EP2123780A1 - Verfahren zur herstellung von stahlblechen für becher - Google Patents

Verfahren zur herstellung von stahlblechen für becher Download PDF

Info

Publication number
EP2123780A1
EP2123780A1 EP08711889A EP08711889A EP2123780A1 EP 2123780 A1 EP2123780 A1 EP 2123780A1 EP 08711889 A EP08711889 A EP 08711889A EP 08711889 A EP08711889 A EP 08711889A EP 2123780 A1 EP2123780 A1 EP 2123780A1
Authority
EP
European Patent Office
Prior art keywords
temperature
steel sheet
less
annealing
recrystallization
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
Application number
EP08711889A
Other languages
English (en)
French (fr)
Other versions
EP2123780A4 (de
EP2123780B1 (de
Inventor
Yuka Nishihara
Katsumi Kojima
Hiroki Iwasa
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
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=39710169&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP2123780(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP2123780A1 publication Critical patent/EP2123780A1/de
Publication of EP2123780A4 publication Critical patent/EP2123780A4/de
Application granted granted Critical
Publication of EP2123780B1 publication Critical patent/EP2123780B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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

Definitions

  • the present invention relates to a process for manufacturing a tin mill black plate used for 2-piece DRD cans (two-piece drawn and redrawn cans) and 3-piece welded cans (three-piece welded cans) used as cans or containers for canned beverages or canned foods.
  • the steel sheets need to have a Rockwell hardness (HR30T) of about 73 to 77 (at least 73 to 76 and preferably 74 to 77) and high strength, that is, a tensile strength (TS) of about 550 to 620 MPa.
  • HR30T Rockwell hardness
  • TS tensile strength
  • Extremely thin, hard tin mill black plates are manufactured by a double reduce process (hereinafter referred to as the DR process) including annealing followed by secondary cold rolling at present.
  • the tin mill black plates are manufactured through a hot rolling step, a cold rolling step, an annealing step, and a secondary cold rolling step. That is, the number of steps in the DR process is one greater than that of steps in an ordinary process ended with an annealing step; hence, the DR process is high in manufacturing cost.
  • This type of tin mill black plate needs to be manufactured at low cost. Therefore, the following processes have been proposed:
  • Patent Document 1 Japanese Unexamined Patent Application Publication No. 2001-107186 (Patent Document 1) and Japanese Unexamined Patent Application Publication No. 2005-336610 (Patent Document 2) disclose high-strength tin mill black plates subjected to recrystallization annealing.
  • the tin mill black plates subjected to recrystallization annealing have low in-plate plastic anisotropy and therefore are suitable for drawn cans in which earing needs to be minimized.
  • a steel sheet that need not have low in-plate plastic anisotropy need not be necessarily subjected to recrystallization annealing after cold rolling.
  • the following technique may be used instead of recrystallization annealing: a technique in which the steel sheet is cold-rolled so as to have increased strength and then heat-treated (called "recovery annealing") at low temperature such that the excessive strain introduced therein by cold-rolling is relieved or the ductility of the material is recovered to a minimum extent.
  • recovery annealing a technique in which the steel sheet is cold-rolled so as to have increased strength and then heat-treated (called "recovery annealing") at low temperature such that the excessive strain introduced therein by cold-rolling is relieved or the ductility of the material is recovered to a minimum extent.
  • recovery annealing a technique in which the steel sheet is cold-rolled so as to have increased strength and then heat-treated at low temperature such that the excessive strain introduced therein by cold-rolling is relieved or the duct
  • Patent Document 3 discloses a technique in which a steel material is hot-rolled at a finishing temperature lower than or equal to the Ar 3 transformation point thereof and the hot-rolled steel sheet is coiled at high temperature so as to have a grain size of 50 ⁇ m or more. According to this technique, the hot-rolled steel sheet is cold-rolled at a reduction rate of 85% to 90% and then subjected to continuous annealing at 450°C to 580°C, whereby a tin mill black plate having a TS of 53 to 57 kgf/mm 2 and an El (total elongation) of 6% to 8% is obtained. A material used is capped steel containing 0.05% to 0.06% C.
  • Patent Document 4 discloses a technique for manufacturing a tin mill black plate having a YS (yield strength) of 640 MPa or more.
  • This tin mill black plate is manufactured in such a manner that a steel material containing REM which is an essential component therefor is hot-rolled at a finishing temperature lower than or equal to the Ar 3 transformation point thereof, the hot-rolled steel sheet is cold-rolled at a reduction rate of 85% or less, and the cold-rolled steel sheet heat-treated at a temperature of 200°C to 500°C for ten minutes or more.
  • Patent Document 5 discloses a technique in which a tempered grade T4-T6 tin mill black plate free from stretcher strain is manufactured by annealing a cold-rolled steel sheet at a temperature ranging from 400°C to the recrystallization temperature thereof.
  • the tin mill black plate manufactured by this technique has a Rockwell hardness (HR30T) of up to 72.9.
  • Patent Document 6 discloses a technique for manufacturing a tin mill black plate having high rigidity (the Rockwell hardness thereof is substantially the same as that disclosed in Patent Document 5).
  • This tin mill black plate is manufactured in such a manner that a steel material having the same composition (specified as follows: C: 0.03% by weight or less, N: 0.005% by weight or less, and so on) as that disclosed in Patent Document 5 is hot-rolled at a finishing temperature lower than or equal to the Ar 3 transformation point thereof at a reduction rate of 50% or more, the hot-rolled steel sheet is cold-rolled at a reduction rate of 50% or more, and the cold-rolled steel sheet is annealed at a temperature ranging from 400°C to the recrystallization temperature thereof.
  • the recrystallization temperature is defined as a temperature at which the percentage of recrystallized microstructures is less than 10%.
  • Patent Document 7 discloses a technique for manufacturing a steel sheet having a YS of 54 to 70 kgf/mm 2 .
