) * | 1995-02-16 | 2006-07-12 | 新日本製鐵株式会社 | 疲労強度が優れた溶接継手 |
WO1997030184A1 (fr) * | 1996-02-13 | 1997-08-21 | Nippon Steel Corporation | Joint de soudure a haute resistance a la fatigue |
JPH09256037A (ja) | 1996-03-22 | 1997-09-30 | Nippon Steel Corp | 応力除去焼鈍処理用の厚肉高張力鋼板の製造方法 |
CZ293084B6 (cs) | 1999-05-17 | 2004-02-18 | Jinpo Plus A. S. | Ocele pro žárupevné a vysokopevné tvářené součásti, obzvláště trubky, plechy a výkovky |
DE60213736T2 (de) * | 2001-11-14 | 2007-08-16 | Sumitomo Metal Industries, Ltd. | Stahl mit verbesserter Ermüdungsfestigkeit und Verfahren zur Herstellung |
JP2004027355A (ja) * | 2001-11-14 | 2004-01-29 | Sumitomo Metal Ind Ltd | 疲労き裂進展抵抗特性に優れた鋼材とその製造方法 |
JP4267367B2 (ja) | 2002-06-19 | 2009-05-27 | 新日本製鐵株式会社 | 原油油槽用鋼およびその製造方法、原油油槽およびその防食方法 |
JP2008100277A (ja) * | 2006-10-23 | 2008-05-01 | Jfe Steel Kk | 靭性に優れた溶接部を有する低降伏比厚肉電縫鋼管の製造方法 |
KR100833070B1 (ko) | 2006-12-13 | 2008-05-27 | 주식회사 포스코 | 내hic특성이 우수한 인장강도 500㎫급 압력용기용 강판및 그 제조 방법 |
KR100833071B1 (ko) | 2006-12-13 | 2008-05-27 | 주식회사 포스코 | 내hic특성이 우수한 인장강도 600㎫급 압력용기용 강판및 그 제조 방법 |
MX2008012239A (es) | 2007-03-30 | 2008-11-28 | Sumitomo Metal Ind | Accesorio tubular para tubos octg para expansion en pozos y metodo de fabricacion del mismo. |
JP5716640B2 (ja) | 2011-11-21 | 2015-05-13 | 新日鐵住金株式会社 | 熱間鍛造用圧延棒鋼 |
-
2009
- 2009-12-28 KR KR1020090132129A patent/KR101322067B1/ko active IP Right Grant
-
2010
- 2010-12-22 JP JP2012546997A patent/JP5657026B2/ja active Active
- 2010-12-22 EP EP10841182.8A patent/EP2520680B1/fr not_active Revoked
- 2010-12-22 CN CN201080064894.0A patent/CN102782169B/zh active Active
- 2010-12-22 WO PCT/KR2010/009225 patent/WO2011081350A2/fr active Application Filing
Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH11131177A (ja) * | 1997-08-29 | 1999-05-18 | Nippon Steel Corp | 溶接後熱処理の省略可能な中常温圧力容器用鋼板およびその製造方法 |
JP2006045672A (ja) * | 2004-07-07 | 2006-02-16 | Jfe Steel Kk | 高張力鋼板の製造方法および高張力鋼板 |
US20090025839A1 (en) * | 2005-03-04 | 2009-01-29 | Nippon Steel Corporation | High tensile strength, refractory steel having excellent weldability and gas cuttability and method for producing same |
JP2009041073A (ja) * | 2007-08-09 | 2009-02-26 | Sumitomo Metal Ind Ltd | 溶接部からの延性き裂発生に対する抵抗性に優れる高張力鋼溶接継手およびその製造方法 |
WO2009119368A1 (fr) * | 2008-03-28 | 2009-10-01 | 株式会社神戸製鋼所 | Tôle d'acier à haute résistance qui présente une excellente résistance au recuit de détente et une excellente ténacité de joint à basse température |
EP2258884A1 (fr) * | 2008-03-28 | 2010-12-08 | Kabushiki Kaisha Kobe Seiko Sho | Tôle d'acier à haute résistance qui présente une excellente résistance au recuit de détente et une excellente ténacité de joint à basse température |
Non-Patent Citations (1)
Title |
---|
See also references of WO2011081350A2 * |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2014201760A (ja) * | 2013-04-01 | 2014-10-27 | Jfeスチール株式会社 | 耐食性に優れる原油タンク用鋼材および原油タンク |
EP3395984A4 (fr) * | 2015-12-22 | 2018-12-26 | Posco | Tôle d'acier présentant une excellente résistance au traitement thermique après soudage pour récipient sous pression à basse température et son procédé de fabrication |
EP3561111A4 (fr) * | 2016-12-22 | 2019-10-30 | Posco | Tôle d'acier épaisse ayant une excellente résistance à l'impact cryogénique et son procédé de fabrication |
US11649515B2 (en) | 2016-12-22 | 2023-05-16 | Posco Co., Ltd | Thick steel plate having excellent cryogenic impact toughness and manufacturing method therefor |
US11578376B2 (en) | 2016-12-23 | 2023-02-14 | Posco Co., Ltd | Steel for pressure vessels having excellent resistance to hydrogen induced cracking and manufacturing method thereof |
EP3733904A4 (fr) * | 2017-12-26 | 2021-03-03 | Posco | Matériau en acier présentant une excellente résistance à la fissuration induite par l'hydrogène et son procédé de préparation |
