EP3282027B1 - High-carbon steel wire material with excellent wire drawability, and steel wire - Google Patents
High-carbon steel wire material with excellent wire drawability, and steel wire Download PDFInfo
- Publication number
- EP3282027B1 EP3282027B1 EP16772782.5A EP16772782A EP3282027B1 EP 3282027 B1 EP3282027 B1 EP 3282027B1 EP 16772782 A EP16772782 A EP 16772782A EP 3282027 B1 EP3282027 B1 EP 3282027B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- wire
- less
- steel wire
- pearlite
- proeutectoid cementite
- 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
Links
- 229910000831 Steel Inorganic materials 0.000 title claims description 82
- 239000010959 steel Substances 0.000 title claims description 82
- 229910000677 High-carbon steel Inorganic materials 0.000 title description 10
- 239000000463 material Substances 0.000 title description 10
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 74
- 229910001567 cementite Inorganic materials 0.000 claims description 73
- 229910001562 pearlite Inorganic materials 0.000 claims description 48
- 238000005491 wire drawing Methods 0.000 claims description 41
- 229910000859 α-Fe Inorganic materials 0.000 claims description 26
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 8
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 claims description 2
- 229910052717 sulfur Inorganic materials 0.000 claims description 2
- 229910052719 titanium Inorganic materials 0.000 claims description 2
- 238000001816 cooling Methods 0.000 description 40
- 230000000694 effects Effects 0.000 description 24
- 238000012360 testing method Methods 0.000 description 19
- 230000001965 increasing effect Effects 0.000 description 12
- 238000000034 method Methods 0.000 description 12
- 239000011572 manganese Substances 0.000 description 10
- 230000003247 decreasing effect Effects 0.000 description 8
- 238000005096 rolling process Methods 0.000 description 8
- 239000010936 titanium Substances 0.000 description 8
- 230000009466 transformation Effects 0.000 description 8
- 239000010955 niobium Substances 0.000 description 7
- 239000011651 chromium Substances 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 6
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 6
- 230000009467 reduction Effects 0.000 description 6
- 229920006395 saturated elastomer Polymers 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 5
- 229910001563 bainite Inorganic materials 0.000 description 5
- 239000010949 copper Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 238000011156 evaluation Methods 0.000 description 5
- 238000005098 hot rolling Methods 0.000 description 5
- 238000001000 micrograph Methods 0.000 description 5
- 239000002699 waste material Substances 0.000 description 5
- 229910052796 boron Inorganic materials 0.000 description 4
- 230000015556 catabolic process Effects 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 238000006731 degradation reaction Methods 0.000 description 4
- 230000000593 degrading effect Effects 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 238000009776 industrial production Methods 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 238000001878 scanning electron micrograph Methods 0.000 description 4
- 238000005204 segregation Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910001335 Galvanized steel Inorganic materials 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 2
- 239000008397 galvanized steel Substances 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 230000001376 precipitating effect Effects 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000010622 cold drawing Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000012790 confirmation Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 239000013307 optical fiber Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
- B21C1/02—Drawing metal wire or like flexible metallic material by drawing machines or apparatus in which the drawing action is effected by drums
-
- 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
- C21D6/001—Heat treatment of ferrous alloys containing 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/007—Heat treatment of ferrous alloys containing Co
-
- 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
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/54—Furnaces for treating strips or wire
- C21D9/64—Patenting furnaces
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
-
- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
- B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Definitions
- the present invention relates to a high-carbon steel wire rod with excellent wire drawability, and a steel wire obtained by wire drawing of the high-carbon steel wire rod mentioned above. More particularly, the present invention relates to a high-carbon steel wire rod produced by hot rolling, which is a raw material of a high strength steel wire to be used mainly for steel cords, wire ropes, saw wires and the like.
- a high strength steel wire used for steel cords, wire rope and the like for example, piano wires mentioned in JIS G 3522(1991).
- the piano wires are roughly classified into three types such as classes A, B, and V, and examples of the high strength piano wire class B include SWP-class B having a wire diameter of 0.2 mm and a tensile strength of 2,840 to 3,090 MPa.
- SWP-class B having a wire diameter of 0.2 mm and a tensile strength of 2,840 to 3,090 MPa.
- pearlite steels such as SWRS82A mentioned in JIS G 3502 (2004) are used as the raw material of the piano wire.
- a common method for producing a high strength steel wire is as follows. First, a steel wire rod produced by hot rolling (also referred to as the rolled wire rod) is placed in a ring shape on a cooling conveyor, thereby allowing to undergo pearlite transformation, and then coiled into a coil shape to obtain a wire rod coil. Then, wire drawing is performed and a steel wire having desired wire diameter and strength is obtained by making use of the work hardening function of pearlite. When it is impossible to be drawn to a desired wire diameter due to working limit of the steel wire rod, a heat treatment called patenting is applied between wire drawings. For example, to obtain an extra fine steel wire having a wire diameter of 0.2 mm, wire drawing and a patenting treatment are generally performed by repeating several times.
