EP2048256A1 - Blech aus nichtrostendem stahl für teile und herstellungsverfahren dafür - Google Patents

Blech aus nichtrostendem stahl für teile und herstellungsverfahren dafür Download PDF

Info

Publication number
EP2048256A1
EP2048256A1 EP07791595A EP07791595A EP2048256A1 EP 2048256 A1 EP2048256 A1 EP 2048256A1 EP 07791595 A EP07791595 A EP 07791595A EP 07791595 A EP07791595 A EP 07791595A EP 2048256 A1 EP2048256 A1 EP 2048256A1
Authority
EP
European Patent Office
Prior art keywords
mass
stainless steel
steel sheet
cold rolling
less
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
EP07791595A
Other languages
English (en)
French (fr)
Other versions
EP2048256B1 (de
EP2048256A4 (de
Inventor
Kazuhiko Adachi
Masaru Abe
Kazuyoshi Fujisawa
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.)
Nippon Steel Corp
Original Assignee
Sumitomo Metal Industries Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Sumitomo Metal Industries Ltd filed Critical Sumitomo Metal Industries Ltd
Publication of EP2048256A1 publication Critical patent/EP2048256A1/de
Publication of EP2048256A4 publication Critical patent/EP2048256A4/de
Application granted granted Critical
Publication of EP2048256B1 publication Critical patent/EP2048256B1/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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0452—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment with application of tension
    • 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
    • C22C38/04—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0252—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with application of tension