  • This steel sheet is manufactured in such a manner that a steel material is finish-rolled such that a total reduction rate at a temperature lower than or equal to the Ar 3 transformation point thereof is 40% or more during hot rolling, the hot-rolled steel sheet is cold-rolled at a reduction rate of 50% or more, and the cold-rolled steel sheet is annealed at a low temperature of 350°C to 650°C for a short time.
  • each steel material needs to be finish-rolled at a temperature lower than or equal to the Ar 3 transformation point thereof during hot rolling.
  • the hot-rolled steel sheet prepared by finish rolling at a temperature lower than or equal to the Ar 3 transformation point has a large ferrite grain size and therefore has low strength as shown in Fig. 3 of Patent Document 3.
  • these techniques are effective in reducing the strength of steel to such an extent that sufficient workability can be achieved.
  • finish rolling is performed at a temperature lower than or equal to the Ar 3 transformation point, widthwise edge portions are cooled at a rate greater than that of a widthwise center portion; hence, the finish-rolling temperature of the widthwise edge portions tends to be lower than that of the widthwise center portion.
  • the cold-rolled steel sheet is annealed at 200°C to 500°C for ten minutes or more such that the strain of the cold-rolled steel sheet is relieved. If the cold-rolled steel sheet needs to be annealed for ten minutes or more in a continuous annealing furnace, the line speed needs to be low. This leads to a significant reduction in productivity.
  • each cold-rolled steel sheet is annealed at a temperature ranging from 400°C to the recrystallization temperature thereof.
  • the obtained steel sheet has a Rockwell hardness of less than 73.0.
  • the annealing temperature needs to be reduced. This leads to the deviation from an annealing temperature range employed in the manufacture of materials for ordinary cans; hence, a dedicated annealing cycle needs to be used. This leads to a reduction in productivity.
  • the present invention has been made in view of the foregoing circumstances. It is an object of the present invention to solve the above problems and to provide a tin mill black plate with high strength.
  • the present invention provides a tin mill black plate which is used for applications, not requiring low in-plate plastic anisotropy, such as welded cans and which needs to have high strength and workability. It is another object of the present invention to provide a process for manufacturing a high-strength tin mill black plate which has a sufficient ductility necessary to machine, for example, flanges of welded cans.
  • target properties can be achieved by meeting the following two requirements as the feature of this invention and major requirements:
  • recovery annealing can be performed in a temperature range (500°C to 700°C) substantially equal to an annealing temperature range used in the manufacture of current tin mill black plates under the above manufacturing conditions adding at least one of 0.001% to 0.05% Nb and 0.0001% to 0.005% B and a tensile strength of 550 to 650 MPa or 550 to 700 MPa can be achieved.
  • the present invention has been made on the basis of the above findings.
  • the substance of the present invention is as described below.
  • the content of a steel component used herein is expressed on a mass basis.
  • Mn: 0.05% to 0.5% herein means “Mn: 0.05% or more and 0.5% or less", that is, “0.05% ⁇ Mn ⁇ 0.5%”.
  • recrystallization starting temperature is defined as a temperature at which a change in strength greatly varies as shown in Fig. 1 (an example and conditions below). In particular, this term is defined as a temperature at which a microstructure in which recrystallized microstructures occupy 5% of the structure is obtained.
  • a tin mill black plate manufactured by a process according to the present invention has a tensile strength of 550 to 650 MPa (see Fig. 1 ) and a total elongation of 5% or more.
  • the tin mill black plate contains Nb and/or B
  • the tin mill black plate has a tensile strength of 550 to 700 MPa (see Fig. 2 and conditions below) and a total elongation of 4% or more.
  • the manufacture of the tin mill black plate according to the present invention is characterized in that hot rolling is performed at a finishing temperature higher than or equal to a Ar 3 transformation point and then annealing is performed within a range from a temperature 200°C lower than the recrystallization starting temperature thereof to a temperature 20°C lower than the recrystallization starting temperature thereof.
  • the tin mill black plate according to the present invention has high strength due to the strain introduced thereinto by cold rolling (primary cold rolling). Therefore, any strengthening element is not essential and the content thereof is minimized in view of ductility.
  • the tin mill black plate contains greater than 0.003% C
  • the tin mill black plate has a local ductility insufficient to form cans.
  • An increase in the amount of remaining solute carbon may cause cracks in a can during the stretch-flange forming of a seeming part in the final step of can making.
  • the increase in the amount of solute carbon also increases the work hardening coefficient thereof and therefore may cause wrinkles during neck forming or flange forming.
  • the content of C is 0.003% or less.
  • the C content is less than 0.0010%, operability is reduced because of a reduction in the annealing temperature necessary to achieve a target strength specified herein and an improvement in ductility is reduced.
  • the C content is preferably 0.0010% or more.
  • N is an unavoidable impurity in steel.
  • An increase in the content of N may cause slab cracking in an unbending zone during continuous casting.
  • N forms precipitates, which cause a reduction in elongation.
  • the presence of the solute nitrogen causes steel to be hardened.
  • the content of N is 0.004% or less.
  • the N content is preferably 0.002% or less.
  • Si is a strengthening element enhancing the strength of steel by solid solution hardening and an increase in the content of Si causes a reduction in corrosion resistance.
  • the Si content is 0.02% or less.
  • Mn is a strengthening element enhancing the strength of steel by solid solution hardening. Mn reduces the size of crystal grains to increase the strength thereof by grain refining hardening. In order to prevent this adverse effect, the upper limit of the content of Mn is 0.5%. The Mn content is preferably 0.3% or less.
  • the lower limit of the Mn content is 0.05%.
  • the Mn content is preferably 0.10% or more.
  • P significantly increases the strength of steel by solid solution hardening and also deteriorates the corrosion resistance thereof.
  • the P content is 0.02% or less.