- Patent Document 1 relates to a wire rod for a high strength steel wire which is useful as the raw material of a galvanized steel wire to be used for ropes for a bridge, and particularly mentions a wire rod for a high strength steel wire, which is excellent in workability when wire drawing is performed by so-called cold drawing without subjecting to a heat treatment after rolling.
- precipitation of proeutectoid cementite is suppressed by precipitating fine TiC near grain boundaries, so that the lower limit of the Ti content is set at 0.02% or more.
- Patent Document 2 relates to a small diameter high-carbon hot-rolled wire rod which is capable of wire drawing at true strain of 2.2 or more even in an as-hot-rolled state. Specifically, Patent Document 2 mentions that a steel billet having the Si content suppressed to 0.50% or less is thinned to a wire rod diameter of 4.5 mm or less by increasing rolling reduction during hot rolling, thereby making austenite grains ( ⁇ grains) finer leading to acceleration of pearlite transformation, thus making it possible to prevent precipitation of particles of proeutectoid ferrite and proeutectoid cementite.
- Patent Document 3 relates to a deformed wire for a submarine optical fiber cable in which a wire rod for a high tensile steel wire is used. Specifically, Patent Document 3 mentions that, by using a wire rod in which Si is segregated so as to satisfy the following inequality expression: Si maximum segregation degree of cementite/ferrite interface in a range of 30 nm from an interface between cementite and ferrite to a ferrite phase side in a pearlite structure (maximum Si concentration in a range of 30 nm from an interface between cementite and ferrite to a ferrite phase side / Si content of bulk) ⁇ 1.1, it is possible to prevent wire breakage during deformation working.
- JP 4 003450 B2 discloses a steel wire and a manufacturing method thereof.
- Patent Documents 1 to 3 respectively have the following problems.
- Patent Document 1 is intended for a wire rod to be used for a galvanized steel wire, and is not intended for a steel wire having an extra fine wire diameter of approximately 0.2 mm, such as a piano wire.
- Patent Document 1 when an extra fine steel wire is produced using a wire rod having a large Ti content, wire breakage during wire drawing becomes remarkable due to Ti based inclusions. Therefore, it is difficult to apply the technique of Patent Document 1 to the extra fine steel wire to be supplied for steel cords.
- Patent Document 2 when using a wire rod having a diameter of 4.5 mm or less, the productivity is degraded to cause a problem that wire rods are easily entangled with each other during the production of a coil.
- Patent Document 3 when using a method in which an Si concentration difference is applied at an interface between cementite and ferrite in the pearlite structure, it is impossible to sufficiently reduce proeutectoid ferrite which is harmful for the wire drawability.
- the degree of working carried out in Patent Document 3 is 82.6% in terms of an area reduction rate even when summing up wire drawing and cold rolling. Since the area reduction rate of wire drawing required to an extra fine steel wire such as a steel cord is larger, it is insufficient to apply the extra fine steel wire to the above-mentioned applications.
- the present invention has been made in light of the foregoing circumstance, and it is an object of the present invention to provide a high-carbon steel wire rod with excellent wire drawability which can also be applied to extra fine steel wires such as steel cord, and a steel wire.
- the present invention can provide a high-carbon steel wire rod with excellent wire drawability which can also be applied to extra fine steel wires such as steel cord.
- Fig. 1 is a diagram showing an Si concentration difference at an interface between a proeutectoid cementite phase and a ferrite phase in the sample of test No. 12 in Table 2 of Example.
- the inventors of the present invention have intensively studied using a high-carbon steel wire rod having the C content of 0.90% or more.
- ferrite an Si concentration difference of 0.50% or more at an interface between proeutectoid cementite and ferrite that forms a lamellar structure of pearlite (hereinafter may be simply referred to as ferrite)
- ferrite an Si concentration difference between an average of the Si concentration inside proeutectoid cementite, and a maximum value of the Si concentration inside ferrite is 0.50% or more
- Patent Document 3 There is also some mention of Si segregation in Patent Document 3.
- the Si concentration difference at an interface between cementite (lamellar cementite that forms a lamellar structure of pearlite) and ferrite in a pearlite structure is controlled, and the cementite is not. Therefore, on this point, the invention of Patent Document 3, and the present invention in which the Si concentration at an interface between proeutectoid cementite that is not cementite in the pearlite structure and ferrite is controlled, differ in structure of interest.