Definitions

  • the present invention relates to a stainless steel sheet processed to be industrial products and the production method thereof. More specifically, the present invention relates to a stainless steel sheet for parts which exhibits high-strength, high-fatigue property, and excellent workability together with high-flatness and low-residual stress and also relates to the production method thereof.
  • the invention relates to a stainless steel sheet which exhibits excellent performance in many products or parts produced from the stainless steel sheet or the steel strip (hereinafter, collectively, refer to as "stainless steel sheet”.) and relates to the production method thereof.
  • the invention relates to a stainless steel sheet suitably used for a wide variety of parts which requires higher precision and complexity with miniaturization and weight saving of the products and which are embedded in the industrial products and relates to the production method thereof.
  • a stainless steel sheet is firstly worked into a piece of predetermined dimensions by cutting, blanking, and so on; then, the obtained piece is formed into a certain shape by using dies.
  • One of the typical examples thereof may be springs.
  • Spring is used in many industrial products and it may often be used in many sites of one product. Spring has a wide variety and it can be roughly classified into disc spring and leaf spring, in view of shape. Specific examples thereof include: a washer inserted between a bolt and a nut; small-sized disc spring used underneath buttons of cellular telephone; gasket and metal packing respectively used for automobiles and motorcycles.
  • etching is carried out by forming a pattern on the sheet surface by using photoresist technique, dipping the patterned sheet into an acid. Then, by using chemical means in a manner like spraying, a part of the material is made corroded and the corroded part is removed (etched) to obtain a shape corresponding to the pattern. Etching is often used in a case where press working is difficult, for instance, working for precision parts.
  • the examples of the parts may be gimbals (spring) used for fixing magnetic head, small-sized parts like gears for feeding printer paper, shadow masks of conventional TV which requires to have an extremely large number of minute holes, and mesh for printing printed-circuit board.
  • metastable austenitic ( ⁇ ) stainless steel such as SUS 301 and SUS 304 has been used.
  • transformation stress-induced martensitic ( ⁇ ') transformation
  • ⁇ -parent phase solid martensitic phase
  • solid martensitic phase By working the austenitic stainless steel at room temperature, transformation (stress-induced martensitic ( ⁇ ') transformation) from ⁇ -parent phase to solid martensitic phase can be caused.
  • ⁇ ' stress-induced martensitic
  • the working is normally carried out by cold rolling so that the strength can be adjusted by adjusting rolling reduction of the cold rolling.
  • Patent document 1 discloses an invention where dimensions of compounds to be a source of breakage are restricted.
  • Patent document 2 discloses an invention where distribution of compounds to be a source of etch pit (hole) is restricted.
  • Patent document 3 discloses formability by microfabrication of crystal grain and improvement of fatigue property.
  • Patent documents 4 and 5 disclose TA (Tension-Annealing) treatment.
  • the treatment is the one in which tension is imparted without largely changing the post-temper-rolling mechanical properties and the tensile material is heated at relatively lower temperature.
  • Patent documents 6 and 7 disclose production methods of stainless steel including temper-annealing method and a high-performance metastable ⁇ -stainless steel sheet which can be obtained by the temper-annealing method.
  • the schematic flow of the process is shown in Fig. 6 .
  • This is a method about treatment of stainless steel material having the predetermined composition, in which the material hardened by cold rolling for reducing the sheet thickness to the finished thickness is softened by temper-annealing and the performance is adjusted. Accordingly, the material gets to have a mixed structure of recrystallized grain and unrecrystallized portion remaining influence of the previous working; hence, by adjusting the optimal ratio, high-strength and high-ductility can be made compatible.
  • Patent documents 8 to 10 disclose a stainless steel sheet for photo-etching by specifying rolling condition and heat treatment condition of the stainless steel sheet as a material and by increasing etching speed within crystal grain by introducing transformation and martensite into crystal grain. By making the etching speed within the area of the crystal grain equivalent to the etching speed in the grain boundary, and so on, flatness of the etched surface is improved.
  • the production method also have similar problems, so there is an issue to adopt a method for producing the stainless steel sheet which is capable of solving the above problems.
  • compatibility between high-strength and high-ductility of the material is limited.
  • leveling becomes difficult so that the sheet shape tends to be deteriorated.
  • straightening annealing takes a long time, this results in a factor for interfering productivity.
  • the variation causes a remarkable problem that lead to a substantial increase of product cost.
  • Patent documents 6 and 7 there are issues in promotion of miniaturization and weight saving of the products and parts as well as further improvement of workability to correspond to the wide variety of products.
  • an object of the present invention is to provide a stainless steel sheet which exhibits favorable strength and ductility and which is capable of improving workability (formability, etchability) and fatigue property.
  • Another object of the invention is to provide a method for producing the stainless steel sheet. Further, by the method for producing the stainless steel sheet, the invention is aimed at industrially and stably providing the stainless steel sheet of the invention with inexpensive price.
  • the present inventors had seriously studied the above problems. As a result, the inventors discovered the following findings to solve the above problems and the present invention was completed.
  • the inventors studied to obtain a mixed structure (mixed structure of highly-ductile recrystallized structure and unrecrystallized structure in which high-strength stress-induced martensitic phase remains) for improving the properties of stainless steel sheet which cannot be obtained from the conventional stainless steel sheet and the production method.
  • final rolling rate in thickness in a series of rolling process and influence of material composition were seriously studied. Consequently, stainless steel sheet having the below-described mixed structure can be obtained; by the production method, it also becomes apparent that workability, fatigue property, and so on can be improved.
  • the above discovery is based on the following findings.
  • (a) The mechanical properties of the stainless steel are improved by a structure having the mixed structure. Namely, recrystallized portion in the mixed structure gives effects for strengthening by microfabrication of crystal grain and for inhibiting uneven deformation by density rise along grain boundary.
  • TRIP effect can be obtained by work hardening and stress-induced ⁇ '-transformation from ⁇ -phase being reversely transformed.
  • the materials can maintain high-strength from the combination effects.
  • deformation is developed evenly so that formability (ductility) is improved.
