[go: up one dir, main page]

EP2799585B1 - Plaque d'acier épaisse de haute résistance mécanique pour structure dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes, et procédé de fabrication de celle-ci - Google Patents

Plaque d'acier épaisse de haute résistance mécanique pour structure dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes, et procédé de fabrication de celle-ci Download PDF

Info

Publication number
EP2799585B1
EP2799585B1 EP12863931.7A EP12863931A EP2799585B1 EP 2799585 B1 EP2799585 B1 EP 2799585B1 EP 12863931 A EP12863931 A EP 12863931A EP 2799585 B1 EP2799585 B1 EP 2799585B1
Authority
EP
European Patent Office
Prior art keywords
less
steel plate
temperature
thickness direction
central portion
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
EP12863931.7A
Other languages
German (de)
English (en)
Other versions
EP2799585A4 (fr
EP2799585A1 (fr
Inventor
Yoshiko TAKEUCHI
Kazukuni Hase
Shinji Mitao
Yoshiaki Murakami
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.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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 JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP2799585A1 publication Critical patent/EP2799585A1/fr
Publication of EP2799585A4 publication Critical patent/EP2799585A4/fr
Application granted granted Critical
Publication of EP2799585B1 publication Critical patent/EP2799585B1/fr
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
    • 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • C21D8/02—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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • 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
    • C22C38/02—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • 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