- the cementite in the pearlite structure is essentially different from proeutectoid cementite, and the precipitation starting temperature of proeutectoid cementite is approximately 750°C and is higher than that of pearlite that precipitates at approximately 590 to 650°C. Therefore, it is considered that proeutectoid cementite which is harmful for the wire drawability cannot be sufficiently reduced by the technique of Patent Document 3.
- Patent Document 3 also mentions that it is effective to set a rate of blast cooling after rolling of the wire rod at 1 to 10°C/second so as to efficiently segregate Si to the above-mentioned interface, and blast cooling at approximately 7°C/second is performed in all Examples.
- components in the steel of the steel wire rod according to the present invention are as follows. Unit of each component is % by mass unless otherwise specified.
- Carbon (C) is effective in increasing the strength, and the strength of the steel wire after cold working increases with the increase of the C content.
- the lower limit of the C content is set at 0.90% or more, preferably 0.93% or more, and more preferably 0.95% or more. Any excessive C content, however, cannot achieve sufficient reduction of proeutectoid cementite which is harmful for the wire drawability, thus degrading the wire drawability. Therefore, the upper limit of the C content is set at 1.3% or less, and preferably 1.25% or less.
- Silicon (Si) is an effective deoxidizing agent and has not only the effect of reducing oxide based inclusions in the steel, but also the effect of increasing the strength of the steel wire rod. As mentioned later, Si also has the effect of suppressing the growth of proeutectoid cementite. To effectively exhibit these effects, the lower limit of the Si content is set at 0.4% or more, preferably 0.45% or more, more preferably more than 0.50%, and still more preferably 0.55% or more. Addition of excessive Si accelerates the embrittlement during wire drawing, thus degrading twisting properties of the drawn wire rod. Therefore, the upper limit of the Si content is set at 1.2% or less, and preferably 1.15% or less.
- Manganese (Mn) has the effect of extremely improving the hardenability of the steel, thus lowering the transformation temperature during blast cooling, leading to increased strength of the pearlite structure.
- the lower limit of the Mn content is set at 0.2% or more, and preferably 0.3% or more.
- Mn is an element which easily segregates into the center of the wire rod and addition of excessive Mn excessively enhances the hardenability of a Mn segregation portion, which may form a supercooled structure such as martensite. Therefore, the upper limit of the Mn content is set at 1.5% or less, preferably 1.0% or less, and more preferably 0.95% or less.
- Phosphorus (P) is contained as impurities, and segregates in the prior austenite grain boundary to thereby cause embrittlement, leading to steel billet cracking and degradation of fatigue-resistant characteristics of the steel wire after wire drawing. Therefore, to prevent these harmful influences, the upper limit of the P content is set at 0.02% or less, and preferably 0.018% or less. It is difficult to set the lower limit of the P content at 0% in view of industrial production.
- the upper limit of the S content is set at 0.02% or less, and preferably 0.018% or less. It is difficult to set the lower limit of the S content at 0% in view of industrial production.
- Al more than 0% and 0.008% or less
- Aluminum (Al) is contained as impurities, and forms Al based inclusions such as Al 2 O 3 to thereby increase a wire breakage ratio during wire drawing. Therefore, to ensure sufficient wire drawability, the upper limit of the Al content is set at 0.008% or less, and preferably 0.006% or less. It is difficult to set the lower limit of the Al content at 0% in view of industrial production.
- Titanium (Ti) is contained as impurities, and forms Ti based inclusions such as TiN to thereby increase a wire breakage ratio during wire drawing. Therefore, to ensure sufficient wire drawability, the upper limit of the Ti content is set at 0.005% or less, and preferably 0.003% or less.
- the upper limit of the N content is set at 0.008% or less, and preferably 0.007% or less.
- the steel wire rod of the present invention contains components mentioned above, the balance being iron and inevitable impurities.
- the steel wire rod of the present invention can further include the following selective elements.
- Boron (B) has the effect of concentrating on the austenite grain boundary to thereby prevent the formation of grain boundary ferrite, thus improving the wire drawability.
- B also has the effect of chemically combining with N to form nitrides such as BN, and suppressing the degradation of the toughness due to solid-soluted N, thus improving twisting properties.
- the lower limit of the B content is preferably set at 0.0005% or more. Addition of excessive B causes cracking during hot rolling as a result of the precipitation of a compound with Fe (B-constituent), so that the upper limit of the B content is preferably set at 0.01% or less, and more preferably 0.008% or less.
- Co Cobalt
- the wire drawability is accelerated by adding Co, in addition to Si.
- the lower limit of the Co content is preferably set at 0.05% or more, and more preferably 0.1%.
- the upper limit of the Co content is preferably set at 1.5% or less, more preferably 1.3% or less, and still more preferably 1% or less.
- Vanadium (V) and chromium (Cr) are elements contributing to improve the strength of the steel wire rod. These elements may be added alone or used in combination.