US11634785B2 (en) | 2017-12-26 | 2023-04-25 | Posco Co., Ltd | Steel material showing excellent hydrogen-induced cracking resistance and method for preparing same |
Also Published As
Publication number | Publication date |
---|---|
CN102782169B (zh) | 2014-11-19 |
WO2011081350A3 (fr) | 2011-11-17 |
EP2520680B1 (fr) | 2016-10-26 |
JP2013515861A (ja) | 2013-05-09 |
KR101322067B1 (ko) | 2013-10-25 |
KR20110075630A (ko) | 2011-07-06 |
EP2520680A4 (fr) | 2014-11-19 |
CN102782169A (zh) | 2012-11-14 |
JP5657026B2 (ja) | 2015-01-21 |
WO2011081350A2 (fr) | 2011-07-07 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2520680B1 (fr) | Feuillard d'acier à résistance mécanique élevée ayant une excellente résistance au traitement thermique post-soudage et son procédé de fabrication | |
KR100833069B1 (ko) | 내hic특성 및 haz 인성이 우수한 인장강도 500㎫급압력용기용 강판 및 그 제조 방법 | |
KR101657828B1 (ko) | Pwht 후 인성이 우수한 고강도 압력용기용 강재 및 그 제조방법 | |
KR101998991B1 (ko) | 인장강도 및 저온충격인성이 우수한 압력용기용 강판 및 그 제조방법 | |
KR101417231B1 (ko) | 저온인성 및 인장특성이 우수한 압력용기용 극후강판 및 그 제조 방법 | |
EP2660346A2 (fr) | Tôle d'acier à haute résistance ayant ténacité supérieure à des températures cryogéniques et son procédé de fabrication | |
KR101568523B1 (ko) | 소려 취화 저항성이 우수한 압력용기용 강판 및 그 제조 방법 | |
KR102209581B1 (ko) | 용접열영향부 인성이 우수한 강재 및 이의 제조방법 | |
KR101819380B1 (ko) | 저온인성이 우수한 고강도 고망간강 및 그 제조방법 | |
KR101536478B1 (ko) | 저온 인성 및 sscc 저항성이 우수한 고압용기용 강재, 이의 제조방법 및 딥 드로잉 제품의 제조방법 | |
EP2215280B1 (fr) | Acier à haute résistance à la traction pour emboutissage profond et procédé de fabrication de celui-ci | |
JP6691967B2 (ja) | 靭性及び耐切断割れ性に優れた高硬度耐摩耗鋼、並びにその製造方法 | |
KR101253888B1 (ko) | 용접 후 열처리 저항성이 우수한 고강도 강판 및 그 제조방법 | |
KR101482342B1 (ko) | 용접성 및 굽힘가공성이 우수한 고강도 열연강판 및 그 제조방법 | |
KR100833070B1 (ko) | 내hic특성이 우수한 인장강도 500㎫급 압력용기용 강판및 그 제조 방법 | |
KR20160078624A (ko) | 저온인성 및 강도가 우수한 강관용 열연강판 및 그 제조방법 | |
KR102031451B1 (ko) | 저온인성이 우수한 저항복비 고강도 강관용 강재 및 그 제조방법 | |
KR101546154B1 (ko) | 유정용 강관 및 그 제조 방법 | |
KR102255823B1 (ko) | 성형성이 우수한 고항복비형 강판 및 그 제조방법 | |
KR102321269B1 (ko) | 고강도 강판 및 이의 제조방법 | |
KR101271968B1 (ko) | 용접 후 열처리 저항성이 우수한 중고온용 강판 및 그 제조방법 | |
KR20180073007A (ko) | 강도 및 저온 충격인성이 우수한 강재 및 그 제조방법 | |
KR101568504B1 (ko) | Pwht 후 강도 및 인성이 우수한 압력용기용 강판 및 그 제조방법 | |
KR102031450B1 (ko) | 고강도 강판 및 그 제조방법 | |
KR101560943B1 (ko) | 저온 인성이 우수한 강관용 열연강판 및 그 제조방법 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 20120724 |
|
AK | Designated contracting states |
Kind code of ref document: A2 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
DAX | Request for extension of the european patent (deleted) | ||
A4 | Supplementary search report drawn up and despatched |
Effective date: 20141016 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: B21B 1/22 20060101ALI20141010BHEP Ipc: C21D 8/02 20060101ALI20141010BHEP Ipc: B21B 3/02 20060101ALI20141010BHEP Ipc: C22C 38/00 20060101AFI20141010BHEP |
|
17Q | First examination report despatched |
Effective date: 20151019 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
INTG | Intention to grant announced |
Effective date: 20160506 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: REF Ref document number: 840097 Country of ref document: AT Kind code of ref document: T Effective date: 20161115 |
|
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: 602010037540 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 7 |
|
