EP2103697B1 - High carbon hot-rolled steel sheet - Google Patents

High carbon hot-rolled steel sheet Download PDF

Info

Publication number
EP2103697B1
EP2103697B1 EP07860538.3A EP07860538A EP2103697B1 EP 2103697 B1 EP2103697 B1 EP 2103697B1 EP 07860538 A EP07860538 A EP 07860538A EP 2103697 B1 EP2103697 B1 EP 2103697B1
Authority
EP
European Patent Office
Prior art keywords
less
steel sheet
hot
ferrite
aspect ratio
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
EP07860538.3A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP2103697A4 (en
EP2103697A1 (en
Inventor
Nobusuke Kariya
Kazuhiro Seto
Nobuyuki Nakamura
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 EP2103697A1 publication Critical patent/EP2103697A1/en
Publication of EP2103697A4 publication Critical patent/EP2103697A4/en
Application granted granted Critical
Publication of EP2103697B1 publication Critical patent/EP2103697B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0221—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
    • 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
    • C22C38/001—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a high-carbon hot-rolled steel sheet, particularly a high-carbon hot-rolled steel sheet having excellent bending properties after processing, and a method of producing the same.
  • Non-Patent Document 1 a double-acting forming technique which permits thickness-additive forming process and realizes a significant reduction in the process is disclosed as a processing technique for automobile driving-system parts using high-carbon steel sheets and partially put into practical application.
  • high-carbon steel sheets are required to be processable without a problem even when a plurality of processing types such as stretching, drawing, bulging, bending, and hole-expansion (burring) are combined.
  • processing types such as stretching, drawing, bulging, bending, and hole-expansion (burring) are combined.
  • a crack frequently occurs in a bent portion, and thus excellent bending properties after stretching are required.
  • Patent Document 1 proposes a method in which high-carbon steel having predetermined chemical components is hot-rolled, descaled, annealed in an atmosphere containing 95% by volume or more of hydrogen at a heating rate for a soaking time which are specified according to the chemical components, and then cooled at a cooling rate of 100 °C/hr or less to produce a high-carbon workable steel strip having a uniform microstructure and excellent workability.
  • Patent Document 2 proposes a method in which a steel sheet rolled at a finishing temperature of (Ac 1 transformation point + 30°C) or more is cooled to a temperature of 20 to 500°C at a cooling rate of 10 to 100 °C/sec, maintained for 1 to 10 seconds, reheated in a temperature range of 500°C to (Ac 1 transformation point + 30°C), and then coiled, and, if required, soaked at 650°C to (Ac 1 transformation point + 30°C) for 1 hour or more to produce a high-carbon thin steel sheet having good workability.
  • Patent Document 3 proposes a method in which steel containing 0.2 to 0.7% by mass of C is hot-rolled at a finishing temperature of (Ar 3 transformation point - 20°C) or more, cooled at a cooling rate of over 120 °C/sec and a cooling stop temperature of 650°C or less, coiled at a coiling temperature of 600°C or less, and then annealed at an annealing temperature of 640°C to Ac 1 transformation point to produce a high-carbon hot-rolled steel sheet having excellent stretch-flangeformability.
  • Non-patent Document 1 Journal of the JSTP, 44, 2003, p. 409-413
  • the high-carbon hot-rolled steel sheets described in these conventional techniques have excellent properties when processed by a single processing type such as stretching or hole-expansion, but has the problem of producing cracks when bending is performed after stretching, i.e., when a plurality of processing types are combined.
  • the present invention provides a high-carbon hot-rolled steel sheet having excellent bending properties after stretching and a method of producing the same.
  • the present invention has been achieved on the basis of the above-mentioned findings and provides a high-carbon hot-rolled steel sheet which is a hot-rolled spheroidizing annealed material, the steel sheet having a composition consisting of, in % by mass, 0.2 to 0.7% of C, 2% or less of Si, 2% or less of Mn, 0.03% or less of P, 0.03% or less of S, 0.01% or less of Sol.
  • N Al, and 0.01% or less of N, optionally at least one selected from B, Cr, Ni, Mo, Cu, Ti, Nb, W, V, and Zr in the following content ranges in % by mass: B: 0.005% or less, Cr: 3.5% or less, Ni: 3.5% or less, Mo: 0.7% or less, Cu: 0.1% or less, Ti: 0.1% or less, Nb: 0.1% or less, W, V, Zr: 0.1% or less in total, the balance being Fe and inevitable impurities, a ferrite grain diameter being 5.0 ⁇ m or less, and an area ratio of ferrite grains with an aspect ratio of 4.0 or more being 15% or less.
  • the ferrite grain diameter is an average grain diameter determined by approximating ferrite grains as circular grains in image analysis