- V has the effect of increasing the strength due to the formation of fine carbonitrides, and also can exhibit the effect of improving twisting properties due to the reduction of solid-soluted N.
- the lower limit of the V content is preferably set at 0.05% or more, and more preferably 0.1% or more.
- V is an expensive element and the effect is saturated even if being added excessively, resulting in economic waste. Therefore, the upper limit of the V content is preferably set at 0.5% or less, and more preferably 0.4% or less.
- the Cr has the effect of making lamellar spacing of pearlite finer to thereby enhance the strength of the steel wire rod.
- the lower limit of the Cr content is preferably set at 0.05% or more, and more preferably 0.1% or more.
- the upper limit of the Cr content is preferably set at 0.5% or less, and more preferably 0.4% or less.
- Cu copper
- MD mechanical descaling
- Nickel (Ni) has the effect of enhancing the corrosion resistance of the steel wire rod.
- the lower limit of the Ni content is preferably set at 0.05% or more. The effect is saturated even if being added excessively, resulting in economic waste. Therefore, the upper limit of the Ni content is preferably set at 0.5% or less, and more preferably 0.4% or less.
- Niobium (Nb) has the effect of making crystal grains finer to thereby enhance the ductility of the wire rod.
- the lower limit of the Nb content is preferably set at 0.05% or more.
- the upper limit of the Nb content is preferably set at 0.5% or less, and more preferably 0.4% or less.
- the steel wire rod of the present invention includes pearlite and proeutectoid cementite, and an area ratio of pearlite is 90% or more relative to the entire structure, a maximum length of proeutectoid cementite is 15 ⁇ m or less, and a concentration difference between an average of the Si concentration inside proeutectoid cementite and a maximum value of the Si concentration inside ferrite (hereinafter may simply referred to as the Si concentration difference) is 0.50 to 3%.
- the steel wire rod of the present invention includes pearlite and proeutectoid cementite. Since the low temperature transformation structure, such as bainite or martensite (may also be referred to as the supercooled structure) inhibits the wire drawability, an area ratio of the pearlite structure is set at 95% or more, so as to ensure sufficient wire drawability.
- the upper limit may be appropriately controlled depending on a relation with proeutectoid cement ite, and is preferably approximately 99 area % or less.
- the steel wire rod of the present invention can include, in addition to pearlite and proeutectoid cementite, the residual structure that is inevitably included during production process.
- the residual structure include non-pearlite structures, such as bainite and proeutectoid ferrite.
- the total content of the non-pearlite structure is preferably controlled to approximately 5 area % or less relative to the entire structure.
- Proeutectoid cementite precipitating in a plate shape is the structure which is harmful for the wire drawability, and disturbs orientation of pearlite colonies of the steel wire rod and increases wire breakage as a starting point of cracking.
- proeutectoid cementite having a short maximum length exert less harmful influences mentioned above.
- Mechanism due to such proeutectoid cementite is as mentioned in detail in Patent Document 1.
- the upper limit of the maximum length of proeutectoid cementite is set at 15 ⁇ m or less, preferably 13 ⁇ m or less, and more preferably 10 ⁇ m or less.
- the lower limit of the maximum length of proeutectoid cementite is not particularly limited and may be, for example, approximately 0.1 ⁇ m.
- Silicon (Si) is an element which is hardly solid-soluted in cementite and is discharged to an austenite phase from a cementite phase when proeutectoid cementite precipitates, and Si concentration difference is generated at the interface (interface between proeutectoid cementite and a ferrite phase).
- the test results of the inventors revealed that, the more this Si concentration difference is large, the more the growth of a proeutectoid cementite phase is suppressed, thus enabling the reduction of the maximum length of proeutectoid cementite.
- Si concentration distribution formed at this time is inherited even through subsequent pearlite transformation, so that observation of the structure of the thus produced steel wire rod leads to confirmation as an Si concentration difference at an interface between the proeutectoid cementite phase and the ferrite phase around the proeutectoid cementite phase.
- a graph showing an Si concentration difference in the sample of test No. 12 in Table 2 of Example mentioned later is shown in Fig. 1 .
- Fig. 1 an average of the Si concentration of the proeutectoid cementite phase in the center, and a maximum value of the Si concentration of each ferrite phase existing around the proeutectoid cementite phase are measured, and a difference therebetween is defined as the Si concentration difference.
- the method for measuring the Si concentration will be mentioned in detail in the columns of Examples mentioned later.
- the Si concentration difference calculated as mentioned above is set at 0.50% or more.
- the maximum length of proeutectoid cementite can be set at 15 ⁇ m or less.
- the Si concentration difference is preferably 0.6% or more. The effect mentioned above is saturated even if the Si concentration difference is excessively formed, so that the upper limit is set at 3% or less, and preferably 2.8% or less.