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: 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: 20161026 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20161226 Year of fee payment: 7 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20161026 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 840097 Country of ref document: AT Kind code of ref document: T Effective date: 20161026 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20161026 Ref country code: NO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20170126 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: 20161026 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: 20170127 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20161026 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: 20161026 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: 20161026 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: 20161026 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: 20161026 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: 20170227 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: 20161026 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: 20170226 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: 20161026 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 20161228 Year of fee payment: 7 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R026 Ref document number: 602010037540 Country of ref document: DE |
|
PLBI | Opposition filed |
Free format text: ORIGINAL CODE: 0009260 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20161026 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: 20161026 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: 20161026 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: 20161026 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: 20161026 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
26 | Opposition filed |
Opponent name: HERZOG, MARTIN / HERZOG FIESSER & PARTNER Effective date: 20170726 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20170126 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: 20161026 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: 20161026 |
|
PLAX | Notice of opposition and request to file observation + time limit sent |
Free format text: ORIGINAL CODE: EPIDOSNOBS2 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20170126 |
|
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: 20161026 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161231 Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161222 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161231 |
|
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: 20161026 Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20170126 Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161222 |
|
PLAF | Information modified related to communication of a notice of opposition and request to file observations + time limit |
Free format text: ORIGINAL CODE: EPIDOSCOBS2 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20171107 Year of fee payment: 8 |
|
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: 20161026 Ref country code: HU Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO Effective date: 20101222 |
|
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: 20161026 Ref country code: TR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20161026 |
|
RDAF | Communication despatched that patent is revoked |
Free format text: ORIGINAL CODE: EPIDOSNREV1 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R064 Ref document number: 602010037540 Country of ref document: DE Ref country code: DE Ref legal event code: R103 Ref document number: 602010037540 Country of ref document: DE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20161222 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST Effective date: 20180831 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: FP Effective date: 20170124 Ref country code: BE Ref legal event code: MM Effective date: 20171231 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180102 |
|
RDAG | Patent revoked |
Free format text: ORIGINAL CODE: 0009271 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: PATENT REVOKED |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171231 |
|
27W | Patent revoked |
Effective date: 20180726 |
|
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: 20161026 |