EP2455499A1 - Process for production of cold-rolled steel sheet having excellent press moldability, and cold-rolled steel sheet - Google Patents
Process for production of cold-rolled steel sheet having excellent press moldability, and cold-rolled steel sheet Download PDFInfo
- Publication number
- EP2455499A1 EP2455499A1 EP10796868A EP10796868A EP2455499A1 EP 2455499 A1 EP2455499 A1 EP 2455499A1 EP 10796868 A EP10796868 A EP 10796868A EP 10796868 A EP10796868 A EP 10796868A EP 2455499 A1 EP2455499 A1 EP 2455499A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel sheet
- cold
- rolled steel
- rolling
- hot
- 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
Links
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 59
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 32
- 238000000034 method Methods 0.000 title claims description 6
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 120
- 239000010959 steel Substances 0.000 claims abstract description 120
- 238000005097 cold rolling Methods 0.000 claims abstract description 37
- 238000000137 annealing Methods 0.000 claims abstract description 24
- 238000005096 rolling process Methods 0.000 claims abstract description 19
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 239000000203 mixture Substances 0.000 claims abstract description 15
- 238000002791 soaking Methods 0.000 claims abstract description 13
- 238000005554 pickling Methods 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 230000001965 increasing effect Effects 0.000 description 20
- 238000005098 hot rolling Methods 0.000 description 18
- 229910052748 manganese Inorganic materials 0.000 description 11
- 229910052759 nickel Inorganic materials 0.000 description 11
- 229910000734 martensite Inorganic materials 0.000 description 9
- 238000004804 winding Methods 0.000 description 9
- 230000000694 effects Effects 0.000 description 7
- 239000004973 liquid crystal related substance Substances 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 239000002994 raw material Substances 0.000 description 5
- 239000013078 crystal Substances 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000005496 tempering Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 3
- 230000002708 enhancing effect Effects 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 230000001939 inductive effect Effects 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- JXDXANRCLTZYDP-UHFFFAOYSA-N 2-[3-(1,4-diazepan-1-ylmethyl)-4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]pyrazol-1-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound N1(CCNCCC1)CC1=NN(C=C1C=1C=NC(=NC=1)NC1CC2=CC=CC=C2C1)CC(=O)N1CC2=C(CC1)NN=N2 JXDXANRCLTZYDP-UHFFFAOYSA-N 0.000 description 1
- ZYPDJSJJXZWZJJ-UHFFFAOYSA-N 2-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-3-piperidin-4-yloxypyrazol-1-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C=1C(=NN(C=1)CC(=O)N1CC2=C(CC1)NN=N2)OC1CCNCC1 ZYPDJSJJXZWZJJ-UHFFFAOYSA-N 0.000 description 1
- WTFUTSCZYYCBAY-SXBRIOAWSA-N 6-[(E)-C-[[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]piperazin-1-yl]methyl]-N-hydroxycarbonimidoyl]-3H-1,3-benzoxazol-2-one Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)N1CCN(CC1)C/C(=N/O)/C1=CC2=C(NC(O2)=O)C=C1 WTFUTSCZYYCBAY-SXBRIOAWSA-N 0.000 description 1
- AFCARXCZXQIEQB-UHFFFAOYSA-N N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CCNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 AFCARXCZXQIEQB-UHFFFAOYSA-N 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000007739 conversion coating Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009713 electroplating Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- AYOOGWWGECJQPI-NSHDSACASA-N n-[(1s)-1-(5-fluoropyrimidin-2-yl)ethyl]-3-(3-propan-2-yloxy-1h-pyrazol-5-yl)imidazo[4,5-b]pyridin-5-amine Chemical compound N1C(OC(C)C)=CC(N2C3=NC(N[C@@H](C)C=4N=CC(F)=CN=4)=CC=C3N=C2)=N1 AYOOGWWGECJQPI-NSHDSACASA-N 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0006—Details, accessories not peculiar to any of the following furnaces
-
- 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
- C21D9/0037—Rotary furnaces with vertical axis; Furnaces with rotating floor
-
- 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
- C22C38/06—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Definitions
- the present invention relates to a method of manufacturing a cold-rolled steel sheet having excellent press formability and a cold-rolled steel sheet manufactured by the manufacturing method.
- liquid crystal frame parts used in a mobile phone or a notebook-type personal computer gasket parts for an automobile engine and the like are formed by a cold press. Accordingly, a thin cold-rolled steel sheet which is used for forming these parts is required to have press formability. Further, with respect to parts of an electronic device represented by a notebook-type personal computer, a mobile phone or a digital camera or parts such as a gasket for an automobile engine, these parts are required to satisfy a demand for the reduction of weight and the miniaturization. To realize the reduction of weight and for the miniaturization of these parts, it is necessary to make a steel sheet thin.