  • etchability is understood that etched surface becomes even by grain refining and increase of ⁇ -parent phase as a unitary construction. As a result, uneven portion to be a source of fatigue breakdown disappears and fatigue property after formation and after etching is improved.
  • the first aspect of the present invention is a stainless steel sheet for parts, which consists essentially of: 0.01-0.08 mass % of C, 0.1-2.0 mass % of Si, 3.0 mass % or less of Mn, 10. 0-20. 0 mass % of Cr, 3. 0-12.
  • the third aspect of the invention is the stainless steel sheet for parts according to the first or second aspect of the invention, wherein average grain diameter of the recrystallized grain is 10 ⁇ m or less.
  • the fourth aspect of the invention is the stainless steel sheet for parts according to the third aspect of the invention, wherein the mixed structure includes 70 mass % or more of austenitic phase.
  • the fifth aspect of the invention is a method for producing the stainless steel sheet for parts, the method comprising the steps of: a first cold rolling (S1) for cold rolling, at least once, a material consisting essentially of 0.01-0.08 mass % of C, 0.1-2.0 mass % of Si, 3.
  • the sixth aspect of the invention is a method for producing the stainless steel sheet for parts, the method comprising the steps of: a first cold rolling (S1) for cold rolling, at least once, a material consisting essentially of 0.01-0.08 mass % of C, 0.1-2.0 mass % of Si, 3. 0 mass % or less of Mn, 10. 0-20.
  • S1 first cold rolling
  • the seventh aspect of the invention is the method for producing the stainless steel sheet for parts according to the fifth or sixth aspect of the invention, wherein the tension of the second annealing is 40% or less of 0.2% yield strength of the material at the maintained temperature.
  • the eight aspect of the invention is the method for producing the stainless steel sheet for parts according to any one of the fifth to seventh aspects of the invention, the method further comprising a temper rolling after the second annealing (S4).
  • the present invention it is possible to provide the stainless steel sheet which can be used for producing various parts accurately with high reliability.
  • the invention also provides a method for producing the stainless steel sheet.
  • the invention it is capable of industrially and stably providing the stainless steel sheet of the invention, which exhibits excellent formability, post-forming-fatigue property, and high-reliability, with inexpensive price. Further, corresponding to the recent environmental issue, it is possible to develop effective use of resources by miniaturization and weight saving.
  • the stainless steel sheet of the present invention As described above, in the stainless steel sheet of the invention, it has characteristics in the composition and structure, Md value, and conformation of the compounds contained therein. Now, each of the characteristics will be described.
  • the main component of the stainless steel sheet of the invention is Fe; contents shown below are the ratio to total mass of the stainless steel sheet as 100 mass %.
  • C is within the range of 0.01-0.08 mass %.
  • C is one of the inexpensive and effective interstitial solid-solution strengthening elements. When 0.01 mass % or more of C is contained, solid solution strengthening effect is attained. On the other hand, the upper limit is 0.08 mass %. Because C is a forceful ⁇ -stabilizing element, excessive addition may inhibit necessary stress-induced martensitic ( ⁇ ') transformation. It is also because when a production method containing temper-annealing is adopted, rough and large carbide is deposited to the grain boundary represented by Cr 23 C 6 compound at a time of temper-annealing and that deteriorates workability as well as corrosion resistance. More preferable C content is within the range of 0.02-0.07 mass %.
  • Si is an effective solid-solution strengthening element.
  • the reason for determining the lower limit to 0.1 mass % or more is because high-temperature strength is raised and that makes it possible to easily obtain the above mixed structure as the characteristic of the invention.
  • the reason for determining the upper limit to 2.0 mass % is because, as Si is also a ferrite ( ⁇ ) stabilizing element, excessive addition increases ⁇ '-phase remained during temper-annealing. More preferable Si content is within the range of 0.2-1.8 mass %.
  • Mn is 3.0 mass % or less.
  • Mn is a ⁇ -stabilizing element so that it is added in consideration for balance with other elements. The reason for determining the content to 3.0 mass % or less is because when excessively added, ⁇ '-phase cannot be obtained. Moreover, in the case, inclusions and the like are formed, which deteriorate the workability and corrosion resistance of the product. More preferable Mn content is within the range of 2.6 mass % or less.
  • Cr is 10.0-20.0 mass %.
  • Cr is one of the basic alloy elements of stainless steel.
  • the reason for determining the content to 10.0 mass % or more is to obtain necessary corrosion resistance.
  • the reason for determining the upper limit to 20.0 mass % is because Cr is a ⁇ -stabilizing element and excessive addition thereof causes increase of ⁇ '-phase remained after temper-annealing. More preferable Cr content is within the range of 13.0-19.0 mass %.
  • Ni is 3.0-12.0 mass %.
  • Ni is also the basic alloy elements of stainless steel. It is also the most effective ⁇ -stabilizing element.
  • the reason for determining the lower limit to 3. 0 mass % is because the range is essential for obtaining ⁇ -phase which is stable at room temperature.
  • the reason for determining the upper limit to 12.0 mass % is because it is necessary to develop ⁇ '-transformation within the predetermined range. More preferable Ni content is within the range of 3.5-11.5 mass %.
  • N is 0.02-0.25 mass %. Similar to C, N is one of the effective interstitial solid-solution strengthening elements so that it is capable of fusing into a state of solid-solution at higher temperature compared with the case of C without forming compound. In other words, it is the major strengthening element of the invention. From this point of view, the lower limit is the lower limit is determined to 0.02 mass %. The reason for determining the upper limit to 0.25 mass % is because excessive addition may deteriorate hot-workability and may interfere with production of the sheet. In addition, similar to C, N is one of the forceful ⁇ -stabilizing elements, so it may inhibit ⁇ '-transformation. More preferable range of N content is 0.04-0.20%, furthermore preferably 0.08-0.02%, the most preferably 0.10-0.20 mass %.
  • Nb Content of Nb is 0.50 mass % or less.
  • Nb enables to make itself deposit as Nb compound which is finely dispersed and is relatively stable even at high temperature, which enables to easily obtain the mixed structure. By inhibiting the grain growth, it is possible to make recrystallized grain finer.
  • the reason for determining the upper limit to 0.50 mass % is because excessive addition forms rough compounds thereby deteriorates ductility of the material. Further, since Nb is an expensive substance, in view of cost, the upper limit is set. More preferable Nb content is within the range of 0.45 mass % or less.
  • Ti Content of Ti is 0.50 mass % or less.
  • Ti seems to show similar effect like Nb. Namely, precipitation of Ti compound enables to obtain mixed structure easily and enables to make recrystallized grain finer. Moreover, it is presumably possible to form the compound easily than the case of Nb.
  • the reason for determining the upper limit to 0.50 mass % is because excessive addition forms rough compounds that results in decrease of ductility of the material. More preferable Ti content is within the range of 0.45 mass % or less.