Definitions

  • the present invention relates to a method for manufacturing a high-strength thick steel plate for structural use having excellent brittle crack arrestability, and in particular, to a method for manufacturing a steel plate having a thickness of 50 mm or more which can be preferably used for ships.
  • Patent Literature 1 proposes a steel material having an ultra-fine crystallization structure in the surface portion in order to improve brittle crack arrestability without an increase in alloy cost.
  • the steel material having excellent brittle crack arrestability according to Patent Literature 1 is characterized in that, focusing on the fact that shear lips (plastic deformation areas), which are formed in the surface portion of a steel material when a brittle crack propagates, are effective for improving brittle crack arrestability, the crystal grain size in the portion of shear-lips is decreased in order to absorb the propagation energy of a propagating brittle crack.
  • an ultra fine ferrite structure or bainite structure is formed in the surface portion of the steel material by repeating once or more a process, in which the surface portion of a hot-rolled steel plate is cooled down to a temperature equal to or lower than the Ar 3 transformation point by performing controlled cooling and then the controlled cooling is stopped in order to allow the surface portion to recuperate to have a temperature equal to or higher than the transformation point, while the steel material is rolled in order for transformation or recrystallization due to deformation to repeatedly occur.
  • Patent Literature 2 it is disclosed that, in order to improve the brittle crack arrestability of a steel material having a microstructure mainly including a ferrite-pearlite phase, it is important to form a layer, in either of the surface portions of the steel material, including 50% or more of a ferrite structure having ferrite grains with a circle-equivalent average grain size of 5 ⁇ m or less and an aspect ratio of the grains of 2 or more, and to prevent the variation of a ferrite grain size, and that, as a method for preventing the variation, the maximum rolling reduction per pass of finishing rolling is controlled to be 12% or less in order to prevent local recrystallization.
  • Patent Literature 3 discloses a technique which is a modification of TMCP and in which, focusing on not only a decrease in ferrite crystal grain size but also a subgrain formed in a ferrite crystal grain, brittle crack arrestability is improved.
  • brittle crack arrestability is improved by controlling (a) rolling conditions such that fine ferrite crystal grains are achieved, (b) rolling conditions such that a fine ferrite structure is formed in a portion constituting 5% or more of the thickness of the steel material, (c) rolling conditions such that subgrains are formed by growing a texture in the fine ferrite and by rearranging dislocations introduced by applying deformation (rolling) using thermal energy and (d) cooling conditions such that an increase in the grain size of the formed fine ferrite crystal grains and in the grain size of the formed fine subgrains is prevented.
  • brittle crack arrestability is improved by applying reduction force of rolling to a transformed ferrite phase in order to grow a texture.
  • Resistance to brittle fractures is increased by forming a separation parallel to the plate surface on the fracture surface of a steel material in order to reduce stress at the brittle crack tip.
  • Patent Literature 4 discloses that brittle fracture resistance is improved by performing controlled rolling in order to form a microstructure having an X-ray intensity ratio in the (110) plane showing a texture developing degree of 2 or more and including large-size grains having a diameter equivalent to a circle in the crystal grains of 20 ⁇ m or more in an amount of 10% or less.
  • Patent Literature 5 discloses, as a steel for welded structural use having excellent brittle crack arrestability in the joint part, a steel plate having an X-ray plane intensity ratio in the (100) plane showing a texture developing degree on a plane inside the plate parallel to the rolling surface of the plate of 1.5 or more. It is disclosed that the steel plate has excellent brittle crack arrestability owing to the difference in angle between the direction of applied stress and the direction of crack propagation as a result of the growth of the texture mentioned above.
  • JP2010202931 A discloses a textured high-strength thick steel plate and a method for producing the same.
  • the steel plates having excellent brittle crack arrestability according to Patent Literatures 1 through 5 described above are mainly intended for a steel plate having a thickness of about 50 mm or less as indicated by the manufacturing conditions and the disclosed experimental data. It is not clear whether specified properties can be obtained in the case where the disclosed techniques are applied to thick material having a thickness of more than 50 mm, and the properties regarding crack propagation in the thickness direction which are required for ship's hull structures have never been tested at all.
  • an object of the present invention is to provide a method for manufacturing a high-strength thick steel plate having excellent brittle crack arrestability which can be stably manufactured using a very simple industrial process in which rolling conditions are optimized to control a texture in the thickness direction.
  • the present inventors diligently conducted investigations in order to solve the problems described above and found the following knowledge regarding a high-strength thick steel plate having excellent crack arrestability despite the steel plate having a heavy thickness.
  • a method for manufacturing a high-strength thick steel plate having a thickness of 50 mm or more having excellent brittle crack arrestability, in which a texture in the thickness direction is appropriately controlled can be provided, and it is effective to apply the present invention to a steel plate having a thickness of preferably more than 50 mm, more preferably 55 mm or more.
  • the present invention contributes to the improvement of the safety of ships by being applied to hutch side coamings and deck part materials in high-strength deck structures of large container carriers and bulk carriers, which results in a large advantage in industry.