- patent document 2 proposes a cold-rolled steel sheet for a gasket material having excellent spring property which is manufactured in such a manner where a steel sheet is heated at a recrystallization temperature or above in continuous annealing, is annealed after soaking, and is subjected to secondary cold rolling.
- the high-strength steel sheets which are disclosed in patent document 1 and patent document 2 aim for the acquisition of high strength so that ductility is lowered and cracks occur at the time of press forming thus giving rise to a drawback that press formability is low. Further, to realize a thin gauge at the time of cold-rolling a high-strength hot-rolled steel sheet, a load at the time of coldrolling is increased thus giving rise to a drawback that productivity is impeded due to lowering of operability and the increase of a yield loss.
- the present invention has been made to overcome the above-mentioned drawbacks, and it is an object of the present invention to provide a cold-rolled steel sheet which undergoes a small load at the time of cold-rolling, has excellent press formability and has high strength, and a method of manufacturing the cold-rolled steel sheet.
- a cold-rolled steel sheet which undergoes a small load at the time of cold-rolling, and has excellent press formability while ensuring high strength and ductility.
- a cold-rolled steel sheet of the present invention it is also possible to provide a cold-rolled steel sheet having both strength and formability which has a thickness of 0.05 mm to 0.6 mm, a tensile strength of 1280 MPa or more, and breaking elongation of 3 % or more, wherein these are conditions which a raw material used for manufacturing a gasket of a gasoline engine for an automobile, a liquid crystal frame or a frame part of a notebook-type personal computer, a mobile phone and a digital camera or the like is required to have.
- the composition of hot-rolled steel sheet is set to the following range by mass%.
- C 0.10 to 0.30, Mn: 0.2 or more, Ni: 0.01 or more, Mn+Ni: 05 to 2.5, Cr: 1.2 to 9.0, balance: Fe and unavoidable elements.
- C is an important element for forming the low-temperature transformed structure such as martensite in the steel sheet such that the steel sheet acquires high tensile strength. When the content of C is extremely small, the required tensile strength cannot be acquired and hence, a lower limit of the content of C is set to 0.10.
- an upper limit of the content of C is set to 0.30.
- the content of C is more preferably set to a value which falls within a range from 0.15 to 0.25.
- both Mn and Ni are elements which enhance hardenability and form the low-temperature transformed structure at the time of continuous annealing, and Mn and Ni impart high tensile strength to a cold-rolled steel sheet to which continuous annealing is applied.
- a lower limit of the total amount of content of Mn and Ni is set to 0.5.
- an upper limit of the total amount of content of Mn and Ni is set to 2.5.
- the steel sheet it is necessary for the steel sheet to contain 0.20 or more of Mn since Mn prevents red heat caused by S which is an impurity, and it is necessary to add 0.01 or more of Ni to the steel sheet since Ni ensures toughness of the steel sheet after heat treatment. Since Ni is expensive, it is advantageous to adjust the total amount of content of Mn and Ni by adjusting the content of Mn in view of cost.
- Cr is also an element which can enhance hardenability, and Cr forms the low-temperature transformed structure at the time of continuous annealing so that the steel sheet can acquire high tensile strength.
- a lower limit of the content of Cr is set to 1.2.
- an upper limit of the content of Cr is set to 9.0.
- the content of Cr is more preferably set to a value which falls within a range from 2.0 to 5.5.
- Si is an element effective for greatly increasing strength of a cold-rolled steel sheet.
- the larger content of Si the more easily the obj ect canbe achieved.
- an upper limit value of the content of Si is set to 2.0 %.
- P is a component which makes crystal grains fine and hence, it is desirable to add a fixed amount of P to the steel sheet for enhancing strength of a cold-rolled steel sheet.
- P also causes segregation in a crystal grain boundary thus inducing brittleness of the steel sheet. Accordingly, the content of P is set to 0.06 % or less.
- S is an impurity component which generates red-brittleness during hot rolling and hence, it is desirable that the steel sheet contains as little S as possible.
- the red-brittleness caused by a small amount of residual S can be alleviated by Mn and hence, an upper limit value of the content of S is set to 0.06 %.
- a fixed amount of Cu may be added to the steel sheet for enhancing the strength of a steel sheet by solid solution strengthening or by precipitation strengthening.
- an upper limit of Cu is set to 0.5 %.