  • the aspect ratio is an average value of (major axis of ellipse)/(minor axis of ellipse) determined by approximating ferrite grains as elliptic grains in image analysis.
  • a section of the steel sheet in a direction parallel to the rolling direction is polished and etched a nital solution (nitric acid + ethanol) at a position of 1/4 thickness of the sheet, and then a microstructure is observed with a scanning electron microscope at a magnification of 1500 ⁇ to determine a ferrite grain diameter and the aspect ratio of a ferrite grain by image analysis using an image analysis software "Image Pro Plus ver.
  • the area ratio of ferrite grains with an aspect ratio of 4.0 or more is determined and then divided by the total area of the field of view to determine the area ratio of each field of view.
  • the average of 50 fields of view is regarded as the area ratio of ferrite grains with an aspect ratio of 4.0 or more.
  • the area ratio of the ferrite grains with an aspect ratio of 4.0 or more is preferably 10% or less.
  • a high-carbon hot-rolled steel sheet exhibiting excellent bending properties even after processing such as stretching can be produced.
  • Fig. 1 is a graph showing a relation between the area ratio of ferrite grains with an aspect ratio of 4.0 or more and bending properties after stretching.
  • C is an important element which forms a carbide and provides hardness after quenching.
  • the C content is less than 0.2%, sufficient strength as machine structural parts cannot be obtained after quenching.
  • the C content exceeds 0.7%, a sufficient bending property after stretching cannot be obtained even when the ferrite grain diameter is 5.0 ⁇ m or less and the area ratio of ferrite grains with an aspect ratio is 15% or less.
  • the hardness after hot rolling is significantly increased, and the steel sheet becomes brittle to cause disadvantage in handling and saturate strength as machine structural parts after quenching. Therefore, the C content is specified to 0.2 to 0.7%.
  • the C content preferably exceeds 0.5%, while when workability is regarded as important, the C content is preferably 0.5% or less.
  • Si content Si graphitizes a carbide and tends to inhibit hardenability, and thus the content is 2% or less and preferably 1% or less.
  • Mn content When Mn is excessively contained, ductility tends to be decreased. Therefore, the Mn content is specified to 2% or less and preferably 1% or less.
  • P content When P is excessively contained, ductility such as stretch-flange properties is decreased, and cracks easily occur. Therefore, the P content is 0.03% or less and preferably 0.02% or less.
  • the S content When S is excessively contained, ductility such as stretch-flangeformability is decreased, and cracks easily occur. Therefore, the S content is 0.03% or less and preferably 0.07% or less.
  • Sol. Al content is the most important element in the present invention. Namely, the inventors newly found that when the Sol. Al content exceeds 0.01%, AlN is formed on a surface layer of the steel sheet in annealing the hot-rolled steel sheet in a nitrogen atmosphere using nitrogen which is relatively inexpensive and frequently used as a non-oxidizing atmosphere, and the surface layer of the steel sheet is hardened to significantly decrease the bending properties after stretching. Therefore, the Sol. Al content is specified to 0.01% or less.
  • N content When N is excessively contained, ductility is decreased. Therefore, the N content is 0.01% or less and preferably 0.005% or less.
  • the content of each element is preferably about 0.0001% or more.
  • the balance is composed of Fe and inevitable impurities, but even when at least one element of B, Cr, Ni, Mo, Cu, Ti, Nb, W, V, and Zr may be added in a usual range in order to improve hardenability by quenching and resistance to temper softening, the advantage of the present invention is not impaired.
  • these elements can be contained at the following contents: B: 0.005% by or less, Cr: 3.5% or less, Ni: 3.5% or less, Mo: 0.7% or less, Cu: 0.1% or less, Ti: 0.1% or less, Nb: 0.1% or less, W, V, Zr: 0.1% or less in total.
  • the elements are preferably contained at the following contents: B: 0.0005% or more, Cr: 0.05% or more, Ni: 0.05% or more, Mo: 0.05% or more, Cu: 0.01% or more, Ti: 0.01% or more, Nb: 0.01% or more, W, V, Zr: 0.01% or more in total.
  • the advantage of the present invention is not affected.
  • the finishing temperature of hot rolling is (Ar 3 transformation point - 20°C) or more.
  • Ar 3 transformation point can be calculated from the equation (1) below, an actually measured temperature may be used.
  • Ar 3 transformation point 910 ⁇ 203 ⁇ C 1 / 2 + 44.7 ⁇ Si ⁇ 30 ⁇ Mn wherein [M] represents the content (%) of element M.
  • correction terms may be introduced according the elements contained. For example, when Cr, Mo, and Ni are contained, the correction terms, such as - 11 ⁇ [Cr], + 31.5 ⁇ [Mo], and - 15.2 ⁇ [Ni], may be added to the right side of the equation (1).