- the Si concentration difference is generated at an interface between the proeutectoid cementite phase and ferrite in the pearlite structure, and the Si concentration difference is not generated at an interface between the proeutectoid cementite phase and the cementite (lamellar cementite that forms a lamellar structure of pearlite) phase in the pearlite structure.
- the high-carbon steel wire rod as mentioned in the present invention is generally produced by the following procedure in which a steel billet with a predetermined chemical component adjusted in advance is austenitized by heating and then hot-rolled into a steel wire rod having a predetermined wire diameter.
- the placing temperature is preferably set at 880 to 980°C.
- the placing temperature is preferably 900°C or higher and 960°C or lower.
- cooling is started at a temperature of 800°C or higher.
- the cooling conditions are extremely important so as to control the desired Si concentration difference within a predetermined range. There is a need that the entire coil placed in a ring shape falls within the above-mentioned range of the cooling stop temperature and holding temperature.
- cooling is performed to the cooling stop temperature of 480 to 620°C at an average cooling rate of 12 to 60°C/s.
- the average cooling rate is low, the Si concentration difference generated at a proeutectoid cementite interface is lost by diffusion of Si atoms, thus failing to obtain the desired Si concentration difference.
- the average cooling rate is high, a supercooled structure is formed and a pearlite area ratio becomes less than 90%.
- the average cooling rate is more preferably 15°C/s or more and 55°C/s or less.
- the cooling stop temperature is more preferably 500°C or higher and 600°C or lower.
- the temperature is raised to the holding temperature of 590 to 650°C and pearlite transformation is performed.
- the holding temperature is too high, Si atoms diffuse to thereby decrease the Si concentration difference. Meanwhile, when the holding temperature is too low, a supercooled structure is generated to thereby decrease the pearlite area ratio.
- the holding temperature is more preferably 600°C or higher and 640°C or lower.
- the steel wire rod of the present invention was obtained by the procedure mentioned above, and then coiled into a coil shape to obtain a wire rod coil. Then, wire drawing is performed to obtain a steel wire having desired wire diameter and strength.
- a patenting treatment is preferably performed after wire drawing.
- An extra fine steel wire having a wire diameter of approximately 0.2 mm can be obtained by further subjecting to wire drawing after the patenting treatment.
- conditions of the patenting treatment There is no particular limitation on conditions of the patenting treatment and, for example, it is possible to employ conditions such as heating temperature of 950°C and patenting temperature of 600°C.
- the patenting treatment may be performed not only once, but also plural times (for example, 2 to 3 times).
- the thus obtained steel wire of the present invention has a high tensile strength such as approximately 4,000 MPa or more.
- a steel wire having a wire diameter of approximately 0.1 to 0.4 mm is obtained, so that the thus obtained steel wire is suitably used for steel cords, wire ropes, saw wires and the like.
- Each of steels A to Z (cross-sectional shape: 155 mm ⁇ 155 mm) shown in Table 1 was heated to a temperature of 1,000°C and hot-rolled into a predetermined wire diameter of 5.5 mm. Then, the hot-rolled steel was placed in a ring shape on a cooling conveyor and allowed to undergo pearlite transformation while control cooling by blast cooling, and then coiled into a coil shape to obtain a coil of rolled material.
- the cooling conditions after rolling and the wire rod diameter after rolling are shown in Table 2.
- the point counting method is a method in which the micrograph is sectioned into meshes and the number of structures existing in lattice points is counted to thereby easily determine an area ratio of the structure.
- a micrograph of the center of the transverse section was taken at a magnification of 4,000 times to fabricate three SEM micrographs.
- the each micrograph was sectioned into 100 lattice points and a pearlite area ratio was determined, and then an average was calculated.
- An evaluation area of one SEM micrograph is 868 ⁇ m 2 .
- the pearlite area ratio and details of the structure in each specimen are shown in Table 2.
- the non-pearlite structure detected by the above point counting method (proeutectoid cementite structure, bainite structure) are also shown in Table 2.
- P denotes a pearlite structure
- B denotes a bainite structure
- ⁇ denotes proeutectoid cementite.
- one ring was collected from the coil end of the non-defective product and then divided into eight samples in a longitudinal direction.
- a tensile test was performed and a tensile strength TS was measured. An average of the tensile strength of eight samples in total was determined, and then TS of the coil of rolled material was calculated.
- the samples of tests Nos. 1 to 3, 11-12, 14-19, 21, and 24 to 32 are examples that satisfy the requirements of the present invention, and satisfactory wire drawability was confirmed without causing wire breakage.
- all samples of tests Nos. 3, 11 to 14, 16 to 18, 20, and 21 in which steels C to G, I to K, M, and N, each containing B, in Table 1 are used wire drawing could be performed to high wire drawing strain without causing wire breakage.