  • S exists as an inclusion in steel and is an element that is unfavorable for the ductility and corrosion resistance of steel; hence, the content of S is 0.03% or less.
  • the S content is preferably 0.01% or less.
  • Al serves as a deoxidizer to enhance the cleanliness of steel.
  • Al has an effect of reducing the amount of solute N because Al reacts with solute N to form AlN. Therefore, steel preferably contains a certain amount of Al.
  • the content of Al therein is preferably about 0.005% or more. When the Al content exceeds 0.1%, the effect of enhancing the cleanliness of steel is saturated and the following problems arise: an increase in manufacturing cost and an increase in surface defects. Thus, the Al content is 0.1% or less.
  • One or two selected from the group consisting of 0.001% to 0.05% Nb and 0.0001% to 0.005% B may be contained in addition to the above components.
  • Nb 0.001% to 0.05%
  • Nb is an element with a high ability to produce a carbide.
  • the pinning of grain boundaries by the carbide increases the recrystallization temperature of steel. Therefore, the steel recrystallization temperature can be varied by the addition of Nb or the variation of the content of Nb.
  • the annealing temperature can be appropriately increased or decreased, that is, the annealing temperature can be freely adjusted to a target value. This allows the tin mill black plate to be annealed at the same opportunity with another steel sheet and therefore is very efficient in view of productivity.
  • the recrystallization temperature is excessively high. This reduces the processing capability in a CAL (continuous annealing line). Furthermore, the strength exceeds a target value because of the precipitation hardening effect of the carbide. Thus, the Nb content is 0.05% or less.
  • Nb is preferably used in view of annealing temperature.
  • a desired strength can be achieved by the precipitation hardening effect of Nb in such a manner that the Nb content is adjusted to 0.05% or less.
  • the addition of Nb prevents recrystallization during welding and therefore is effective in preventing the reduction of weld strength.
  • the upper limit of the Nb content is preferably 0.04%. When the Nb content is less than 0.001%, the above advantages cannot be achieved; hence, the lower limit of the Nb content is 0.001% in the case where Nb is used for the purpose of achieving the above advantages.
  • the Nb content is preferably 0.005% or more and more preferably 0.01% or more.
  • B is an element increasing recrystallization temperature. Therefore, B may be used for the same purpose as that of Nb.
  • the use of an excessive amount of B prevents recrystallization of austenite during hot rolling to increase rolling load; hence, the content of B is 0.005% or less.
  • the B content is preferably 0.002% or less.
  • the B content is 0.0001% or less, the effect of enhancing the recrystallization temperature cannot be achieved; hence, the lower limit of the B content is 0.0001% in the case where B is used for the purpose of achieving this effect.
  • the B content is preferably 0.0005% or more and more preferably 0.0008% or more.
  • B as well as Nb, is effective in achieving a desired strength by the precipitation hardening effect of B when the B content is within the above range.
  • B prevents recrystallization during.welding and therefore is effective in preventing the reduction of weld strength.
  • Nb and B may be used within the above range.
  • the remainder is Fe and unavoidable impurities.
  • the thickness of the tin mill black plate is an important factor in the present invention. When the thickness thereof is 0.18 mm or less, it is meaningful to gauge down the tin mill black plate such that the tin mill black plate has a tensile strength of 550 MPa or more. Further, although steel sheets having a thickness exceeding 0.18 mm can be continuously annealed at high temperatures exceeding 750°C with ease, steel sheets having a thickness of 0.18 mm or less may be broken or deteriorated in shape during continuous annealing, which leads to a reduction in productivity.
  • an annealing temperature is set to be 20°C or more lower than a recrystallization starting temperature (usually to about 700°C or less as described in an example below); hence, a steel sheet having a thickness of 0.18 mm can be readily manufactured.
  • the thickness of the tin mill black plate is therefore limited to 0.18 mm or less because a tensile strength of 550 MPa or more is effective and annealing at low temperatures is remarkably effective in enhancing productivity.
  • An object of the tin mill black plate which is manufactured by a process according to the present invention, is that the tin mill black plate is used in a field where ultra-thin high-strength steel sheets such as DR materials are presently used and, in particular, is used for bodies of welded cans such as DRD cans.
  • a steel sheet having a thickness of 0.18 mm or less and a tensile strength of 550 MPa or less is used, the steel sheet may be buckled because its strength is insufficient.
  • the target tensile strength of the tin mill black plate is set to 550 MPa or more.
  • the tensile strength thereof is controlled to a target value mainly by adjusting the composition, cold rolling reduction rate, and/or annealing temperature of the tin mill black plate.
  • the tensile strength thereof is controlled to 550 to 650 MPa in such a manner that the tin mill black plate is prepared to so as to have a C content of 0.003% or less, a N content of 0.004% or less, a Mn content of 0.05% to 0.5%, a P content of 0.02% or less, a Si content of 0.02% or less, a S content of 0.03% or less, and an Al content of 0.1% or less; the cold rolling reduction rate thereof is adjusted to 60% or more; and annealing is performed at a soaking temperature 20°C to 200°C lower than the recrystallization starting temperature thereof (see Fig. 1 ).
  • the tensile strength thereof is controlled to 550 to 700 MPa in such a manner that the tin mill black plate is prepared to so as to have a C content of 0.003% or less, a N content of 0.004% or less, a Mn content of 0.05% to 0.5%, a P content of 0.02% or less, a Si content of 0.02% or less, a S content of 0.03% or less, an Al content of 0.1% or less, and at least one of a Nb content of 0.001% to 0.05% and a B content of 0.0001% to 0.005%; the cold-rolling reduction rate thereof is adjusted to 60% or more; and annealing is performed at a soaking temperature 20°C to 200°C lower than the recrystallization starting temperature thereof (see Fig. 2 ).
  • the Rockwell hardness (HR30T) of the tin mill black plate is about 74 to 77 when the tin mill black plate contains no Nb or B.
  • the Rockwell hardness (HR30T) thereof is about 74 to 80 when the tin mill black plate contains at least one of Nb and B.