  • Cooling condition after hot rolling In the present invention, grain refining of ferrite grains is achieved in spite of the low Sol. Al content and difficulty in inhibiting grain growth by AlN pinning. This is estimated to be due to the fact that strain applied to austenite grains during rolling is easily accumulated by rapid cooling after hot rolling, and the accumulated strain contributes as nucleation sites of ferrite grains during subsequent annealing. When the cooling rate after hot rolling is less than 60 °C/sec, the strain applied to the austenite grains during rolling is little accumulated, and thus the number of the nucleation sites of ferrite grains is decreased in subsequent annealing, thereby accelerate the growth of ferrite grains.
  • the ferrite grain diameter exceeds 5.0 ⁇ m, and the bending properties after stretching are degraded.
  • the cooling rate is 120 °C/sec or more
  • the ferrite grain diameter after annealing is 5.0 ⁇ m or less, but the area ratio of ferrite grains with an aspect ratio of 4.0 or more exceeds 15%. Therefore, as described above, the bending properties after stretching are degraded. This is estimated to be due to the fact that when the cooling rate is 120 °C/sec or more, the strain applied to the austenite grains during rolling is excessively present after rolling, thereby causing difficulty in growth of equiaxial ferrite grains in subsequent annealing. Therefore, the cooling rate after hot rolling is 60 °C/sec to less than 120 °C/sec.
  • the upper limit of the cooling rate is preferably 115 °C/sec.
  • the cooling stop temperature When the end-point of cooling of the hot-rolled steel sheet at the above-described cooling rate, i.e., the cooling stop temperature, is higher than 650°C, the strain accumulated in austenite in cooling is released until the hot-rolled steel sheet is coiled. As a result, the ferrite grain diameter after annealing exceeds 5.0 ⁇ m, and thus the bending properties after stretching are degraded. Therefore, the cooling stop temperature is 650°C or less and preferably 600°C or less. In view of the problem with measurement accuracy of the temperature, the cooling stop temperature is preferably 500°C or more.
  • Cooling after the cooling stop temperature is attained is not particularly specified, and natural cooling or accelerated cooling with deceased cooling force may be continued. From the viewpoint of homogeneous mechanical properties of the steel sheet, accelerated cooling is preferably performed to an extent which suppresses regeneration of heat.
  • Coiling temperature The hot-rolled steel sheet after cooling is coiled.
  • the coiling temperature exceeds 600°C, the strain accumulated in austenite during hot rolling is released.
  • the ferrite grain diameter after annealing exceeds 5.0 ⁇ m, and thus the bending properties after stretching are degraded. Therefore, the coiling temperature is 600°C or less.
  • the coiling stop is preferably lower than the cooling termination temperature. Since the shape of the hot-rolled steel sheet is degraded, the coiling temperature is preferably 200°C or more and more preferably 350°C or more.
  • the cooling rate is 80 °C/sec to less than 120 °C/sec
  • the cooling stop temperature is 600°C or less
  • the coiling temperature is 550°C or less.
  • the hot-rolled steel sheet after coiling is generally descaled before subsequent annealing.
  • the descaling means is not particularly limited, but pickling by a usual method is preferred.
  • Annealing temperature of hot-rolled steel sheet After descaling by pickling, the hot-rolled steel sheet is annealed by spheroidizing annealing for spheroidizing carbides.
  • the annealing temperature is less than 640°C, growth of ferrite grains is insufficient, and thus the area ratio of ferrite grains with an aspect ratio of 4.0 or more exceeds 15%, thereby deteriorating the bending properties after stretching.
  • the annealing temperature exceeds the Ac 1 transformation point, austenite formation partially proceeds to form pearlite during cooling, thereby deteriorating the bending properties after stretching. Therefore, the annealing temperature of the hot-rolled steel sheet is 640°C to the Ac 1 transformation point.
  • the annealing temperature of the hot-rolled steel sheet is preferably 680°C or above.
  • the Ac 1 transformation point can be calculated from the equation (2) below, an actually measured temperature may be used.
  • Ac 1 transformation point 754.83 ⁇ 32.85 ⁇ C + 23.32 ⁇ Si ⁇ 17.76 ⁇ Mn wherein [M] represents the content (%) of element M.
  • correction terms may be introduced according the elements contained. For example, when Cr, Mo, and V are contained, the correction terms, such as + 17.3 ⁇ [Cr], + 4.51 ⁇ [Mo], and + 15.62 ⁇ [V], may be added to the right side of the equation (2).
  • the annealing time of the hot-rolled steel sheet is preferably about 8 to 80 hours.
  • the carbide in the resultant steel sheet is spheroidized, and the average aspect ratio is about 5.0 or less (a value measured at a position of about 1/4 thickness of the sheet).
  • a converter or an electric furnace can be applied for steel making of the high-carbon steel according to the present invention.
  • high-carbon steel is formed into a slab by ingoting and blooming or continuous casting.