  • V Content of V is 0.50 mass % or less.
  • V seems to show similar effect like Nb and Ti. Namely, precipitation of V compound enables to obtain mixed structure easily and enables to make recrystallized grain finer.
  • the reason for determining the upper limit to 0.50 mass % is because excessive addition forms rough compounds that results in decrease of ductility of the material. More preferable V content is within the range of 0.001 mass % or more and 0.45 mass % or less.
  • elements added from the industrial aspect like Ca, Al, rare-earth metal (REM) these of which are used as deoxidizing agent at a time of molding, or B anticipated for improvement of hot-workability, may be contained such that total amount becomes 0.3 mass % or less.
  • inevitable Cu and Mo respectively may be contained within the range of 0.4 mass % or less.
  • Cu and Mo in the invention act as adjusting elements for ⁇ -stability. Inevitable impurities in the normal composition may be contained.
  • Md value is calculated based on the following formula (1) or (2) shown in the present invention; the value is within the range of 0-80 °C.
  • formula (2) is used when at least one selected from the above Nb, Ti, V, each of which is not inevitable impurities, is added.
  • formula (1) is used.
  • content (mass %) of corresponding component is substituted.
  • Md 500 - 458 ⁇ C + N - 9 ⁇ Si + Mn - 14 ⁇ Cr - 20 ⁇
  • Ni Md 500 - 458 ⁇ C + N - 9 ⁇ Si + Mn - 14 ⁇ Cr - 20 ⁇ Ni - 65 ⁇ Nb - 27 ⁇ Ti - 61 ⁇
  • the formula is formulated the temperature (30 °C), where 50% of the total transforms to ⁇ '-phase when 30% tensile deformation is given to ⁇ - monophase material, based on results of a series of experiment of the present invention.
  • the invention is intended for metastable ⁇ -stainless steel and utilize ⁇ '-transformation, so it is necessary to control ⁇ '-transformation. Therefore, the optimal Md value for this is set to 0-80 °C. It is more preferably 10-70 °C.
  • the compound contained in the stainless steel sheet particularly the compound whose maximum diameter is 20 ⁇ m or more exists at a ratio of 30 or less per 5 g (mass) of the stainless steel sheet. Accordingly, it is possible to reduce defects attributed to the compounds.
  • material of the invention has excellent formability; in addition, seemingly, probability where rough compounds exist in the vicinity of the sheet surface becomes extremely small.
  • convexo-concaves and minor cracks attributed to the large difference of deformability of the both (material and rough compound) can be improved.
  • compound exposure attributed to the difference of corrosion resistance as well as occurrence of local defects such as holes (etch pit) caused by dropping can be prevented. As a result, machined surface of the parts becomes flat and smooth; whereby fatigue property is improved. The local defects are also presumably detected by measurement of surface roughness of the machined surface.
  • Structure of the material for the stainless steel sheet of the present invention is a "mixed structure" defined by a structure in which recrystallized grain and unrecrystallized portion which leaves influence of the pre-working are mixed.
  • the mixed structure may be a structure having 70 area % or more of ⁇ -phase.
  • ⁇ -phase As the main structure, formability and fatigue property can be further improved. More preferable ratio of the ⁇ -phase is 80 area % or more.
  • the stainless steel sheet By forming the stainless steel sheet as described above, it is possible to provide a stainless steel sheet which is excellent in various properties and also is possible to improve workability (formability, etchability) and fatigue property.
  • grain diameter of the recrystallization may be 10 ⁇ m or less. As a consequent, formability and fatigue property attributed to the miniaturization of crystal grain can be further improved. More preferable grain diameter thereof is 6 ⁇ m or less.
  • the method for producing the stainless steel sheet of the invention includes the steps of: a first cold rolling (S1) for giving at least one cold rolling; a first annealing (S2) being made a set together with the first cold rolling (S1); a second cold rolling (S3); and a second annealing (S4) for giving annealing for the purpose of tempering.
  • S1 first cold rolling
  • S2 first annealing
  • S3 second cold rolling
  • S4 second annealing
  • first cold rolling step (S1) materials, to which the above described components are added and hot-worked, are supplied.
  • the step is provided to mainly make the dimension of the material closer to the dimensions of the finished steel sheet. Thus, it is not necessarily once, several times of rolling can be carried out.
  • rolling reduction of the first cold rolling step (S1) and the second cold rolling conducted later on is 60% or more, preferably 70% or more, more preferably 80% or more, and the most preferably 90% or more.
  • This step is the one to be made a set together with the above first cold rolling step (S1); it is provided for softening and elongating the material as the main purpose. Therefore, any type of annealing which is normally carried out is not specifically restricted to. The condition may be determined depending on the material to be provided and confirmation of finally obtained steel sheet.
  • the second cold rolling step (S3) is provided after the above-described set of the first cold rolling step (S1) and the first annealing step (S2); this is the last cold rolling step.
  • thickness of the sheet is reduced to that of the finished stainless steel sheet.
  • the reduction of thickness is expressed in rolling reduction at 20% or more and in a total rolling reduction of the first cold rolling and the second cold rolling at 60% or more. This is because if the rolling reduction is set at 20% or more, sufficient stress-induced martensitic ( ⁇ ') phase can be obtained. Further, due to this, grain refining can be done.
  • the rolling reduction is preferably at 30% or more.
  • the reason for setting the rolling reduction of total of the first cold rolling and the second cold rolling to 60% or more is to reduce the number of rough compounds having the grain diameter of 20 ⁇ m or more, by having lager rolling reduction to crush the compounds into finer pieces. Thereby, it becomes possible to make maximum diameter of the compounds smaller and to reduce the number of rough compounds having the grain diameter of 20 ⁇ m or more. In such a case, as it gives larger effect in crushing the rough compounds, it is preferable to carry out cold rolling by using work roll having a small diameter.
  • the second annealing step (S4) is the last annealing step; by this step, conformation of the materials of the finished stainless steel sheet can be determined.
  • annealing temperature is set at 650-1000 °C and holding time is set for 300 seconds or less.
  • the conditions are provided in view of adjusting mechanical properties of the material, as well as productivity and impact on the metallographic structure of the material like grain growth. Under the conditions, the production is effective, and it is capable of obtaining a stainless steel sheet of high-planarization and low-residual stress.
  • Fig. 2 is a graph showing an example about relations between temperature and 0.2% yield strength of the material. The tension is determined based on i.e. Fig. 2 and loaded.
  • the method for microfabrication of inclusion may preferably be a measure for strengthening floatation-separation of the rough inclusion at a time of molding.
  • there may be a method for carrying out floatation-separation of rough inclusion by extending the heating duration of the molten metal.