- Al is added to a steel bath as a deoxidizing agent in making steel. Al reacts with solid solution N and segregates as AIN thus contributing to making the crystal grain fine. On the other hand, when the content of Al exceeds 0.10 %, the solidification of N becomes conspicuous thus lowering solid solution strengthening brought about by N and hence, the content of Al is set to 0.10 % or less.
- the addition of Ti is effective for making the crystal grain fine, for suppressing a grain growth, for enhancing corrosion resistance and the like.
- the content of Ti added to the steel sheet is excessively large, the advantageous effect is saturated and hence, the content of Ti is set to 0.30 % or less.
- N is , in the same manner as C and Mn, a component necessary for imparting high strength to a cold-rolled steel sheet and for increasing durability of the cold-rolled steel sheet.
- setting the content of N to less than 0.002 % is difficult in terms of making steel.
- the addition of the content of N which exceeds 0.015 % remarkably lowers a yield rate of ferro-nitride at the time of making steel thus making the steel sheet unstable, and also remarkably deteriorates anisotropy of the steel sheet at the time of press forming.
- cracks occur on a surface of a continuously-cast slab and the cracks become a defect in casting. Accordingly, the content of N is desirably set to 0.015 % or less in the present invention.
- Raw materials are melted in a converter or an electric furnace to produce molten steel and molten steel is cast for producing a slab whose composition is adjusted to the above-mentioned range.
- a slab whose components are adjusted to the above-mentioned range is formed into a steel sheet having a sheet thickness of 1.2 to 3.0 mm by hot-rolling.
- a load at the time of hot-rolling is increased. Accordingly, a lower limit of the sheet thickness is set to 1.2.
- a load at the time of cold-rolling which is performed after hot-rolling is increased. Accordingly, an upper limit of the sheet thickness is set to 3.0.
- a heat temperature of the slab having the above-mentioned composition is set to 1100 °C or above, and a coiling temperature (CT) is set to 600 °C or above.
- CT coiling temperature
- the heating temperature of the slab is below 1100 °C, the positive decomposition solid solution of N becomes insufficient and a load at the time of hot-rolling is increased. Accordingly, such a heating temperature is not preferable.
- the winding temperature is set to a value which falls within a range from 600 °C to 800 °C. When the winding temperature is low, strength of the hot-rolled steel sheet is largely increased so that such a steel sheet is not preferable for cold-rolling. Accordingly, a lower limit of the winding temperature is set to 600°C.
- the hot-rolled steel sheet which is manufactured under the above-mentioned condition may have a tensile strength of 1000 MPa or less. This is because when tensile strength of the hot-rolled steel sheet exceeds 1000 MPa, a rolling load at the time of cold rolling is increased so that the tensile strength exceeding 1000 MPa is not preferable.
- Scales generated on a surface of the steel sheet at the time of hot-rolling are removed in an acid bath in accordance with a normal method and, thereafter, the steel sheet is subjected to cold-rolling and continuous annealing.
- Cold-rolling is applied to the steel sheet once or several times at a rolling reduction of 60 % or more in total until the steel sheet, as a product, acquires a predetermined product thickness of 0.05 to 0.6 mm. This is because when the product thickness becomes 0.05 mm or less, rigidity of the steel sheet is lowered so that there may be a case where when the steel sheet is used for manufacturing products such as a gasket of a gasoline engine of an automobile, a liquid crystal frame or a frame part of a notebook-type personal computer, a mobile phone and a digital camera, the shape of the product is liable to be deformed and hence, the product cannot be manufactured.
- products such as a gasket of a gasoline engine of an automobile, a liquid crystal frame or a frame part of a notebook-type personal computer, a mobile phone and a digital camera
- the product thickness becomes 0.6 mm or more
- a product such as a gasket of a gasoline engine of an automobile, a liquid crystal frame or a frame part of anotebook-typepersonal computer, a mobile phone and a digital camera
- a weight of the product becomes larger than a designed value or the miniaturization of the product cannot be realized.
- an upper limit of the total rolling reduction in cold-rolling is not particularly limited, the upper limit of the total rolling reduction is set to 98 %. Further, by applying continuous annealing at a temperature of 500 °C or above or batch annealing at a temperature of 500 °C or above to the steel sheet after cold-rolling, the rolled sheet which is hardened by work hardening is softened so that cold-rolling can be applied to the steel sheet again.
- a method of cold-rolling and the number of times that cold-rolling is performed are not particularly designated, and the method and the number of times that cold-rolling is performed can be suitably selected in accordance with a target sheet thickness.
- Continuous annealing is applied to the steel sheet for removing strains in the sheet generated at the time of cold-rolling.
- cold-rolling is performed plural times, continuous annealing can be performed in each cold-rolling.