  • the slab is generally heated, (reheated), and then treated by hot-rolled.
  • the slab manufactured by continuous casting may be treated by hot direct rolling directly from the slab or after heat-holding to prevent temperature reduction.
  • the slab heating temperature is preferably specified to 1280°C or below to avoid the deterioration of surface condition caused by scale.
  • the hot-rolling can be given only by finishing rolling eliminating rough rolling.
  • the material being rolled may be heated during hot-rolling using a heating means such as sheet bar heater.
  • a heating means such as sheet bar heater.
  • the coiled sheet may be thermally insulated by a slow-cooling cover or other means.
  • the thickness of the hot-rolled sheet is not specifically limited if only the manufacturing conditions of the present invention are maintained, a particularly preferable range of the thickness thereof is from 1.0 to 10.0 mm from the point of operability.
  • the annealing of hot-rolled sheet can be done either by box annealing or by continuous annealing. After annealing or hot-rolled sheet, skin-pass rolling is applied, at need. Since the skin-pass rolling does not affect the hardenability by quenching, there is no specific limitation or the condition of skin-pass rolling.
  • the hot-rolled steel sheet produced by the above-described method of the present invention is a hot-rolled steel sheet subjected to hot-rolling spheroidizing annealing and containing carbides spheroidized to an average aspect ratio of about 5.0 or less.
  • the hot-rolled steel sheet of the present invention has a ferrite grain diameter of 5.0 ⁇ m or less.
  • the ferrite grain diameter affects the bending properties after stretching.
  • the ferrite grain diameter exceeds 5.0 ⁇ m, many fine carbide grains are precipitated in ferrite grains, and voids produced by stretching at interfaces between carbides and ferrite are connected together during bending to cause cracks.
  • the ferrite grain diameter is 5.0 ⁇ m or less, the number of carbide in ferrite grains is decreased, and the fine voids produced by stretching are little connected by bending after stretching, thereby suppressing the occurrence of cracks.
  • the area ratio of ferrite grains with an aspect ratio of 4.0 or more is 15% or less.
  • the shape of ferrite grains affects the bending properties after stretching.
  • the aspect ratio of the ferrite grains is 4.0 or more, fine cracks easily occur by stretching at grain boundaries between ferrite grains with an aspect ratio of 4.0 or more and equiaxial ferrite grains with an aspect ratio less than 4.0.
  • the area ratio of such ferrite grains with an aspect ratio of 4.0 or more exceeds 15%, cracking starts in bending at fine cracks produced in stretching.
  • the area ratio of ferrite grains with an aspect ratio of 4.0 or more is 15% or less, the occurrence of cracks in bending after stretching can be suppressed.
  • the area ratio of ferrite grains with an aspect ratio of 4.0 or more is more preferably 10% or less.
  • Steel sheets Nos. 1 to 10 are examples of the present invention, and steel sheet Nos. 11 to 20 are comparative examples.
  • the ferrite grain diameter and the aspect ratio and area ratio of ferrite grains were measured by the following methods.
  • the bending properties after stretching were also measured by the following method.
  • the ferrite grain diameter is an average grain diameter determined by approximating ferrite grains as circular grains in image analysis
  • the aspect ratio is an average value of (major axis of ellipse)/(minor axis of ellipse) determined by approximating ferrite grains as elliptic grains in image analysis.
  • a thickness section of the steel sheet in a direction parallel to the rolling direction was polished and etched a nital solution (nitric acid + ethanol) at a position of 1/4 thickness of the sheet, and then a microstructure was observed with a scanning electron microscope at a magnification of 1500 ⁇ to determine a ferrite grain diameter and the aspect ratio of a ferrite grain by image analysis using an image analysis software "Image Pro Plus ver. 4.0" (TM) manufactured by Media Cybernetics Co., Ltd.
  • the area ratio of ferrite grains with an aspect ratio of 4.0 or more was determined and then divided by the total area of a field of view to determine the area ratio of each field of view.
  • the average of 50 fields of view was regarded as the area ratio of ferrite grains with an aspect ratio of 4.0 or more.
  • a thickness section of the steel sheet in a direction parallel to the rolling direction was polished and etched a picral solution (picric acid + ethanol) at a position of 1/4 thickness of the sheet, and then a microstructure was observed with a scanning electron microscope at a magnification of 3000 ⁇ to determine the aspect ratio (maximum diameter)/(minimum diameter) of carbide using the image analysis software.
  • the aspect ratios of carbides were averaged (number average) to determine the average aspect ratio. As a result, it was confirmed that the carbides were spheroidized and annealed.