  • S1 and S2 With rolls of small diameter, it is possible to crush the rough inclusion into finer pieces.
  • the above two methods may be combined; it is not specifically restricted as long as number of the compound whose maximum diameter is 20 ⁇ m or more contained in the stainless steel sheet can be reduced to 30 or less per 5 g (mass) of the stainless steel sheet.
  • temper rolling may be given after the second annealing step.
  • the invention enables to produce the stainless steel sheet which is excellent in the above various properties and is possible to improve workability (formability, etchability) and fatigue property. Moreover, according to the production method, it is capable of industrially and stably providing the stainless steel sheet of the invention with inexpensive price.
  • compositions of the test material are shown in Table 1. Among the compositions, some of the components whose value are outside the scope of the invention are marked with "*" on the right shoulder of numeric value of the content.
  • thickness of the sheet were adjusted by partial-cutting work and acid cleaning, and then, first cold rolling and annealing were carried out. Further, second cold rolling and second annealing were carried out based on the conditions shown in Table 2. Final thickness of the sheets was 0.2 mm. About examples shown in No. 10 and No. 17, for microfabrication of inclusion, small diameter of work rolls (60 mm in diameter) were used for cold rolling, compared with the work rolls of 200 mm in diameter used in other purposes than microfabrication of inclusion.
  • test pieces were taken; then, various properties were researched and made comparison.
  • the structure about a cross section parallel to the rolling direction was observed by using optical microscope and SEM. Meanwhile, thin film was produced and the structure was observed by using transmission electron microscope (TEM). A photograph of average structure in each test pieces were taken, and grain diameter was measured from these photographs. In addition to this, judgment whether or not the structure is a mixed structure was carried out.
  • grain diameter of Nos. 1-26 are shown by the value of recrystallized grain after temper-annealing
  • grain diameter of Nos. 27-32 are shown by the value of recrystallized grain after second annealing step.
  • the grain diameters are shown in brackets in Table 3. It was presumed that no change in grain diameter was made by straightening annealing.
  • Fatigue limit (the upper limit endurable for 107-time repeated bending) of the material where bending work had not been given was clarified by using a Reversed Plane-Bending Fatigue tester. Following to this, bending was repeatedly given to the test pieces used for bending for measurement of the above surface roughness under 90% stress of the fatigue limit of the material; and existence of cracks after 107-time repeated bending was observed. When cracked, it was evaluated by X; when crack was not caused, it was evaluated by ⁇ .
  • flatness was evaluated by warping of the sheet.
  • Example 30 means an example of the present invention.
  • Comp. example means a comparative example to the present invention.
  • example 27 340 34.2 79 221 ⁇ -40 -38 301-1/2H Comp. example 28 389 24.5 24 245 ⁇ -36 -34 301-3/4H Comp. example 29 473 8.9 64 324 ⁇ -31 -18 301-H Comp. example 30 295 30.8 48 205 ⁇ -42 -42 304-1/2H Comp. example 31 354 18.4 36 274 ⁇ -38 -45 304-3/4H Comp. example 32 394 7.2 50 358 ⁇ -42 -40 304-H Comp. example note: "Example” means an example of the present invention. "Comp. example” means a comparative example to the present invention.
  • Fig. 3 a relation between hardness and elongation is shown in Fig. 3 based on the results of Examples of the present invention. As seen from Table 4 and Fig. 3 , Nos. 1-17 of Examples of the invention shows higher-strength and higher-ductility compared with any of the Nos. 18-32 as Comparative examples.
  • FIG. 4 is photographs about the surface of sheets before-and-after the bending and the surface roughness (Ry) at the time. Specifically, about an Example of the present invention (No. 4) and a Comparative example (No. 28), photographs and surface roughness are shown in cases of flat sheet, bending radius of 2 mm, and bending radius of 0.5 mm. According to the photographs and values of Ry, effects of the present invention can be seen. Particularly, with regard to the flat sheet, although any of the stainless steel sheets show almost the same surface roughness, when bended, the surface roughness of each sheet shows various difference.
  • bending fatigue property about the present invention is favorable. Therefore, it is capable of maintaining excellent fatigue property even after bending. As it were, by optimizing not only mixed structure but also distribution of indwelling compounds, even deformation is developed and defect caused by bending is decreased. As a result, it is assumed that the invention can show excellent formability and maintain high fatigue strength.
  • etchability maximum value of the surface roughness decreases and defects like etch pit decreases in the worked surface; the surface tends to become smoother compared with the state before working.
  • workability together with etchability can also be improved so that it is possible to maintain high fatigue strength even if it is worked parts.
  • temper-annealing temperature is relatively high, diameter of recrystallized grains rise over 10 ⁇ m.
  • imparted tension rises over 40% of 0.2% yield strength; thereby ⁇ -phase ratio of mixed structure becomes less than 70%. Due to this, although these Examples can obtain superior stainless steel sheets to those of Comparative examples, among the Examples, the balance between strength and ductility tends to be inferior. So, for Nos. 2, 11, and 12, similar to Nos. 14, 16, and 17, it is possible to inhibit grain growth by adding Nb, Ti, and V to improve the performance furthermore. About Nos. 7 and 8, similar to No. 10, the performance can be improved by diminishing the imparted tension.
  • Nos. 1-18, Nos. 20-22, and Nos. 26-32 in which microfabrication of inclusion were carried out number of inclusion whose maximum diameter is 20 ⁇ m or more is within the scope of the present invention.
  • No. 10 using floatation of inclusion and work rolls of small diameter particularly show the best balance between strength and ductility as well as workability.
  • the Comparative examples as described above are poor in balance between those strength and ductility. More specifically, content of the components and Md value of Nos. 18-21 meet the scope of the present invention; however, due to the lack of rolling reduction, Nos. 18 and 19 cause production of 30 or more of compounds whose maximum diameter is 20 ⁇ m or more. Consequently, since mixed structure is not formed, favorable properties are not obtained about these Comparative examples. Moreover, about Nos. 20 and 21, as temper-annealing temperature is out of the scope of the production method of the present invention; the mixed structure is not formed. Thereby, the workability and fatigue property of the products are equivalent to or less than those of conventional products. As materials of other Comparative examples do not also satisfy necessary composition, high performance cannot be obtained.
  • Table 5 shows results of properties of the No. 2 material treated by temper rolling under rolling reduction at 10% and 20%.
  • No. 2-a is a case where No. 2 is treated by temper rolling under 10% rolling reduction; similarly, No. 2-b is a case where No. 2 is treated by temper rolling under 20% rolling reduction. As a result, it becomes apparent that the material maintains excellent properties even after temper rolling.