  • Fig. 1 is a schematic diagram illustrating the fracture surface shape of an ESSO test compliant with WES 3003 of a thick steel plate having a thickness of more than 50 mm, where (a) is a diagram illustrating a plane view of a test piece and (b) is a diagram illustrating the fracture surface of the test piece.
  • a fracture surface shape illustrated in Fig. 1 with which crack arrestability can be increased against a crack propagating in the horizontal direction (planar direction) such as the rolling direction or a direction at a right angle to the rolling direction toughness and the integration degree I of the RD//(110) plane in the surface portion and the central portion in the thickness direction are appropriately specified.
  • a Charpy fracture appearance transition temperature vTrs in the surface portion be -60°C or lower and that a Charpy fracture appearance transition temperature vTrs in the central portion in the thickness direction be -50°C or lower. It is preferable that the Charpy fracture appearance transition temperature vTrs in the central portion in the thickness direction be -60°C or lower.
  • cleavage planes are integrated diagonally to the main direction of a crack in order to form fine branched cracks, which results in an increase in brittle crack arrestability owing to a stress relaxation effect at a brittle crack tip.
  • the integration degree I of the RD//(110) plane in the surface portion be 1.3 or more, preferably 1.6 or more, and that the integration degree I of the RD//(110) plane in the central portion in the thickness direction be 1.8 or more, preferably 2.0 or more.
  • the integration degree I of the RD//(110) plane in the surface portion or the central portion in the thickness direction is defined in the following way. Firstly, by performing mechanical polishing and electrolytic polishing on a surface, being parallel to the steel plate surface, of a sample having a thickness of 1 mm cut out of the surface portion or the central portion in the thickness direction, a test piece for X-ray diffractometry is prepared. Incidentally, in the case of the surface portion, the surface of the sample nearer to the outermost surface is polished. By performing X-ray diffraction measurement using a Mo X-ray source on this test piece, the pole figures of (200), (110) and (211) planes are obtained.
  • the Charpy fracture appearance transition temperature and the integration degrees I of the RD//(110) plane in the surface portion and the central portion in the thickness direction satisfy the relational expression (1) below: vTrs surface + 1.9 ⁇ vTrs 1 / 2 t ⁇ 6 ⁇ I RD / / 110 surface ⁇ 84 ⁇ I RD / / 110 1 / 2 t ⁇ ⁇ 350
  • a metallographic structure mainly includes a ferrite phase.
  • a metallographic structure mainly includes a ferrite phase means that the area fraction of a ferrite phase is 60% or more with respect to the whole metallographic structure.
  • the area fraction of the remainder consisting of, for example, a bainite phase, a martensite phase (including martensite islands) and a pearlite phase is 40% or less.
  • a metallographic structure mainly including a ferrite phase is obtained by performing rolling under ordinary rolling conditions for an austenite phase
  • target toughness can be obtained in a structure mainly including a ferrite phase
  • the obtained texture becomes a random structure, which results in the target value of the integration degree I of the RD//(110) plane in the surface portion, that is, 1.3 or more, preferably 1.6 or more, not being achieved, and which results in the target value of the integration degree I of the RD//(110) plane in the central portion in the thickness direction, that is, 1.8 or more, preferably 2.0 or more, not being achieved.
  • C is a chemical element which increases the strength of steel and it is necessary that the C content be 0.03% or more in order to achieve the desired strength as described in the present disclosure
  • the C content in the case where the C content is more than 0.20%, there is not only a decrease in weldability but also a negative influence on toughness. Therefore, it is preferable that the C content be 0.03% to 0.20%, more preferably 0.05% to 0.15%.
  • Si is effective as a deoxidizing chemical element and as a chemical element for increasing the strength of steel, the effect cannot be realized in the case where the Si content is less than 0.03%.
  • the Si content is more than 0.5%, there is not only the deterioration of the surface quality of steel but also a significant decrease in toughness. Therefore, it is preferable that the Si content be 0.03% or more and 0.5% or less.
  • Mn is added as a chemical element for increasing strength. Since the effect is insufficient in the case where the Mn content is less than 0.5%, and since there is a decrease in weldability and an increase in steel material cost in the case where the Mn content is more than 2.2%, it is preferable that the Mn content be 0.5% or more and 2.2% or less.
  • Al is effective as a deoxidizing agent, and it is necessary that the Al content be 0.005% or more in order to realize this effect, but, in the case where the Al content is more than 0.08%, there is not only a decrease in toughness but also a decrease in the toughness of a weld metal when welding is performed. Therefore, it is preferable that the Al content be 0.005% to 0.08%, more preferably 0.02% to 0.04%.
  • N increases the strength of steel by controlling a crystal grain size as a result of combining with Al in steel to form AlN when rolling is performed, but, since there is a decrease in toughness in the case where the N content is more than 0.0050%, it is preferable that the N content be 0.0050% or less.
  • the content of P and S be respectively 0.03% or less and 0.01% or less, more preferably 0.02% or less and 0.005% or less respectively.
  • a small content of Ti is effective for increasing the toughness of a base metal by decreasing a crystal grain size as a result of forming a nitride, carbide or carbonitride. This effect is realized in the case where the Ti content is 0.005% or more, but, since there is a decrease in the toughness of a base metal and a welded heat affected zone in the case where the Ti content is more than 0.03%, the Ti content is set to be 0.005% to 0.03%.
  • the chemical composition described above is the preferable base chemical composition used in the present invention