  • Bending properties after stretching A tensile test was performed by a method according to JIS Z 2241 using a JIS No. 5 test piece obtained in a direction perpendicular to the rolling direction and having a parallel portion of 30 mm in width to apply predistortion of 15%, and then a bending test was performed by a pressing bend method according to JIS Z 2249. The bending test was performed three times using a punch diameter D of 1 mm. When no crack occurred in the three tests, the bending property was decided as ⁇ , when cracks occurred one time or two times, the bending property was decided as ⁇ , and when cracks occurred three times, the bending property was decided as ⁇ . In the case of ⁇ , the test piece was considered as an example of the present invention.
  • the ferrite grain diameter is 5.0 ⁇ m or less
  • the area ratio of ferrite grains with an aspect ratio of 4.0 or more is 15% or less, and thus the bending property after stretching is excellent.
  • the average aspect ratio of carbides is 5.0 or less, and the carbides are spheroidized by spheroidizing annealing.
  • Fig. 1 shows a relation between the area ratio of ferrite grains with an aspect ratio of 4.0 or more and bending property after stretching when the ferrite grain diameter is 5.0 ⁇ m or less.
  • steel sheet Nos. 1 to 10 as the examples of the present invention, when the ferrite grain diameter is 5.0 ⁇ m or less, and the area ratio of ferrite grains with an aspect ratio of 4.0 or more is 15% or less, the excellent bending property after stretching can be obtained.
  • Table 1 (% by mass) Steel C Si Mn P S Sol.
  • Example 12 A 751 100 610 570 700°C ⁇ 40hr Comp.
  • Example 13 B 798 110 620 560 600°C ⁇ 40hr Comp.
  • Example 14 B 793 90 600 630 690°C ⁇ 40hr Comp.
  • Example 15 C 816 150 580 520 720°C ⁇ 40hr Comp.
  • Example 16 C 806 55 630 550 710°C ⁇ 40hr Comp.
  • Example 17 D 794 115 670 590 720°C ⁇ 40hr Comp.
  • Example 18 D 719 95 610 580 680°C ⁇ 40hr Comp.
  • Example 19 E 752 130 590 550 710°C ⁇ 40hr Comp.
  • Example 20 Z 805 100 580 530 720°C ⁇ 40hr Comp.
  • a slab was formed by continuous casting of each of steel E shown in Table 1 and the following steels:
  • the Ar 3 transformation point and the Ac 1 transformation point of each of steels F to I were determined from the equations (1) and (2), and the Ar 3 transformation point and the Ac 1 transformation point of each of steels G and I containing Cr or Mo were determined using the above-described correction terms.
  • Table 5 indicates that in steel sheet Nos. 21 to 27 produced under the constant conditions except the cooling rate, steel sheet Nos. 22 to 26 produced at the cooling rates within the range of the present invention have excellent bending property after stretching. It is also found that in steel sheet Nos. 23 to 26, the area ratio of ferrite grains with an aspect ratio of 4.0 or more can be controlled to 10% or less. It is further found that in steel sheet Nos. 28 to 33 produced at a constant cooling rate, steel sheet Nos. 30 to 33 produced at a cooling termination temperature and a coiling temperature both of which are within the ranges of the present invention have excellent bending properties after stretching. It is further found that in steel sheet No.
  • the area ratio of ferrite grains with an aspect ratio of 4.0 or more can be controlled to 10% or less.
  • the average aspect ratio of carbides is 5.0% or less, and the carbides are spheroidized by spheroidizing annealing.
  • Steels E to I each having the composition within the range of the present invention, including steels G and I containing an ally element other than the basic components, exhibit excellent bending properties after stretching.
  • Table 4 Steel sheet No. Steel Hot rolling condition Annealing of hot-rolled steel sheet Remarks Finishing temperature (°C) Cooling rate (°C/sec) Cooling termination temperature (°C) Coiling temperature (°C) 21 F 820 50 560 530 700°C ⁇ 30hr Comp.
  • Example 22 F 820 70 560 530 700°C ⁇ 30hr Example of this invention 23 F 820 85 560 530 700°C ⁇ 30hr Example of this invention 24 F 820 95 560 530 700°C ⁇ 30hr Example of this invention 25 F 820 105 560 530 700°C ⁇ 30hr Example of this invention 26 F 820 115 560 530 700°C ⁇ 30hr Example of this invention 27 F 820 140 560 530 700°C ⁇ 30hr Comp. Example 28 F 820 105 660 530 700°C ⁇ 30hr Comp. Example 29 F 820 105 630 610 700°C ⁇ 30hr Comp.
  • Example 30 F 820 105 630 560 700°C ⁇ 30hr Example of this invention 31 F 820 105 630 530 700°C ⁇ 30hr Example of this invention 32 F 820 105 580 560 700°C ⁇ 30hr Example of this invention 33 F 820 105 580 530 700°C ⁇ 30hr Example of this invention 34 E 790 105 560 530 715°C ⁇ 60hr Example of this invention 35 G 800 105 560 530 720°C ⁇ 50hr Example of this invention 36 H 810 105 560 530 700°C ⁇ 30hr Example of this invention 37 I 820 105 560 530 700°C ⁇ 30hr Example of this invention Table 5 Steel No.
  • Example 30 4.3 12.1 ⁇ Example of this invention 31 4.0 13.3 ⁇ Example of this invention 32 4.5 10.7 ⁇ Example of this invention 33 3.9 8.4 ⁇ Example of this invention 34 3.8 9.5 ⁇ Example of this invention 35 3.7 8.7 ⁇ Example of this invention 36 4.8 9.6 ⁇ Example of this invention 37 3.5 8.8 ⁇ Example of this invention