- wire drawing could be performed to higher wire drawing strain range (2.13 or more).
- Test No. 13 and 20 have a pearlite area ratio outside of the ratio defined in present claim 1.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2015070095 | 2015-03-30 | ||
JP2015188843 | 2015-09-25 | ||
PCT/JP2016/060019 WO2016158901A1 (ja) | 2015-03-30 | 2016-03-29 | 伸線性に優れた高炭素鋼線材、および鋼線 |
Publications (3)
Publication Number | Publication Date |
---|---|
EP3282027A1 EP3282027A1 (en) | 2018-02-14 |
EP3282027A4 EP3282027A4 (en) | 2018-09-05 |
EP3282027B1 true EP3282027B1 (en) | 2020-10-21 |
Family
ID=57006008
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP16772782.5A Active EP3282027B1 (en) | 2015-03-30 | 2016-03-29 | High-carbon steel wire material with excellent wire drawability, and steel wire |
Country Status (8)
Country | Link |
---|---|
US (1) | US20180087125A1 (ja) |
EP (1) | EP3282027B1 (ja) |
JP (1) | JP6795319B2 (ja) |
KR (1) | KR20170130527A (ja) |
CN (1) | CN107406950B (ja) |
CA (1) | CA2980886C (ja) |
ES (1) | ES2835325T3 (ja) |
WO (1) | WO2016158901A1 (ja) |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
TWI658472B (zh) * | 2017-04-28 | 2019-05-01 | 吳政雄 | 複合導電體結合之電導體及其製造方法 |
JP6922726B2 (ja) * | 2017-12-26 | 2021-08-18 | 日本製鉄株式会社 | 熱間圧延線材 |
KR102534998B1 (ko) | 2018-10-16 | 2023-05-26 | 닛폰세이테츠 가부시키가이샤 | 열간 압연 선재 |
CN112176258B (zh) * | 2020-09-30 | 2022-06-21 | 江苏省沙钢钢铁研究院有限公司 | 2500MPa级钢绞线用盘条及其制造方法 |
CN113293337A (zh) * | 2021-04-28 | 2021-08-24 | 顿口渔具科技(东莞)有限公司 | 一种鱼钩用铌-钒复合微合金化高碳钢丝 |
CN117858973A (zh) * | 2021-08-11 | 2024-04-09 | 浦项股份有限公司 | 高强度高韧性钢板及其制造方法 |
Family Cites Families (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2001181789A (ja) * | 1999-12-22 | 2001-07-03 | Nippon Steel Corp | 伸線加工性に優れた細径高炭素鋼熱間圧延線材 |
JP4003450B2 (ja) * | 2001-12-13 | 2007-11-07 | 住友金属工業株式会社 | 鋼線材、鋼線及びその製造方法 |
JP4016894B2 (ja) * | 2003-06-12 | 2007-12-05 | 住友金属工業株式会社 | 鋼線材及び鋼線の製造方法 |
JP4621133B2 (ja) * | 2004-12-22 | 2011-01-26 | 株式会社神戸製鋼所 | 伸線性に優れた高炭素鋼線材およびその製法 |
JP4374357B2 (ja) * | 2005-06-29 | 2009-12-02 | 新日本製鐵株式会社 | 伸線特性に優れた高強度線材及びその製造方法、並びに伸線特性に優れた高強度鋼線 |
JP2007327084A (ja) * | 2006-06-06 | 2007-12-20 | Kobe Steel Ltd | 伸線加工性に優れた線材およびその製造方法 |
JP4970562B2 (ja) * | 2009-04-21 | 2012-07-11 | 新日本製鐵株式会社 | 延性に優れた高強度鋼線用線材及び鋼線の製造方法 |
KR101318009B1 (ko) * | 2010-02-01 | 2013-10-14 | 신닛테츠스미킨 카부시키카이샤 | 선재, 강선 및 그들의 제조 방법 |
CN102791900B (zh) * | 2010-04-01 | 2016-11-09 | 株式会社神户制钢所 | 拉丝加工性和拉丝后的疲劳特性优异的高碳钢线材 |
EP2557191B1 (en) * | 2010-04-08 | 2016-07-27 | Nippon Steel & Sumitomo Metal Corporation | Wire material for saw wire and method for producing same |
JP5802162B2 (ja) * | 2012-03-29 | 2015-10-28 | 株式会社神戸製鋼所 | 線材及びこれを用いた鋼線 |
-
2016
- 2016-03-29 WO PCT/JP2016/060019 patent/WO2016158901A1/ja active Application Filing
- 2016-03-29 JP JP2016064791A patent/JP6795319B2/ja not_active Expired - Fee Related
- 2016-03-29 ES ES16772782T patent/ES2835325T3/es active Active
- 2016-03-29 CA CA2980886A patent/CA2980886C/en not_active Expired - Fee Related
- 2016-03-29 EP EP16772782.5A patent/EP3282027B1/en active Active
- 2016-03-29 CN CN201680019334.0A patent/CN107406950B/zh not_active Expired - Fee Related
- 2016-03-29 KR KR1020177030428A patent/KR20170130527A/ko not_active Application Discontinuation
- 2016-03-29 US US15/562,441 patent/US20180087125A1/en not_active Abandoned
Non-Patent Citations (1)
Title |
---|
None * |
Also Published As
Publication number | Publication date |
---|---|
ES2835325T3 (es) | 2021-06-22 |
CN107406950B (zh) | 2020-04-14 |
CA2980886C (en) | 2019-09-24 |
WO2016158901A1 (ja) | 2016-10-06 |
CN107406950A (zh) | 2017-11-28 |
US20180087125A1 (en) | 2018-03-29 |
JP6795319B2 (ja) | 2020-12-02 |
CA2980886A1 (en) | 2016-10-06 |
EP3282027A4 (en) | 2018-09-05 |
EP3282027A1 (en) | 2018-02-14 |
JP2017061740A (ja) | 2017-03-30 |
KR20170130527A (ko) | 2017-11-28 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP3282027B1 (en) | High-carbon steel wire material with excellent wire drawability, and steel wire | |
EP2083094B1 (en) | High-strength steel wire excelling in ductility and process for producing the same | |
EP3015563B1 (en) | High-carbon steel wire rod and method for manufacturing same | |
EP2175043B1 (en) | Steel rod and high strenght steel wire having superior ductility and methods of production of the same | |
EP1897964B1 (en) | High-strength wire rod excelling in wire drawing performance and process for producing the same | |
EP1900837A1 (en) | High-strength wire rod excelling in wire drawing performance and process for producing the same | |