  • the target total elongation thereof is 4% or more.
  • the total elongation thereof is preferably 5% or more.
  • the total elongation thereof is controlled to a target value mainly by adjusting the composition of the tin mill black plate or the cooling rate of the finish-rolled tin mill black plate in hot rolling.
  • a molten steel containing the above chemical components is produced by a known steel-making method using a converter and the like and then cast into a rolling material (a steel ingot or slab in particular) by an ordinary casting method such as a continuous casting method.
  • the obtained rolling material is hot-rolled into a hot-rolled steel sheet.
  • the rolling material Before being hot-rolled, the rolling material is preferably heated to 1250°C or more. This is because precipitates in steel are completely converted into solid solutions such that segregation is eliminated and thereby the rolling material is homogenized.
  • the finishing temperature of the hot-rolled steel sheet is higher than or equal to the Ar 3 transformation point thereof. Then, the hot-rolled steel sheet is coiled at 600°C to 750°C. The hot-rolled steel sheet is then usually pickled, whereby scales are removed therefrom. The resulting hot-rolled steel sheet is cold-rolled at a reduction rate of 60% to 95% and the cold-rolled steel sheet is annealed at a temperature of (recrystallization starting temperature - 200°C) to (recrystallization starting temperature - 20°C).
  • the finishing temperature during hot rolling needs to be higher than or equal to the Ar 3 transformation point of the steel sheet.
  • the finish rolling of the steel sheet at a temperature lower than the Ar 3 transformation point thereof has an advantage in reducing the strength of the steel sheet during recovery annealing. If, however, a slab is finish-rolled such that a center portion thereof has a temperature lower than its Ar 3 transformation point, widthwise edge portions thereof are cooled at a rate greater than that of the center portion; hence, it is difficult to relieve the strain introduced into each widthwise edge portion during finish rolling by recrystallization or recovery.
  • the finishing temperature needs to be higher than or equal to the Ar 3 transformation point.
  • the finishing temperature is preferably 5°C or more higher than the Ar 3 transformation point (i.e. (Ar 3 transformation point +5°C) or higher).
  • the finishing temperature is preferably 950°C or less.
  • the Ar 3 transformation point thereof is within a range from 840°C to 910°C.
  • the process according to the present invention allows the total elongation of steel to be adjusted by performing only hot rolling at a temperature higher than or equal to the Ar 3 transformation point. This is because as described below.
  • the hot-rolled steel sheet has a relatively small ferrite grain size.
  • this hot-rolled steel sheet has a relatively large ferrite grain size.
  • the cold-rolled steel sheet prepared from the hot-rolled steel sheet with a small ferrite grain size has higher strain energy. This is because this cold-rolled steel sheet has a large number of grain boundaries keeping strain. Since the driving force for a recovery phenomenon is the strain energy stored in this cold-rolled steel sheet, a condition of the present invention promotes the progress of the recovery phenomenon. This cold-rolled steel sheet is reduced in strength because of the recovery phenomenon. Since the condition thereof allows the strain energy to be maintained high, the strength of this cold-rolled steel sheet can be maintained at a high target value after recovery. The recovery phenomenon improves the ductility of this cold-rolled steel sheet; hence, the ductility thereof can be maintained at an appropriate target value. High-temperature finish hot rolling and high purity composition are preferably avoided because the grain size becomes large due to the above mechanism.
  • the coiling temperature of a hot rolling step needs to be 600°C to 750°C.
  • the hot-rolled steel sheet has excessively high strength because the heat retention of the coiled hot-rolled steel sheet is insufficient and therefore the hot-rolled steel sheet has an excessively small ferrite grain size.
  • a microstructure having a mixed grain size is likely to be formed, which is not preferable.
  • the coiling temperature exceeds 750°C, scales on the hot-rolled steel sheet have a significantly large thickness and therefore the descalability of a subsequent pickling step can be low.
  • the coiling temperature is preferably 700°C or less.
  • Cold rolling is performed at a reduction rate of 60% to 95%.
  • the reduction rate is less than 60%, the cold-rolled steel sheet heat-treated (subjected to recovery annealing) cannot reach target strength. Furthermore, the cold-rolled steel sheet has defects probably caused by the non-uniformity, especially by the thickness-wise non-uniformity of the cold-rolled steel sheet.
  • the reduction rate exceeds 95%, it is difficult to avoid the deterioration of local ductility.
  • the reduction rate is preferably 80% or more.
  • Heat treatment is performed in a temperature range of (recrystallization starting temperature - 200°C) or more and (recrystallization starting temperature - 20°C) or less.
  • the recrystallization temperature of steel is variable due to the use of, for example, Nb and/or B, the temperature range (soaking temperature range) of the steel is set to be 20°C to 200°C lower than the recrystallization starting temperature thereof.
  • an object of annealing is to reduce the increased strength of the cold-rolled steel sheet strained by cold rolling to a target value by strain relief annealing.
  • the annealing temperature is below a temperature 200°C lower than the recrystallization starting temperature, the strain of the cold-rolled steel sheet is not sufficiently relieved and the annealed steel sheet has a strength greater than a target value and a ductility smaller than a target value.
  • the lower limit of the annealing temperature is a temperature 200°C lower than the recrystallization starting temperature.
  • the lower limit of the annealing temperature is preferably a temperature 150°C lower than the recrystallization starting temperature.
  • the upper limit of the annealing temperature is a temperature 20°C lower than the recrystallization starting temperature. Recrystallized grains and as-recovered grains can be identified from each other by optical or electronic microscopy. In view of strength, the upper limit thereof is a temperature 30°C lower than the recrystallization starting temperature.