  • one or more of Nb, Cu, Ni, Cr, Mo, V, B, Ca and REM may be added in order to further improve the properties.
  • Nb contributes to an increase in strength as a result of precipitating in the form of NbC when ferrite transformation occurs or reheating is performed.
  • Nb since Nb is effective for expanding a temperature range in which recrystallization does not occur when rolling is performed under conditions for forming an austenite phase, which results in a decrease in ferrite grain size, Nb contributes to an increase in toughness. This effect is realized in the case where the Nb content is 0.005% or more, but, since there is conversely a decrease in toughness as a result of the precipitation of large-size NbC in the case the Nb content is more than 0.05%, it is preferable that the upper limit of the Nb content be 0.05%.
  • Cu, Ni, Cr and Mo are all chemical elements which increase the hardenability of steel. Since these chemical elements directly contribute to an increase in strength after rolling has been performed and may be added in order to improve functional properties such as toughness, high temperature strength or weather resistance, and since these effects are realized in the case where the contents of these chemical elements are respectively 0.01% or more, it is preferable that the contents of these chemical elements be respectively 0.01% or more in the case where these chemical elements are added. However, since there is a decrease in toughness and weldability in the case where the contents of these chemical elements are excessively large, it is preferable that the upper limits of the contents of Cu, Ni, Cr and Mo be respectively 0.5%, 1.0%, 0.5% and 0.5% in the case where these chemical elements are added.
  • V 0.001% to 0.10%
  • V is a chemical element which increases the strength of steel by precipitation strengthening as a result of precipitating in the form of V(C,N).
  • the V may be contained in the amount of 0.001% or more in order to realize this effect, but there is a decrease in toughness in the case where the V content is more than 0.10%. Therefore, in the case where V is added, it is preferable that the V content be in the range of 0.001% to 0.10%.
  • a small amount of B may be added as a chemical element which increases the hardenability of steel.
  • the B content is more than 0.0030%, since there is a decrease in the toughness of a weld zone, it is preferable that the B content be 0.0030% or less in the case where B is added.
  • Ca and REM increase toughness as a result of decreasing a grain size in a structure in a welded heat affected zone and there is no decrease in the effect of the present invention even in the case where these chemical elements are added, these chemical elements may be added as needed.
  • the upper limit of the contents of Ca and REM be respectively 0.0050% and 0.010% in the case where these are added.
  • manufacturing conditions such as the heating temperature of a slab as a steel material, hot rolling conditions and cooling conditions be specified.
  • hot rolling it is preferable to specify, in addition to total cumulative rolling reduction, cumulative rolling reduction and average rolling reduction per pass for each of the cases where the central portion in the thickness direction has a temperature in the austenite recrystallization temperature range and where the central portion in the thickness direction has a temperature in the austenite non-recrystallization temperature range.
  • molten steel having the chemical composition described above is produced using, for example, a converter furnace and made into a slab using, for example, a continuous casting method. Subsequently, the slab is heated at a temperature of 900°C to 1150°C and then hot-rolled.
  • the heating temperature is low in order to decrease a crystal grain size before rolling is performed, it is impossible to secure sufficient time for performing rolling in the austenite recrystallization temperature range in the case where the heating temperature is lower than 900°C.
  • the heating temperature is higher than 1150°C, since there is not only a decrease in toughness due to an increase in austenite grain size but also a decrease in yield due to a significant loss caused by oxidation, it is preferable that the heating temperature be 900°C to 1150°C, more preferably, the heating temperature be in the range of 1000°C to 1100°C from the viewpoint of toughness.
  • the target values of the integration degree I of the RD//(110) plane in the surface portion that is, 1.3 or more, preferably 1.6 or more, and of the integration degree I of the RD//(110) plane in the central portion in the thickness direction, that is, 1.8 or more, preferably 2.0 or more, cannot be achieved. Therefore, in the present invention, it is preferable to specify hot rolling conditions as described below.
  • hot rolling be performed, firstly, while the central portion in the thickness direction has a temperature in the austenite recrystallization temperature range, under the conditions that the cumulative rolling reduction is 20% or more and the average rolling reduction per pass is 5.0% or less.
  • the cumulative rolling reduction is 20% or more, since an austenite grain size becomes small, a grain size in a metallographic structure which is finally obtained becomes small, which results in an increase in toughness.
  • the average rolling reduction per pass in this temperature range is 5.0% or less, since it is possible to introduce strain into a steel material, in particular in the portion in the vicinity of the surface portion of the steel material, it is possible to control the integration degree I of the RD//(110) plane in the surface portion to be 1.3 or more, preferably 1.6 or more, and to further decrease the grain size in the surface portion, which results in an increase in the toughness of the surface portion.
  • the central portion in the thickness direction has a temperature in the austenite non-recrystallization temperature range, under the conditions that the cumulative rolling reduction is 40% or more and the average rolling reduction per pass is 7.0% or more.
  • the cumulative rolling reduction in this temperature range to be 40% or more, a texture in the central portion in the thickness direction can be sufficiently grown.
  • the average rolling reduction per pass it is possible to control the integration degree I of the RD//(110) plane in the central portion in the thickness direction to be 1.8 or more, preferably 2.0 or more.