JP6180351B2 (ja) | 生引き性に優れた高強度鋼線用線材および高強度鋼線 | |
EP3366802A1 (en) | Steel wire for wire drawing | |
EP2832878B1 (en) | Wire rod and steel wire using same | |
KR20130034045A (ko) | 특수강 강선 및 특수강 선재 | |
WO2008044354A1 (fr) | Fil machine à résistance élevée présentant une excellente aptitude au tréfilage et procédé de fabrication de celui-ci | |
US10487379B2 (en) | High-carbon steel wire rod with excellent wire drawability | |
CN113748224B (zh) | 线材 | |
JP2004091912A (ja) | 鋼線材とその製造法及び当該鋼線材を用いる鋼線の製造法 | |
US20190024222A1 (en) | Steel wire for non-heat treated machine part and non-heat treated machine part | |
EP3378964A1 (en) | Wire rod for steel wire, and steel wire | |
EP3492616A1 (en) | High strength steel wire | |
EP3486345A1 (en) | Steel wire | |
EP3115478B1 (en) | High-carbon steel wire having superior wire drawing properties and method for producing same | |
CN108368583B (zh) | 非调质机械部件用钢丝及非调质机械部件 | |
JP5945196B2 (ja) | 高強度鋼線用線材 | |
WO2020080415A1 (ja) | 熱間圧延線材 | |
EP3165623A1 (en) | Wire material for steel wire, and steel wire | |
JP4527913B2 (ja) | 高強度高炭素鋼線用線材及びその製造方法 | |
JP6922726B2 (ja) | 熱間圧延線材 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE |
|
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 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE |
|
17P | Request for examination filed |
Effective date: 20170928 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
AX | Request for extension of the european patent |
Extension state: BA ME |
|
DAV | Request for validation of the european patent (deleted) | ||
DAX | Request for extension of the european patent (deleted) | ||
A4 | Supplementary search report drawn up and despatched |
Effective date: 20180803 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: B21C 1/02 20060101ALI20180730BHEP Ipc: B21C 1/00 20060101ALI20180730BHEP Ipc: C22C 38/54 20060101ALI20180730BHEP Ipc: C22C 38/16 20060101ALI20180730BHEP Ipc: C22C 38/08 20060101ALI20180730BHEP Ipc: C22C 38/14 20060101ALI20180730BHEP Ipc: C21D 9/52 20060101ALI20180730BHEP Ipc: C22C 38/28 20060101ALI20180730BHEP Ipc: C22C 38/04 20060101ALI20180730BHEP Ipc: C22C 38/06 20060101ALI20180730BHEP Ipc: C22C 38/32 20060101ALI20180730BHEP Ipc: C22C 38/02 20060101ALI20180730BHEP Ipc: C21D 6/00 20060101ALI20180730BHEP Ipc: C22C 38/30 20060101ALI20180730BHEP Ipc: C21D 8/06 20060101ALI20180730BHEP Ipc: C22C 38/00 20060101AFI20180730BHEP Ipc: C22C 38/24 20060101ALI20180730BHEP |
|
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: 20190503 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R079 Ref document number: 602016046308 Country of ref document: DE Free format text: PREVIOUS MAIN CLASS: C22C0038000000 Ipc: C21D0006000000 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C21D 9/52 20060101ALI20200323BHEP Ipc: C22C 38/32 20060101ALI20200323BHEP Ipc: C22C 38/14 20060101ALI20200323BHEP Ipc: B21C 1/00 20060101ALI20200323BHEP Ipc: C22C 38/06 20060101ALI20200323BHEP Ipc: C21D 8/06 20060101ALI20200323BHEP Ipc: C22C 38/24 20060101ALI20200323BHEP Ipc: C22C 38/08 20060101ALI20200323BHEP Ipc: C21D 9/46 20060101ALI20200323BHEP Ipc: C22C 38/16 20060101ALI20200323BHEP Ipc: C22C 38/00 20060101ALI20200323BHEP Ipc: C22C 38/30 20060101ALI20200323BHEP Ipc: C21D 6/00 20060101AFI20200323BHEP Ipc: C22C 38/04 20060101ALI20200323BHEP Ipc: C21D 9/64 20060101ALI20200323BHEP Ipc: C22C 38/28 20060101ALI20200323BHEP Ipc: C22C 38/54 20060101ALI20200323BHEP Ipc: C22C 38/02 20060101ALI20200323BHEP |
|
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 38/08 20060101ALI20200403BHEP Ipc: C21D 9/46 20060101ALI20200403BHEP Ipc: C21D 9/64 20060101ALI20200403BHEP Ipc: C22C 38/04 20060101ALI20200403BHEP Ipc: C22C 38/10 20060101ALI20200403BHEP Ipc: C21D 8/06 20060101ALI20200403BHEP Ipc: C22C 38/16 20060101ALI20200403BHEP Ipc: C22C 38/14 20060101ALI20200403BHEP Ipc: C22C 38/18 20060101ALI20200403BHEP Ipc: C22C 38/28 20060101ALI20200403BHEP Ipc: C22C 38/02 20060101ALI20200403BHEP Ipc: C22C 38/00 20060101ALI20200403BHEP Ipc: C22C 38/24 20060101ALI20200403BHEP Ipc: C22C 38/12 20060101ALI20200403BHEP Ipc: B21C 1/00 20060101ALI20200403BHEP Ipc: C21D 6/00 20060101AFI20200403BHEP Ipc: C22C 38/06 20060101ALI20200403BHEP Ipc: C21D 9/52 20060101ALI20200403BHEP Ipc: C22C 38/32 20060101ALI20200403BHEP Ipc: C22C 38/30 20060101ALI20200403BHEP |
|
INTG | Intention to grant announced |
Effective date: 20200512 |
|