  • the recrystallization starting temperature of the steel sheet, cold-rolled under the above conditions, having the above composition is within a range from about 560°C to 650°C (in the case of the absence of both Nb and B) or a range from about 620°C to 780°C (in the case of the presence of at least one of Nb and B).
  • annealing is preferably performed using a continuous annealing furnace.
  • the soaking time during annealing is preferably 10s or more and 90s or less.
  • the thin steel sheets were annealed (recovery-annealed) at 350°C to 620°C for 30 s in a continuous annealing furnace, temper-rolled so as to have an elongation rate of 1.5% or less, and then continuously plated (electroplated) with chromium by an ordinary technique, whereby plated steel sheets (tin-free steel sheets) were obtained.
  • Detailed manufacturing conditions are summarized in Table 2.
  • the plated steel sheets manufactured as described above were subjected to a tensile test and r-value measurement.
  • tensile test tensile test specimens (rolling direction) of JIS No. 5 size were used to measure tensile strength and elongation (total elongation) and then evaluated for strength and ductility.
  • the average r-value of each specimen was determined by the natural frequency method specified in JIS Z2254.
  • Table 3 shows that examples (Steel Sheets 1, 2, and so on) of the present invention have a tensile strength of 550 to 600 MPa and a total elongation of 5% or more.
  • a comparative example (Steel Sheet 3) have low ductility because the annealing temperature thereof is lower than the temperature range specified herein and therefore the strain stored therein is only slightly relieved.
  • the annealing temperature of a comparative example (Steel Sheet 4) is higher than the temperature range specified herein and therefore the strength thereof is insufficient because of local recrystallization.
  • the steel sheets annealed at a temperature 20°C to 200°C lower than the recrystallization starting temperature thereof have a TS of 550 to 650 MPa.
  • the steel sheets annealed at a temperature 40°C or more lower than the recrystallization starting temperature thereof have a TS of 600 to 650 MPa.
  • annealing is preferably performed at a temperature about 20°C to 50°C (preferably 20°C to 40°C) lower than the recrystallization starting temperature thereof.
  • Steels containing components shown in Table 4 were produced with an existing converter, the remainder being unavoidable impurities and Fe. Slabs of the steels were then manufactured. The steel slabs were reheated at 1150°C to 1250°C and then hot-rolled. During hot rolling, the finishing temperature of the steel slabs was varied within a range from 880°C to 900°C and the coiling temperature thereof was 620°C. The obtained hot-rolled steel sheets were pickled and then cold-rolled at a reduction rate of 80% to 90%, whereby thin steel sheets with a thickness of 0.15 to 0.18 mm were manufactured.
  • Fig. 2 shows the results obtained by investigating the recrystallization behavior of Steel 5 (manufactured under substantially the same conditions as those for manufacturing Steel Sheet 13 shown in Table 5 except the annealing temperature thereof) shown in Table 4.
  • the plated steel sheets (tin-free steel sheets) manufactured as described above were subjected to a tensile test and r-value measurement. Properties of the plated steel sheets were measured in the same manner as that described in Example 1. The obtained results are summarized in Table 6.
  • Table 6 shows that examples (Steel Sheets 5, 7, 9, 10, 12, 13, and so on) have a tensile strength of 550 to 700 MPa and a total elongation of 4% or more.
  • comparative examples have high strength and low ductility because the annealing temperature thereof is lower than the temperature range specified herein and therefore the strain stored therein is only slightly relieved.
  • the annealing temperature of a comparative example is higher than the temperature range specified herein and therefore the strength thereof is insufficient because of local recrystallization.
  • the steel sheets annealed at a temperature 20°C to 200°C lower than the recrystallization staring temperature thereof have a TS of 550 to 700 MPa.
  • the steel sheets annealed at a temperature 40°C or more lower than the recrystallization staring temperature have a TS of 650 to 700 MPa.
  • annealing is preferably performed at a temperature 20°C to 50°C (preferably 20°C to 40°C) lower than the recrystallization staring temperature thereof.
  • Comparative examples have high strength and low ductility because the content of a component therein exceeds the range specified herein.
  • the annealing temperature of a steel sheet according to the present invention can be varied because the recrystallization behavior thereof varies depending on the content of Nb or B.
  • the strength therefore can be also varied by controlling the Nb or B content. Therefore, a process according to the present invention is extremely efficient in manufacturing a tin mill black plate with an existing plant because a steel sheet for manufacturing the tin mill black plate can be annealed in the same cycle as that of other tin mill black plates so as to have a desired strength.
  • a tin mill black plate having a tensile strength of 550 to 650 MPa and a total elongation of 5% or more can be obtained.
  • the tin mill black plate contains Nb and/or B
  • the tin mill black plate can be manufactured even by a process including no DR step or recrystallization annealing step so as to have a tensile strength of 550 to 700 MPa and a total elongation of 4% or more.
  • a high-strength tin mill black plate which is used to manufacture cans and therefore need not have low in-plate plastic anisotropy can be manufactured at low cost by a process according to the present invention without impairing the corrosion resistance thereof.
  • the process according to the present invention includes annealing performed at a lower temperature as compared to a process for manufacturing an ordinary tin mill black plate and therefore is effective in reducing energy cost.
  • the addition of Nb and/or B allows annealing to be performed at the same temperature as that at which ordinary tin mill black plates are annealed. In this case, no separate annealing chances are necessary. Therefore, a steel sheet having a TS of 550 to 700 MPa can be manufactured without a reduction in productivity.
  • annealing can be performed within a temperature range where a change in strength is small; hence, a steel sheet that is uniform in the width direction thereof can be obtained even if the annealing temperature thereof is varied.
  • a tin mill black plate manufactured by the process according to the present invention is suitable for cans, especially two-piece DRD cans and three-piece welded cans used as containers for canned beverages or canned foods.