  • the total cumulative rolling reduction in the austenite recrystallization temperature range and in the austenite non-recrystallization temperature range is preferable to control the total cumulative rolling reduction in the austenite recrystallization temperature range and in the austenite non-recrystallization temperature range to be 65% or more. This is because, by controlling the total cumulative rolling reduction to be 65% or more, it is possible to apply sufficient reduction to a structure, which results in the values of target toughness and strength being achieved.
  • the austenite recrystallization temperature range and the austenite non-crystallization temperature range are determined by performing preliminary experiments using steel having the chemical composition described above in which the steel is subjected to heating and processing history under various conditions.
  • finishing temperature of hot rolling from the view point of rolling efficiency, it is preferable that the finishing temperature be in the austenite non-recrystallization temperature range.
  • the rolled steel plate be cooled down to a temperature of 600°C or lower at a cooling rate of 4.0°C/s or more.
  • the cooling rate By controlling the cooling rate to be 4.0°C/s or more, since there is not an increase in grain size in a structure, the structure having a small grain size can be obtained, which results in the target excellent toughness being achieved.
  • the cooling rate is less than 4.0°C/s, since there is an increase in grain size in a structure, the target toughness cannot be achieved.
  • the cooling stop temperature to be 600°C or lower, since the progression of recrystallization is prevented, it is possible to maintain the desired texture which has been achieved through the hot rolling and the subsequent cooling.
  • the cooling rate and cooling stop temperature described above are determined by using the temperature of the central portion in the thickness direction of the steel plate.
  • the temperature of the central portion in the thickness direction can be derived from, for example, the thickness, the surface temperature, the cooling conditions and the like using, for example, simulation calculation. For example, by calculating the temperature distribution in the thickness direction using a difference method, the temperature of the central portion in the thickness direction of the steel plate can be derived.
  • a temper treatment may be performed on the cooled steel plate. By performing a tempering treatment, it is possible to further increase the toughness of steel plate. By controlling a tempering temperature to be equal to or lower than the A C1 point in terms of the average temperature of the steel plate, it is possible to prevent the desired structure obtained through rolling and cooling from being lost.
  • the A C1 point (°C) is derived using the equation below.
  • a c 1 point 751 ⁇ 26.6 C + 17.6 Si ⁇ 11.6 Mn ⁇ 169 Al ⁇ 23 Cu ⁇ 23 Ni + 24.1 Cr + 22.5 Mo + 233 Nb ⁇ 39.7 V ⁇ 5.7 Ti ⁇ 895 B , where an atomic symbol in the equation above represents the content (mass%) of the chemical element in the steel and where the symbol is assigned a value of 0 in the case where the chemical element is not contained.
  • the average temperature of the steel plate can be derived from, for example, the thickness, the surface temperature and the cooling conditions using, for example, simulation calculation, as is the case with the temperature of the central portion in the thickness direction.
  • molten steels (steel codes A through O) having the chemical compositions given in Table 1 using a converter furnace
  • molten steels steel codes A through O
  • slabs having a thickness of 250 mm
  • hot-rolling the slabs into hot-rolled steel plates having a thickness of 50 to 80 mm
  • sample steels No. 1 through No. 29 were obtained.
  • Some of the sample steels were subjected to a tempering treatment after having been cooled.
  • the hot rolling conditions, the cooling conditions and the tempering conditions are given in Table 2.
  • a fracture appearance transition temperature (vTrs) was determined.
  • vTrs fracture appearance transition temperature
  • Kca value at a temperature of -10°C was determined by performing an ESSO test compliant with WES 3003.
  • the integration degree I of the RD//(110) plane in the central portion in the thickness direction was derived in the following way. Firstly, by performing mechanical polishing and electrolytic polishing on the surface parallel to the steel plate surface of a sample having a thickness of 1 mm cut out of the central portion in the thickness direction, a test piece for X-ray diffractometry was prepared. By performing X-ray diffraction measurement using a Mo X-ray source on this test piece, the pole figures of (200), (110) and (211) planes were obtained. Three dimensional orientation distribution function was calculated from the obtained pole figures by using a Bunge method.
  • Sample steel plates (serial Nos. 1 through 13 and 27 through 29), which had the toughness indexes in the surface portion and the central portion in the thickness direction and textures which were within the range according to the present disclosure, had a Kca (-10°C) of 6000 N/mm 3/2 or more, which means these sample steel plates had excellent brittle crack arrestability.
  • sample steel plates (serial Nos. 1 through 13), each of which had the Charpy fracture appearance transition temperature and the integration degree I of the RD//(110) plane in the surface portion and the central portion in the thickness direction satisfying the relational expression (1), had higher Kca(-10°C) than sample steel plates (serial Nos. 27 through 29) that do not satisfy the relational expression (1).
  • sample steel plates (serial Nos. 21 through 26), which were prepared under manufacturing conditions outside the range according to the present invention and had toughness or textures not satisfying the specifications according to the present disclosure, had a Kca(-10°C) of less than 6000 N/mm 3/2 .
  • Sample steel plates (serial Nos. 14 through 20), which had chemical compositions outside the preferable ranges according to the present invention, had toughness not satisfying the specifications according to the present disclosure and a Kca(-10°C) of less than 6000 N/mm 3/2 .