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)
  • Metal Rolling (AREA)
EP07791595.7A 2006-07-28 2007-07-30 Blech aus nichtrostendem stahl für teile und herstellungsverfahren dafür Active EP2048256B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2006206250 2006-07-28
PCT/JP2007/064910 WO2008013305A1 (fr) 2006-07-28 2007-07-30 Feuille en acier inoxydable pour pièces et procédé de fabrication de celle-ci

Publications (3)

Publication Number Publication Date
EP2048256A1 true EP2048256A1 (de) 2009-04-15
EP2048256A4 EP2048256A4 (de) 2016-07-13
EP2048256B1 EP2048256B1 (de) 2021-11-10

Family

ID=38981613

Family Applications (1)

Application Number Title Priority Date Filing Date
EP07791595.7A Active EP2048256B1 (de) 2006-07-28 2007-07-30 Blech aus nichtrostendem stahl für teile und herstellungsverfahren dafür

Country Status (4)

Country Link
EP (1) EP2048256B1 (de)
JP (1) JP4475352B2 (de)
CN (1) CN101490298B (de)
WO (1) WO2008013305A1 (de)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11486017B2 (en) 2016-05-24 2022-11-01 Arcelormittal Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts
EP4177369A4 (de) * 2020-09-03 2024-07-17 Posco Co Ltd Austenitischer edelstahl und herstellungsverfahren dafür
EP4343013A4 (de) * 2021-06-21 2024-09-25 Posco Co Ltd Austenitischer edelstahl und herstellungsverfahren dafür
EP4343014A4 (de) * 2021-07-06 2024-09-25 Posco Co Ltd Austenitischer edelstahl und herstellungsverfahren dafür