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 Sheet Steel (AREA)
EP08711889.9A 2007-02-21 2008-02-19 Verfahren zur herstellung von stahlblechen für becher Active EP2123780B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2007041065A JP5076544B2 (ja) 2007-02-21 2007-02-21 缶用鋼板の製造方法
PCT/JP2008/053125 WO2008102899A1 (ja) 2007-02-21 2008-02-19 缶用鋼板の製造方法

Publications (3)

Publication Number Publication Date
EP2123780A1 true EP2123780A1 (de) 2009-11-25
EP2123780A4 EP2123780A4 (de) 2010-10-27
EP2123780B1 EP2123780B1 (de) 2015-12-02

Family

ID=39710169

Family Applications (1)

Application Number Title Priority Date Filing Date
EP08711889.9A Active EP2123780B1 (de) 2007-02-21 2008-02-19 Verfahren zur herstellung von stahlblechen für becher

Country Status (5)

Country Link
EP (1) EP2123780B1 (de)
JP (1) JP5076544B2 (de)
KR (1) KR101128315B1 (de)
CN (1) CN101578381B (de)
WO (1) WO2008102899A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2123780B1 (de) 2007-02-21 2015-12-02 JFE Steel Corporation Verfahren zur herstellung von stahlblechen für becher

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5655300B2 (ja) * 2009-03-05 2015-01-21 Ｊｆｅスチール株式会社 曲げ加工性に優れた冷延鋼板、その製造方法およびそれを用いた部材
JP5811686B2 (ja) * 2010-10-18 2015-11-11 Ｊｆｅスチール株式会社 高強度缶用鋼板およびその製造方法
JP5903884B2 (ja) * 2011-12-27 2016-04-13 Ｊｆｅスチール株式会社 耐腰折れ性に優れた高強度薄鋼板の製造方法
WO2013144320A1 (en) * 2012-03-30 2013-10-03 Tata Steel Ijmuiden Bv A process for manufacturing a recovery annealed coated steel substrate for packaging applications and a packaging steel product produced thereby
DE102013003516A1 (de) * 2013-03-04 2014-09-04 Outokumpu Nirosta Gmbh Verfahren zur Herstellung eines ultrahochfesten Werkstoffs mit hoher Dehnung
KR101871735B1 (ko) * 2014-02-25 2018-06-27 제이에프이 스틸 가부시키가이샤 크라운 캡용 강판 및 그의 제조 방법 및 크라운 캡
EP3150734B1 (de) 2014-05-30 2019-12-11 JFE Steel Corporation Stahlblech und dosen und herstellungsverfahren dafür
MY196420A (en) * 2019-03-29 2023-03-30 Jfe Steel Corp Steel Sheet for Cans and Method for Manufacturing the same