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)

Claims (2)

  1. Procédé pour la fabrication d'une plaque d'acier épaisse haute résistance pour une utilisation structurelle possédant une excellente capacité d'arrêt de propagation de fissures cassantes, le procédé comprenant le chauffage d'une brame à une température de 900°C ou plus et de 1150°C ou moins, la mise en oeuvre d'un laminage dans lequel une réduction cumulative totale de laminage dans la plage de températures de recristallisation d'austénite et dans la plage de températures de non recristallisation d'austénite s'élève à 65 % ou plus, dans lequel, tandis que la portion centrale dans la direction d'épaisseur possède une température dans la plage de températures de recristallisation d'austénite, la réduction cumulative de laminage est commandée pour s'élever à 20 % ou plus et la réduction moyenne de laminage par passage est commandée pour s'élever à 5 % ou moins, et dans lequel, à la suite, tandis que la portion centrale dans la direction d'épaisseur possède une température dans la plage de températures de non recristallisation d'austénite, la réduction cumulative de laminage est commandée pour s'élever à 40 % ou plus et la réduction moyenne de laminage par passage est commander pour s'élever à 7 % ou moins, et la mise en oeuvre d'un refroidissement accéléré de la plaque d'acier laminée jusqu'à une température de 600°C ou moins à une vitesse de refroidissement de 4°C/s ou plus ;
    dans lequel la brame possède une composition chimique constituée par, en % en masse, C : 0,03 % ou plus et 0,20 % ou moins ; Si : 0,03 % ou plus et 0,5 % ou moins ; Mn : 0,5 % ou plus et 2,2 % ou moins ; Al : 0,005 % ou plus et 0,08 % ou moins ; P : 0,03 % ou moins ; S : 0,01 % ou moins ; N : 0,0050 % ou moins ; Ti : 0,005 % ou plus et 0,03 % ou moins, et de manière facultative, en % en masse, un ou plusieurs éléments choisis parmi Nb : 0,005 % ou plus et 0,05 % ou moins ; Cu : 0,01 % ou plus et 0,5 % ou moins ; Ni : 0,01 % ou plus et 1 % ou moins ; Cr : 0,01 % ou plus et 0,5 % ou moins ; Mo : 0,01 % ou plus et 0,5 % ou moins ; V : 0,001 % ou plus et 0,10 % ou moins ; B : 0,0030 % ou moins ; Ca : 0,0050 % ou moins ; et REM : 0,010 % ou moins, le reste étant du Fe et des impuretés inévitables.
  2. Procédé pour la fabrication d'une plaque d'acier épaisse haute résistance pour une utilisation structurelle possédant une excellente capacité d'arrêt de propagation de fissures cassantes selon la revendication 1, le procédé comprenant en outre un procédé dans lequel la plaque d'acier qui a été soumise à un refroidissement accéléré jusqu'à une température de 600°C ou moins est soumise à une trempe à une température égale ou inférieure au point AC1.
EP12863931.7A 2011-12-27 2012-05-18 Plaque d'acier épaisse de haute résistance mécanique pour structure dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes, et procédé de fabrication de celle-ci Active EP2799585B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2011285569 2011-12-27
JP2012111157A JP5304924B2 (ja) 2011-12-27 2012-05-15 脆性亀裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
PCT/JP2012/063410 WO2013099319A1 (fr) 2011-12-27 2012-05-18 Plaque d'acier épaisse de haute résistance mécanique pour structure dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes, et procédé de fabrication de celle-ci

Publications (3)

Publication Number Publication Date
EP2799585A1 EP2799585A1 (fr) 2014-11-05
EP2799585A4 EP2799585A4 (fr) 2015-01-14
EP2799585B1 true EP2799585B1 (fr) 2017-01-18

Family

ID=48696842

Family Applications (1)