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)
  • Heat Treatment Of Steel (AREA)
EP07860538.3A 2006-12-25 2007-12-21 High carbon hot-rolled steel sheet Active EP2103697B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2006347539A JP4952236B2 (ja) 2006-12-25 2006-12-25 高炭素熱延鋼板およびその製造方法
PCT/JP2007/075341 WO2008081956A1 (ja) 2006-12-25 2007-12-21 高炭素熱延鋼板およびその製造方法

Publications (3)

Publication Number Publication Date
EP2103697A1 EP2103697A1 (en) 2009-09-23
EP2103697A4 EP2103697A4 (en) 2015-03-11
EP2103697B1 true EP2103697B1 (en) 2019-05-01

Family

ID=39588633

Family Applications (1)

Application Number Title Priority Date Filing Date
EP07860538.3A Active EP2103697B1 (en) 2006-12-25 2007-12-21 High carbon hot-rolled steel sheet

Country Status (6)

Country Link
EP (1) EP2103697B1 (ko)
JP (1) JP4952236B2 (ko)
KR (1) KR101107531B1 (ko)
CN (1) CN101568655B (ko)
TW (1) TWI333507B (ko)
WO (1) WO2008081956A1 (ko)

Families Citing this family (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101352723B (zh) * 2008-08-20 2010-12-22 秦皇岛首秦金属材料有限公司 一种中厚板柔性轧制方法
US9267194B2 (en) * 2011-04-27 2016-02-23 Nippon Steel & Sumitomo Metal Corporation Fe-based metal sheet and manufacturing method thereof
CN103084386B (zh) * 2011-10-31 2015-02-25 上海汇众汽车制造有限公司 优化热轧钢板表面质量的方法
KR101353551B1 (ko) * 2011-12-22 2014-01-23 주식회사 포스코 성형성이 우수한 고탄소 강판 및 그 제조방법
KR101505287B1 (ko) * 2013-05-30 2015-03-23 현대제철 주식회사 강재 및 그 제조 방법
CN104032214B (zh) * 2013-09-26 2015-12-09 北大方正集团有限公司 一种非调质钢及其生产工艺
CN106133169B (zh) * 2014-03-28 2018-01-05 杰富意钢铁株式会社 高碳热轧钢板及其制造方法
JP6065120B2 (ja) * 2014-03-28 2017-01-25 Ｊｆｅスチール株式会社 高炭素熱延鋼板およびその製造方法
JP6265108B2 (ja) * 2014-11-07 2018-01-24 Ｊｆｅスチール株式会社 冷延鋼板用または溶融亜鉛めっき鋼板用熱延鋼板およびその製造方法
EP3390040B2 (en) 2015-12-15 2023-08-30 Tata Steel IJmuiden B.V. High strength hot dip galvanised steel strip
CN108367539B (zh) 2015-12-15 2021-06-11 塔塔钢铁艾默伊登有限责任公司 高强度热浸镀锌钢带材
KR101770073B1 (ko) * 2016-09-20 2017-08-21 현대제철 주식회사 고강도 철근의 제조 방법
KR101889173B1 (ko) * 2016-12-13 2018-08-16 주식회사 포스코 고강도 저항복비형 미세 구상화 강판 및 그 제조방법
WO2019090109A1 (en) 2017-11-02 2019-05-09 Ak Steel Properties, Inc. Press hardened steel with tailored properties
WO2019131099A1 (ja) * 2017-12-25 2019-07-04 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
KR102209556B1 (ko) 2018-12-19 2021-01-29 주식회사 포스코 구멍확장성이 우수한 강판, 부재 및 이들의 제조방법
JP7151885B2 (ja) * 2019-05-16 2022-10-12 日本製鉄株式会社 鋼線
CN110983181B (zh) * 2019-12-16 2021-04-16 首钢集团有限公司 一种700MPa级热轧钢及其制备方法、应用
CN110983182B (zh) * 2019-12-16 2021-03-23 首钢集团有限公司 一种800MPa级热轧钢及其制备方法、应用
KR102415763B1 (ko) 2019-12-20 2022-07-04 주식회사 포스코 냉간성형성이 우수한 열연 소둔강판, 부재 및 그 제조 방법
US20230203614A1 (en) * 2020-05-28 2023-06-29 Jfe Steel Corporation Abrasion-resistant steel plate and method of producing abrasion-resistant steel plate