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5272457B2 (ja) * 2008-03-12 2013-08-28 Ｊｆｅスチール株式会社 高速モータ用ロータおよびその製造方法
AT513014A2 (de) * 2012-05-31 2013-12-15 Berndorf Band Gmbh Metallband sowie Verfahren zur Herstellung eines oberflächenpolierten Metallbandes
CN104302800B (zh) * 2012-08-20 2016-08-17 新日铁住金株式会社 不锈钢板及其制造方法
WO2014038510A1 (ja) * 2012-09-04 2014-03-13 新日鐵住金株式会社 ステンレス鋼板およびその製造方法
CN106148849A (zh) * 2015-03-23 2016-11-23 江苏锦明不锈钢新材料有限公司 一种高强度不锈钢
KR101742088B1 (ko) * 2015-12-23 2017-06-01 주식회사 포스코 친수성 및 접촉저항이 향상된 고분자 연료전지 분리판용 스테인리스강 및 이의 제조 방법
WO2017203311A1 (en) * 2016-05-24 2017-11-30 Arcelormittal Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts
JP6857308B2 (ja) * 2017-03-15 2021-04-14 日立金属株式会社 鋼帯の製造方法
JP7116648B2 (ja) * 2018-09-13 2022-08-10 日鉄ステンレス株式会社 ステンレス鋼板およびその製造方法
JP7165202B2 (ja) * 2018-10-04 2022-11-02 日本製鉄株式会社 オーステナイト系ステンレス鋼板及びその製造方法

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05279802A (ja) 1991-03-11 1993-10-26 Nisshin Steel Co Ltd ばね特性および加工部の疲労特性に優れたばね用ステンレス鋼およびその製造方法
US5407493A (en) * 1993-03-08 1995-04-18 Nkk Corporation Stainless steel sheet and method for producing thereof
JPH1034237A (ja) 1996-07-30 1998-02-10 Sumitomo Metal Ind Ltd 平坦度に優れた冷間圧延ステンレス鋼板の製造方法
EP1036853B1 (de) * 1998-09-04 2015-07-15 Nippon Steel & Sumitomo Metal Corporation Rostfreier stahl für motordichtung
JP3544488B2 (ja) 1999-03-23 2004-07-21 新日本製鐵株式会社 ステンレス極薄箔
JP3573047B2 (ja) 2000-02-10 2004-10-06 住友金属工業株式会社 エッチング後の平坦性に優れたステンレス鋼板の製造方法
JP3603726B2 (ja) * 2000-03-03 2004-12-22 住友金属工業株式会社 電子機器部品用オーステナイト系ステンレス鋼板
JP2002173742A (ja) * 2000-12-04 2002-06-21 Nisshin Steel Co Ltd 形状平坦度に優れた高強度オーステナイト系ステンレス鋼帯およびその製造方法
JP2002194506A (ja) 2000-12-25 2002-07-10 Sumitomo Metal Ind Ltd ステンレス鋼板およびその製造方法
JP3696552B2 (ja) * 2001-04-12 2005-09-21 日新製鋼株式会社 加工性，冷間鍛造性に優れた軟質ステンレス鋼板
JP4285302B2 (ja) 2004-03-31 2009-06-24 住友金属工業株式会社 微細介在物含有ステンレス鋼とその製造方法
JP2005314772A (ja) 2004-04-30 2005-11-10 Nippon Yakin Kogyo Co Ltd フォトエッチング加工用ステンレス鋼板およびその製造方法
JP4332670B2 (ja) 2004-05-10 2009-09-16 日本冶金工業株式会社 フォトエッチング加工用ステンレス鋼板およびその製造方法
JP4324509B2 (ja) 2004-05-10 2009-09-02 日本冶金工業株式会社 フォトエッチング加工用ステンレス鋼板およびその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2008013305A1 *

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11486017B2 (en) 2016-05-24 2022-11-01 Arcelormittal Cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts
EP4177369A4 (de) * 2020-09-03 2024-07-17 Posco Co Ltd Austenitischer edelstahl und herstellungsverfahren dafür
EP4343013A4 (de) * 2021-06-21 2024-09-25 Posco Co Ltd Austenitischer edelstahl und herstellungsverfahren dafür
EP4343014A4 (de) * 2021-07-06 2024-09-25 Posco Co Ltd Austenitischer edelstahl und herstellungsverfahren dafür

Also Published As

Publication number Publication date
CN101490298B (zh) 2011-11-16
JP4475352B2 (ja) 2010-06-09
JPWO2008013305A1 (ja) 2009-12-17
WO2008013305A1 (fr) 2008-01-31
EP2048256B1 (de) 2021-11-10
EP2048256A4 (de) 2016-07-13
CN101490298A (zh) 2009-07-22