Application Number Title Priority Date Filing Date
EP12863931.7A Active EP2799585B1 (fr) 2011-12-27 2012-05-18 Plaque d'acier épaisse de haute résistance mécanique pour structure dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes, et procédé de fabrication de celle-ci

Country Status (6)

Country Link
EP (1) EP2799585B1 (fr)
JP (1) JP5304924B2 (fr)
KR (1) KR101588261B1 (fr)
CN (1) CN104011250B (fr)
BR (1) BR112014015795B1 (fr)
WO (1) WO2013099319A1 (fr)

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105102651B (zh) * 2013-03-26 2018-01-05 杰富意钢铁株式会社 脆性裂纹传播停止特性优良的大线能量焊接用高强度钢板及其制造方法
CN104264047B (zh) * 2014-09-15 2016-06-08 南京钢铁股份有限公司 一种集装箱船用特厚钢板及其制备方法
WO2016143345A1 (fr) * 2015-03-12 2016-09-15 Ｊｆｅスチール株式会社 Tôle d'acier épaisse à haute résistance et son procédé de fabrication
CN108026618B (zh) * 2015-09-18 2020-03-06 杰富意钢铁株式会社 结构用高强度厚钢板及其制造方法
WO2017145651A1 (fr) * 2016-02-24 2017-08-31 Ｊｆｅスチール株式会社 Tôle d'acier ultra-épaisse de haute résistance, ayant d'excellentes caractéristiques d'arrêt de la propagation des fissures fragiles et son procédé de fabrication
RU2630086C1 (ru) * 2016-06-14 2017-09-05 Федеральное государственное бюджетное образовательное учреждение высшего образования "Калининградский государственный технический университет" Малокремнистая судостроительная сталь
KR101899694B1 (ko) * 2016-12-23 2018-09-17 주식회사 포스코 저온 충격인성 및 ctod 특성이 우수한 후강판 및 그 제조방법
KR102255828B1 (ko) * 2019-12-16 2021-05-25 주식회사 포스코 구조용 강재 및 그 제조방법

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07100814B2 (ja) 1990-09-28 1995-11-01 新日本製鐵株式会社 脆性亀裂伝播停止特性と低温靭性の優れた鋼板の製造方法
JP2659661B2 (ja) 1993-01-06 1997-09-30 新日本製鐵株式会社 継手部の脆性破壊伝播停止性能の優れた溶接用構造用鋼とその製造方法
JPH07100814A (ja) 1993-10-04 1995-04-18 Sekisui Chem Co Ltd セメント成形品の製造方法
JPH08209239A (ja) * 1995-02-01 1996-08-13 Kobe Steel Ltd −５０℃以下の脆性亀裂伝播停止特性を有する低温用厚鋼材の製造方法
JP3548349B2 (ja) 1996-09-18 2004-07-28 新日本製鐵株式会社 塑性変形後の耐脆性破壊特性の優れた構造用鋼板
JP3467767B2 (ja) 1998-03-13 2003-11-17 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れた鋼材およびその製造方法
JP4077167B2 (ja) 2001-02-28 2008-04-16 株式会社神戸製鋼所 アレスト特性に優れた鋼板およびその製法
JP3848211B2 (ja) * 2002-05-31 2006-11-22 株式会社神戸製鋼所 低温靭性に優れた厚鋼板およびその製造方法
JP2004269924A (ja) * 2003-03-06 2004-09-30 Nippon Steel Corp 強度・靭性に優れた鋼板の高効率製造方法
JP5344454B2 (ja) * 2005-11-21 2013-11-20 独立行政法人物質・材料研究機構 温間加工用鋼、その鋼を用いた温間加工方法、およびそれにより得られる鋼材ならびに鋼部品
JP4910638B2 (ja) * 2006-10-31 2012-04-04 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れた厚鋼板の製造方法
JP4946512B2 (ja) * 2007-02-28 2012-06-06 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
JP4876972B2 (ja) * 2007-02-28 2012-02-15 Ｊｆｅスチール株式会社 板厚方向の耐疲労亀裂伝播特性に優れた溶接構造用厚鋼板およびその製造方法
JP5051001B2 (ja) * 2008-05-29 2012-10-17 住友金属工業株式会社 圧延方向に対し４５°方向のアレスト特性に優れた高強度厚肉鋼板およびその製造方法
JP5434145B2 (ja) * 2009-03-04 2014-03-05 Ｊｆｅスチール株式会社 脆性亀裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
JP5457938B2 (ja) * 2010-05-20 2014-04-02 株式会社神戸製鋼所 疲労亀裂進展抑制特性および靭性に優れた鋼板
EP2762583B1 (fr) * 2011-09-30 2018-11-07 Nippon Steel & Sumitomo Metal Corporation Tôle d'acier galvanisée à chaud à résistance élevée présentant une excellente résistance à la rupture retardée et son procédé de production