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0556834A2 (de) * 1992-02-21 1993-08-25 Kawasaki Steel Corporation Verfahren zum Herstellen hochfester Stahlbleche für Dosen
JPH10330882A (ja) * 1997-04-04 1998-12-15 Nippon Steel Corp 成形性に優れた冷延鋼板およびその製造方法
WO2003031670A1 (en) * 2001-10-04 2003-04-17 Nippon Steel Corporation Steel sheet for container and method of producing the same
JP2007009271A (ja) * 2005-06-30 2007-01-18 Jfe Steel Kk 異方性の小さい鋼板およびその製造方法
WO2008075444A1 (ja) * 2006-12-20 2008-06-26 Jfe Steel Corporation 冷延鋼板およびその製造方法

Family Cites Families (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3264144A (en) 1962-09-13 1966-08-02 Youngstown Sheet And Tube Co Method of producing a rolled steel product
JPS5320445B2 (de) 1972-03-09 1978-06-27
US3950190A (en) 1974-11-18 1976-04-13 Youngstown Sheet And Tube Company Recovery-annealed cold-reduced plain carbon steels and methods of producing
US3963531A (en) 1975-02-28 1976-06-15 Armco Steel Corporation Cold rolled, ductile, high strength steel strip and sheet and method therefor
JPS62161938A (ja) * 1986-01-09 1987-07-17 Kawasaki Steel Corp 化成処理性、加工性の良好な冷延鋼板とその製造方法
JPH02118024A (ja) * 1988-10-28 1990-05-02 Kawasaki Steel Corp 缶用鋼板の製造方法
JPH02118026A (ja) * 1988-10-28 1990-05-02 Kawasaki Steel Corp 缶用鋼板の製造方法
JPH03294432A (ja) * 1990-04-13 1991-12-25 Nippon Steel Corp 板取り性が優れた溶接缶用極薄鋼板の製造法
JPH06248332A (ja) 1993-02-26 1994-09-06 Nippon Steel Corp 容器用鋼板の製造方法
JPH06248339A (ja) 1993-02-26 1994-09-06 Nippon Steel Corp 高剛性容器用鋼板の製造方法
JPH06248338A (ja) 1993-02-26 1994-09-06 Nippon Steel Corp 容器用原板の製造方法
JP3596037B2 (ja) * 1994-08-01 2004-12-02 Ｊｆｅスチール株式会社 製缶用鋼板の製造方法
JPH08127816A (ja) 1994-10-28 1996-05-21 Nippon Steel Corp 耐しわ性にすぐれた容器用原板の製造方法
JPH08246060A (ja) * 1995-03-10 1996-09-24 Kawasaki Steel Corp 缶用鋼板の製造方法
JPH08264060A (ja) * 1995-03-23 1996-10-11 Ngk Insulators Ltd ポリマー碍子の接合方法
JPH08269568A (ja) 1995-03-30 1996-10-15 Kawasaki Steel Corp フランジ成形性に優れた製缶用鋼板の製造方法
JP4244486B2 (ja) 1999-08-05 2009-03-25 Ｊｆｅスチール株式会社 高強度缶用鋼板およびその製造方法
JP4283574B2 (ja) * 2003-03-24 2009-06-24 新日本製鐵株式会社 製缶性に優れた高時効硬化容器用鋼板及びその製造方法
JP4525450B2 (ja) 2004-04-27 2010-08-18 Ｊｆｅスチール株式会社 高強度高延性な缶用鋼板およびその製造方法
JP5076544B2 (ja) 2007-02-21 2012-11-21 Ｊｆｅスチール株式会社 缶用鋼板の製造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0556834A2 (de) * 1992-02-21 1993-08-25 Kawasaki Steel Corporation Verfahren zum Herstellen hochfester Stahlbleche für Dosen
JPH10330882A (ja) * 1997-04-04 1998-12-15 Nippon Steel Corp 成形性に優れた冷延鋼板およびその製造方法
WO2003031670A1 (en) * 2001-10-04 2003-04-17 Nippon Steel Corporation Steel sheet for container and method of producing the same
JP2007009271A (ja) * 2005-06-30 2007-01-18 Jfe Steel Kk 異方性の小さい鋼板およびその製造方法
WO2008075444A1 (ja) * 2006-12-20 2008-06-26 Jfe Steel Corporation 冷延鋼板およびその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of WO2008102899A1 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2123780B1 (de) 2007-02-21 2015-12-02 JFE Steel Corporation Verfahren zur herstellung von stahlblechen für becher

Also Published As

Publication number Publication date
EP2123780A4 (de) 2010-10-27
CN101578381A (zh) 2009-11-11
KR20090084885A (ko) 2009-08-05
JP5076544B2 (ja) 2012-11-21
CN101578381B (zh) 2013-06-19
JP2008202113A (ja) 2008-09-04
KR101128315B1 (ko) 2012-04-12
EP2123780B1 (de) 2015-12-02
WO2008102899A1 (ja) 2008-08-28