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62284019A (ja) * 1986-06-03 1987-12-09 Nippon Steel Corp 高炭素鋼板の製造方法

Family Cites Families (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5550427A (en) * 1978-10-03 1980-04-12 Kawasaki Steel Corp Manufacture of hot rolled medium or high carbon steel strip suitable for use in precision punching
JPH04214839A (ja) * 1990-12-14 1992-08-05 Sumitomo Metal Ind Ltd 成形性の良好な高炭素薄鋼板とその製造方法
JPH059588A (ja) 1991-02-26 1993-01-19 Sumitomo Metal Ind Ltd 成形性の良好な高炭素薄鋼板の製造方法
JPH05239588A (ja) * 1992-02-26 1993-09-17 Sumitomo Metal Ind Ltd 成形性と溶接性に優れた中炭素熱延鋼板とその製造方法
JP3242303B2 (ja) * 1995-09-29 2001-12-25 川崎製鉄株式会社 超微細粒を有する延性、靱性、疲労特性、強度延性バランスに優れた高張力熱延鋼板およびその製造方法
JP3125978B2 (ja) 1995-12-05 2001-01-22 住友金属工業株式会社 加工性に優れた高炭素鋼帯の製造方法
JPH10265845A (ja) * 1997-03-24 1998-10-06 Kawasaki Steel Corp 冷間加工性に優れた熱延合金鋼板の製造方法
JP3755368B2 (ja) * 2000-01-31 2006-03-15 Ｊｆｅスチール株式会社 伸びフランジ性に優れた高炭素鋼板
JP3879446B2 (ja) * 2001-06-28 2007-02-14 Ｊｆｅスチール株式会社 伸びフランジ性に優れた高炭素熱延鋼板の製造方法
KR100673422B1 (ko) * 2003-08-28 2007-01-24 제이에프이 스틸 가부시키가이샤 고탄소열연강판, 냉연강판 및 그 제조방법
JP4380471B2 (ja) * 2003-08-28 2009-12-09 Ｊｆｅスチール株式会社 高炭素熱延鋼板およびその製造方法
JP4380469B2 (ja) * 2003-08-28 2009-12-09 Ｊｆｅスチール株式会社 高炭素熱延鋼板およびその製造方法
JP2005094470A (ja) 2003-09-18 2005-04-07 Fuji Photo Film Co Ltd デジタルカメラ
US20050199322A1 (en) * 2004-03-10 2005-09-15 Jfe Steel Corporation High carbon hot-rolled steel sheet and method for manufacturing the same
JP4650006B2 (ja) * 2004-03-10 2011-03-16 Ｊｆｅスチール株式会社 延性および伸びフランジ性に優れた高炭素熱延鋼板およびその製造方法
JP5011846B2 (ja) * 2005-06-29 2012-08-29 Ｊｆｅスチール株式会社 高炭素熱延鋼板およびその製造方法
JP5050433B2 (ja) * 2005-10-05 2012-10-17 Ｊｆｅスチール株式会社 極軟質高炭素熱延鋼板の製造方法
CN101379208B (zh) * 2006-01-31 2012-06-20 杰富意钢铁株式会社 精冲加工性优良的钢板及其制造方法
JP5076347B2 (ja) * 2006-03-31 2012-11-21 Ｊｆｅスチール株式会社 ファインブランキング加工性に優れた鋼板およびその製造方法

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62284019A (ja) * 1986-06-03 1987-12-09 Nippon Steel Corp 高炭素鋼板の製造方法

Also Published As

Publication number Publication date
JP2008156712A (ja) 2008-07-10
JP4952236B2 (ja) 2012-06-13
EP2103697A4 (en) 2015-03-11
KR101107531B1 (ko) 2012-01-31
EP2103697A1 (en) 2009-09-23
WO2008081956A1 (ja) 2008-07-10
KR20090094001A (ko) 2009-09-02
CN101568655B (zh) 2011-06-29
TWI333507B (en) 2010-11-21
TW200837199A (en) 2008-09-16
CN101568655A (zh) 2009-10-28