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): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602016046308 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: AT Ref legal event code: REF Ref document number: 1325943 Country of ref document: AT Kind code of ref document: T Effective date: 20201115 |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: T3 Ref document number: E 36019 Country of ref document: SK |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 1325943 Country of ref document: AT Kind code of ref document: T Effective date: 20201021 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20201021 |
|
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: 20201021 Ref country code: NO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20210121 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: 20210222 Ref country code: RS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201021 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: 20201021 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: 20210122 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20210311 Year of fee payment: 6 |
|
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: 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: 20201021 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: 20201021 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: 20210121 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: 20201021 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: 20201021 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: 20210221 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20210317 Year of fee payment: 6 Ref country code: TR Payment date: 20210203 Year of fee payment: 6 Ref country code: BE Payment date: 20210218 Year of fee payment: 6 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2835325 Country of ref document: ES Kind code of ref document: T3 Effective date: 20210622 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: HR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201021 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SK Payment date: 20210325 Year of fee payment: 6 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602016046308 Country of ref document: DE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: RO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201021 Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201021 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: 20201021 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: 20201021 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: 20201021 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20210331 Year of fee payment: 6 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201021 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: ES Payment date: 20210405 Year of fee payment: 6 |
|
26N | No opposition filed |
Effective date: 20210722 |
|
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: 20201021 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: 20201021 Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201021 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
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: 20201021 |
|
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: 20210329 Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210329 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210331 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210331 |
|
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: 20210221 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R119 Ref document number: 602016046308 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: MM4A Ref document number: E 36019 Country of ref document: SK Effective date: 20220329 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20220329 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20220331 |
|
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 NON-PAYMENT OF DUE FEES Effective date: 20220329 Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20220329 Ref country code: FR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20220331 Ref country code: DE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20221001 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20220331 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 20230504 |
|
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: 20201021 |
|
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: 20160329 Ref country code: ES Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20220330 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201021 |