Similar Documents

Publication Publication Date Title
EP2128289B1 (de) Stahlblech für dosen, heissgewalztes stahlblech zur verwendung als basismetall und herstellungsverfahren für beide
EP2123780B1 (de) Verfahren zur herstellung von stahlblechen für becher
JP5135868B2 (ja) 缶用鋼板およびその製造方法
EP3859041A1 (de) Hochfestes kaltgewalztes stahlblech mit hohem lochausdehnungsverhältnis, hochfestes feuerverzinktes stahlblech und herstellungsverfahren dafür
EP2615191B1 (de) Hochfestes kaltgewalztes stahlblech mit ausgezeichneten dehnungs- und bördelungseigenschaften sowie herstellungsverfahren dafür
EP2792763B1 (de) Stahlblech mit hervorragenden alterungseigenschaften und herstellungsverfahren dafür
US9879332B2 (en) Method of manufacturing high-strength steel sheet for a can
JP2005126733A (ja) 高温加工性にすぐれた熱間プレス用鋼板及び自動車用部材
EP4159886A1 (de) Ultrahochfester zweiphasiger stahl und herstellungsverfahren dafür
JP2009263789A (ja) 高強度容器用鋼板およびその製造方法
JP5272714B2 (ja) 製缶用鋼板の製造方法
US20070289679A1 (en) High Strength Cold Rolled Steel Sheet Having Excellent Shape Freezability, and Method for Manufacturing the Same
JP4244486B2 (ja) 高強度缶用鋼板およびその製造方法
EP2868764B1 (de) Stahlblech für weiche nitrierung und verfahren zur herstellung davon
EP2907887B1 (de) Kaltgewalztes stahlblech mit überlegener formfestigkeit und herstellungsverfahren dafür
CN109440004B (zh) 罐用钢板及其制造方法
EP1975268A1 (de) Kaltgewalztes stahlblech und herstellungsverfahren dafür
JP2007239035A (ja) 耐ひずみ時効性および耐肌荒れ性に優れ、面内異方性の小さい冷延鋼板およびその製造方法
EP4431630A1 (de) Ultrahochfestes stahlblech mit hervorragender biegbarkeit und streckbarkeit sowie herstellungsverfahren dafür
EP4108796A1 (de) Stahlblech für dose und verfahren zur herstellung davon
KR20190022127A (ko) 저온 충격인성이 개선된 페라이트계 스테인리스강 및 이의 제조 방법
CN115176042A (zh) 钢板和钢板的制造方法

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: 20090624

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK TR

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20100928

17Q First examination report despatched

Effective date: 20130426

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 602008041383

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C21D0009460000

Ipc: C22C0038040000

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 9/46 20060101ALI20150609BHEP

Ipc: C22C 38/06 20060101ALI20150609BHEP

Ipc: C21D 8/02 20060101ALI20150609BHEP

Ipc: C22C 38/04 20060101AFI20150609BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20150723

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): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MT NL NO PL PT RO SE SI SK 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: AT

Ref legal event code: REF

Ref document number: 763673

Country of ref document: AT

Kind code of ref document: T

Effective date: 20151215

Ref country code: CH

Ref legal event code: EP

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: 602008041383

Country of ref document: DE

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 9

REG Reference to a national code

Ref country code: NL

Ref legal event code: FP

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 763673

Country of ref document: AT

Kind code of ref document: T

Effective date: 20151202

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

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: 20151202

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: 20160302

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: 20151202

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: 20151202

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: 20151202

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: 20151202

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: 20151202

Ref country code: BE

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

Effective date: 20160229

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: 20151202

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: 20160303

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: 20151202

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

Ref country code: IS

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

Effective date: 20151202

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

Ref country code: CZ

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

Effective date: 20151202

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: 20151202

REG Reference to a national code

Ref country code: DE

Ref legal event code: R026

Ref document number: 602008041383

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: 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: 20151202

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: 20160402

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: 20151202

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: 20151202

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: 20160404

26 Opposition filed

Opponent name: TATA STEEL IJMUIDEN BV

Effective date: 20160822

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: 20151202

Ref country code: LU

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: 20160219

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PLAX Notice of opposition and request to file observation + time limit sent

Free format text: ORIGINAL CODE: EPIDOSNOBS2

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: 20160229

Ref country code: CH

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

Effective date: 20160229

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: 20151202

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: 20151202

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: BE

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: 20151202

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 10

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

Ref country code: IE

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

Effective date: 20160219

PLBB Reply of patent proprietor to notice(s) of opposition received

Free format text: ORIGINAL CODE: EPIDOSNOBS3

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

Ref country code: MT

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

Effective date: 20151202

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 11

REG Reference to a national code

Ref country code: DE

Ref legal event code: R100

Ref document number: 602008041383

Country of ref document: DE

PLCK Communication despatched that opposition was rejected

Free format text: ORIGINAL CODE: EPIDOSNREJ1

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: 20151202

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: 20080219

PLBN Opposition rejected

Free format text: ORIGINAL CODE: 0009273

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

Free format text: STATUS: OPPOSITION REJECTED

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

Ref country code: MT

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

Effective date: 20160229

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: 20151202

27O Opposition rejected

Effective date: 20180209

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: 20151202

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

Ref country code: FR

Payment date: 20220118

Year of fee payment: 15

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

Ref country code: GB

Payment date: 20221230

Year of fee payment: 16

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

Ref country code: DE

Payment date: 20221229

Year of fee payment: 16

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

Effective date: 20230512

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

Ref country code: NL

Payment date: 20230113

Year of fee payment: 16

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: 20230228

REG Reference to a national code

Ref country code: NL

Ref legal event code: MM

Effective date: 20240301