Similar Documents

Publication Publication Date Title
EP2103697B1 (en) High carbon hot-rolled steel sheet
EP2053140B1 (en) High-strength steel sheets and processes for production of the same
EP1905851B1 (en) High-carbon hot-rolled steel sheet and process for producing the same
EP2053139B1 (en) Hot-rolled steel sheets excellent both in workability and in strength and toughness after heat treatment and process for production thereof
EP1932933A1 (en) Dead-soft high-carbon hot-rolled steel sheet and process for producing the same
EP3530769B1 (en) Martensitic stainless steel sheet
EP2796584B1 (en) High-strength steel sheet and process for producing same
JP2005528519A5 (ko)
CN111527224B (zh) 高强度钢板及其制造方法
EP2980245B1 (en) High-strength alloyed molten-zinc-plated steel sheet and method for manufacturing same
EP2631314A1 (en) Hot-rolled steel sheet, cold-rolled steel sheet, and plated steel sheet each having exellent uniform ductility and local ductility in high-speed deformation
EP1905850B1 (en) Process for manufacture of cold-rolled high-carbon steel plate
EP2955242B1 (en) Steel sheet for nitriding and production method therefor
EP4015660A1 (en) Steel sheet, member, method for producing said steel sheet and method for producing said member
EP2868762B1 (en) Steel sheet for soft nitriding and process for producing same
JP3460659B2 (ja) 軟質で熱処理歪みの小さい高炭素鋼帯とその製造方法
EP2868764B1 (en) Steel sheet for soft nitriding and method for manufacturing the same
EP3904554B1 (en) High-strength hot-dip galvanized steel sheet and method for manufacturing the same
CN115298341A (zh) 高强度热轧钢板及其制造方法
JP2001098328A (ja) 延性、加工性および耐リジング性に優れたフェライト系ステンレス鋼板の製造方法
JP3230587B2 (ja) 成形加工性および疲労特性に優れ且つ時効処理によって高強度を発現する高強度ステンレス冷延鋼帯およびその製造方法。
US11891676B2 (en) Flat steel product having improved processing properties
JP2001098327A (ja) 延性、加工性および耐リジング性に優れたフェライト系ステンレス鋼板の製造方法
JP2002167645A (ja) 焼付け硬化型冷延鋼板およびその製造方法
JP7323095B1 (ja) 高強度鋼板およびその製造方法

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: 20090623

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 HU IE IS IT LI LT LU LV MC MT NL 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: 20150211

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/58 20060101ALI20150205BHEP

Ipc: C21D 8/02 20060101ALI20150205BHEP

Ipc: C21D 9/46 20060101AFI20150205BHEP

Ipc: C22C 38/06 20060101ALI20150205BHEP

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

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20180323

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 602007058266

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C21D0009460000

Ipc: C22C0038000000

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

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

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/38 20060101ALI20181024BHEP

Ipc: C21D 8/02 20060101ALI20181024BHEP

Ipc: C21D 9/46 20060101ALI20181024BHEP

Ipc: C22C 38/04 20060101ALI20181024BHEP

Ipc: C22C 38/08 20060101ALI20181024BHEP

Ipc: C22C 38/06 20060101ALI20181024BHEP

Ipc: C22C 38/02 20060101ALI20181024BHEP

Ipc: C22C 38/00 20060101AFI20181024BHEP

INTG Intention to grant announced

Effective date: 20181106

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

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

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU LV MC MT NL 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: CH

Ref legal event code: EP

Ref country code: AT

Ref legal event code: REF

Ref document number: 1126960

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190515

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602007058266

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20190501

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: 20190501

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: 20190501

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: 20190901

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: 20190501

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: 20190501

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: 20190501

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

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: 20190802

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: 20190801

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: 20190501

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1126960

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190501

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: 20190901

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: 20190501

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: 20190501

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: 20190501

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: 20190501

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: 20190501

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: 20190501

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602007058266

Country of ref document: DE

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

Ref country code: IT

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

Effective date: 20190501

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: 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: 20190501

26N No opposition filed

Effective date: 20200204

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: 20190501

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: 20190501

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20191231

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: 20190501

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: 20191221

Ref country code: IE

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

Effective date: 20191221

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: 20191231

Ref country code: BE

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

Effective date: 20191231

Ref country code: CH

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

Effective date: 20191231

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: 20190501

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: 20190501

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: 20071221

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

Ref country code: GB

Payment date: 20221027

Year of fee payment: 16

Ref country code: FR

Payment date: 20221110

Year of fee payment: 16

Ref country code: DE

Payment date: 20221102

Year of fee payment: 16