Non-Patent Citations (1)

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

Also Published As

Publication number Publication date
KR20140094022A (ko) 2014-07-29
WO2013099319A1 (fr) 2013-07-04
EP2799585A4 (fr) 2015-01-14
BR112014015795A8 (pt) 2017-07-04
CN104011250B (zh) 2017-03-08
JP5304924B2 (ja) 2013-10-02
BR112014015795B1 (pt) 2019-02-12
CN104011250A (zh) 2014-08-27
KR101588261B1 (ko) 2016-01-25
BR112014015795A2 (pt) 2017-06-13
EP2799585A1 (fr) 2014-11-05
JP2013151731A (ja) 2013-08-08

Similar Documents

Publication Publication Date Title
EP2799584B1 (fr) Procédé de fabrication d'une plaque d'acier épaisse de haute résistance mécanique pour structure dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes
EP2799585B1 (fr) Plaque d'acier épaisse de haute résistance mécanique pour structure dotée d'excellentes propriétés d'arrêt de propagation de fissures cassantes, et procédé de fabrication de celle-ci
CN104011247B (zh) 脆性裂纹传播停止特性优良的高强度厚钢板及其制造方法
CN105102650B (zh) 脆性裂纹传播停止特性优良的大线能量焊接用高强度厚钢板及其制造方法
JP5598617B1 (ja) 脆性亀裂伝播停止特性に優れた大入熱溶接用高強度厚鋼板およびその製造方法
JP2018024905A (ja) 脆性亀裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
JP5812193B2 (ja) 脆性き裂伝播停止特性に優れた構造用高強度厚鋼板およびその製造方法
CN104024456B (zh) 脆性裂纹传播停止特性优良的结构用高强度厚钢板及其制造方法
TWI650431B (zh) 高強度厚鋼板及其製造方法
JP2013133543A (ja) 厚鋼板及び厚鋼板の製造方法

Legal Events

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

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20140702

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

A4 Supplementary search report drawn up and despatched

Effective date: 20141212

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/14 20060101AFI20141208BHEP

Ipc: C21D 8/02 20060101ALI20141208BHEP

Ipc: C22C 38/58 20060101ALI20141208BHEP

DAX Request for extension of the european patent (deleted)
17Q First examination report despatched

Effective date: 20151218

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20160908

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: 862975

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170215

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: 602012028103

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20170118

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

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

Ref country code: NL

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

Effective date: 20170118

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

Ref country code: HR

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

Effective date: 20170118

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: 20170118

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: 20170118

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: 20170518

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: 20170419

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: 20170418

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

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: 20170118

Ref country code: LU

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

Effective date: 20170531

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: 20170118

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: 20170418

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: 20170118

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: 20170518

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: 20170118

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: 20170118

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602012028103

Country of ref document: DE

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

Ref country code: SK

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

Effective date: 20170118

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: 20170118

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: 20170118

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: 20170118

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: 20170118

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

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: 20170118

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: 20170118

26N No opposition filed

Effective date: 20171019

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

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

Effective date: 20170518

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: 20170118

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: 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: 20170118

Ref country code: CH

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

Effective date: 20170531

Ref country code: LI

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

Effective date: 20170531

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20180131

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

Ref country code: LU

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

Effective date: 20170518

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20170531

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

Ref country code: GB

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

Effective date: 20170518

Ref country code: IE

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

Effective date: 20170518

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: 20170531

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: 20170531

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: 20170518

REG Reference to a national code

Ref country code: AT

Ref legal event code: UEP

Ref document number: 862975

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170118

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

Ref country code: HU

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

Effective date: 20120518

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: 20170118

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: 20170118

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

Ref country code: TR

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

Effective date: 20170118

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: 20170118

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

Ref country code: DE

Payment date: 20240328

Year of fee payment: 13

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

Ref country code: AT

Payment date: 20240425

Year of fee payment: 13