Similar Documents

Publication Publication Date Title
EP2048256B1 (de) Blech aus nichtrostendem stahl für teile und herstellungsverfahren dafür
EP1734143B1 (de) Blech aus ferritischem nichtrostendem stahl mit hervorragender umformbarkeit und vefahren zu seiner herstellung
JP5960809B2 (ja) 精密加工用ステンレス鋼板およびその製造方法
KR100977600B1 (ko) 오렌지 필이 작고 성형성이 우수한 페라이트계 스테인레스강판 및 그 제조 방법
EP2039791B1 (de) Hochfestes stahlblech und herstellungsverfahren dafür
JP5056985B2 (ja) オーステナイト系ステンレス鋼板およびその製造方法
EP1990430B1 (de) Widerstandsfähige heißgewalzte Stahlplatte und Herstellungsverfahren dafür
EP2554699B1 (de) Stahlblech von hoher zugfestigkeit und hervorragender dehnbarkeit sowie verfahren zu seiner herstellung
EP1484424B1 (de) Rostfreier ferritischer Bandstahl mit hervorragenden Press- sowie sekundären Verformungseigenschaften und Verfahren zu seiner Herstellung
US4812176A (en) Process for the production of a strip of a chromium stainless steel of a duplex structure having high strength and elongation as well as reduced plane antisotropy
KR101620252B1 (ko) 스테인리스 강판과 그 제조 방법
JPH0814004B2 (ja) 耐食性に優れた高延性高強度の複相組織クロムステンレス鋼帯の製造法
JP2010133028A (ja) 延性に優れた高強度低比重鋼板の製造方法
KR102711663B1 (ko) 오스테나이트계 스테인리스 강판
JPH1072644A (ja) スプリングバック量が小さいオーステナイト系ステンレス冷延鋼板およびその製造方法
JP2005029889A (ja) 延性に優れた高強度低比重鋼板およびその製造方法
JP4964492B2 (ja) 中炭素鋼板及びその製造方法
JP2020164956A (ja) フェライト系ステンレス鋼板およびその製造方法
KR101618489B1 (ko) 열연 강판 및 그 제조 방법
JP3603726B2 (ja) 電子機器部品用オーステナイト系ステンレス鋼板
JP2001207244A (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冷延鋼板およびその製造方法
JP3727646B2 (ja) 精密打抜き性に優れたオーステナイト系ステンレス鋼板の製造方法
EP4108796A1 (de) Stahlblech für dose und verfahren zur herstellung davon
KR20110075408A (ko) 페라이트계 스테인레스강 및 그 제조방법
JPH11315353A (ja) 成形性に優れたフェライト系ステンレス鋼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: 20090115

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

AX Request for extension of the european patent

Extension state: AL BA HR MK RS

DAX Request for extension of the european patent (deleted)
RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: NIPPON STEEL & SUMITOMO METAL CORPORATION

RA4 Supplementary search report drawn up and despatched (corrected)

Effective date: 20160613

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/00 20060101AFI20160607BHEP

Ipc: C21D 6/00 20060101ALI20160607BHEP

Ipc: C21D 9/46 20060101ALI20160607BHEP

Ipc: C22C 38/40 20060101ALI20160607BHEP

Ipc: C22C 38/50 20060101ALI20160607BHEP

Ipc: C22C 38/46 20060101ALI20160607BHEP

Ipc: C21D 8/04 20060101ALI20160607BHEP

Ipc: C22C 38/48 20060101ALI20160607BHEP

Ipc: C22C 38/58 20060101ALI20160607BHEP

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: 20180704

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

Free format text: STATUS: EXAMINATION IS IN PROGRESS

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: NIPPON STEEL CORPORATION

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 602007061362

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C22C0038000000

Ipc: C22C0038020000

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 38/02 20060101AFI20210412BHEP

Ipc: C21D 8/02 20060101ALI20210412BHEP

Ipc: C21D 9/46 20060101ALI20210412BHEP

Ipc: C22C 38/00 20060101ALI20210412BHEP

Ipc: C22C 38/04 20060101ALI20210412BHEP

Ipc: C21D 6/00 20060101ALI20210412BHEP

Ipc: C21D 8/04 20060101ALI20210412BHEP

Ipc: C22C 38/40 20060101ALI20210412BHEP

Ipc: C22C 38/48 20060101ALI20210412BHEP

Ipc: C22C 38/50 20060101ALI20210412BHEP

Ipc: C22C 38/46 20060101ALI20210412BHEP

INTG Intention to grant announced

Effective date: 20210503

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

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

Free format text: STATUS: EXAMINATION IS IN PROGRESS

INTC Intention to grant announced (deleted)
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

INTG Intention to grant announced

Effective date: 20210818

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: AT

Ref legal event code: REF

Ref document number: 1446160

Country of ref document: AT

Kind code of ref document: T

Effective date: 20211115

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602007061362

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: LT

Ref legal event code: MG9D

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1446160

Country of ref document: AT

Kind code of ref document: T

Effective date: 20211110

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: 20211110

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: 20211110

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: 20220210

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: 20211110

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: 20220310

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: 20211110

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: 20220310

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: 20211110

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: 20211110

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: 20211110

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: 20220211

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: 20211110

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

Ref country code: SK

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

Effective date: 20211110

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: 20211110

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: 20211110

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: 20211110

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: 20211110

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602007061362

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

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

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20220811

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: 20211110

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: 20211110

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: 20220731

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: 20220730

Ref country code: LI

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

Effective date: 20220731

Ref country code: FR

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

Effective date: 20220731

Ref country code: CH

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

Effective date: 20220731

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: 20211110

Ref country code: BE

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

Effective date: 20220731

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: 20220730

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

Ref country code: HU

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

Effective date: 20070730

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: 20211110

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

Ref country code: GB

Payment date: 20240606

Year of fee payment: 18

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: 20211110

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

Ref country code: DE

Payment date: 20240604

Year of fee payment: 18