- the steel sheet is soaked and held at a soaking temperature of 750°C or above for 1 second or more and 100 seconds or less.
- a temperature of the steel sheet does not exceed an Ae3 transformation temperature and hence, the steel sheet cannot acquire sufficient tensile strength.
- an upper limit of the soaking temperature is set to 1000°C.
- a part or the entire steel sheet is formed into austenite by heating the steel sheet and, thereafter, these parts are transformed into martensite or the like by cooling after such heating.
- the steel sheet can acquire a predetermined strength.
- the steel sheet After the steel sheet is soaked and held at a soaking temperature of 750°C or above for 1 second or more and 100 seconds or less, the steel sheet is cooled at a cooling rate of 3°C/s to 100°C/s. Due to such cooling, the austenite structure of the steel sheet is formed into structures such as martensite, tempered martensite and bainite. When the cooling rate is 3°C/s or less, the formation of the low-temperature transformed structure such as martensite becomes insufficient and hence, the steel sheet cannot acquire sufficient strength. On the other hand, when the cooling rate exceeds 100°C/s, although the steel sheet can acquire required strength, a shape of the steel sheet is deteriorated and hence, such a steel sheet is not preferable for press application.
- a steel sheet is cooled at a cooling rate which is remarkably slow compared with a cooling rate for general quenching using water or the like which is performed for ensuring a shape so that the low-temperature transformed structure is formed and thereby a high strength steel sheet is acquired.
- Mn and Ni which are effective austenite stabilizing elements used as general quenching elements, it is necessary to add a considerable amount of Mn and Ni to the steel sheet to acquire a required strength at the above-mentioned cooling rate.
- the addition of a considerable amount of Mn and Ni to the steel sheet largely increases strength of the steel sheet after hot-rolling so that a load at the time of cold-rolling is increased whereby productivity is impeded thus inducing an increase in product cost.
- the content of Mn and the content of Ni are set relatively small, and Cr which is a ferrite stabilizing element is added to the steel sheet so as to form a composite and hence, it is possible to make the steel sheet relatively soft after hot-rolling and to manufacture a high-strength steel sheet by continuous annealing which is performed after cold-rolling whereby a load in the manufacture of the steel sheet can be significantly reduced.
- tempering treatment below 600 °C may be applied to the steel sheet after the steel sheet is cooled after final continuous annealing.
- the steel sheet is formed into the quenched structure at a relatively low cooling rate and hence, an effect substantially equal to an effect obtained by tempering treatment can be acquired at the time of cooling whereby the tempering step can be omitted.
- the omission of the tempering step largely contributes to the reduction of a load in the manufacture of the steel sheet.
- tensile strength of a cold-rolled steel sheet acquired by the manufacturing method of the present invention can be increased to 1280 MPa or more. Since the cold-rolled steel sheet has such strength, when the cold-rolled steel sheet is used for manufacturing a gasket of a gasoline engine of an automobile, there is no possibility that a gas leak will occur. Further, when a sheet thickness of the cold-rolled steel sheet is made small for reduction of weight and the cold-rolled steel sheet is used for manufacturing a liquid crystal frame or frame parts of a notebook-type personal computer, a mobile phone, or a digital camera, and particularly when the cold-rolled steel sheet is used inmobile applications, theseparts can ensure the required rigidity as the parts.
- breaking elongation of a cold-rolled steel sheet can be set to 3 % or more.
- a value of breaking elongation indicative of ductility is important when a cold-rolled steel sheet is press-formed for manufacturing products such as gaskets for an automobile engine and electronic parts.
- breaking elongation is less than 3 %, cracks are liable to occur inportions which are subjected to some degree of bulging forming, bending at 90° or the like.
- a steel sheet manufactured by the above-mentioned manufacturing method has the structure formed of martensite, tempered martensite, bainite structure and the like by a volume% of 60 % or more, has high tensile strength of 1280 MPa or more, and ensures ductility.
- the steel sheet obtained in this manner is, whennecessary, subjected to temper rolling for surface roughness adjustment or subjected to electro plating and chemical conversion coating using Zn, Ni or the like for rust prevention.
- the steel sheet obtained by the manufacturing method of the present invention can be used as a raw material for press forming.
- the steel sheet obtained by the manufacturing method of the present invention largely differs from a generally-used cold-rolled steel sheet in a strength range and hence, it is necessary to take into account spring-back or the like.
- slabs having compositions corresponding to specimens 1 to 18 shown in Table 1 are prepared.
- the specimens 1 to 11, 17, 18 are slabs having the compositions which fall within a composition range of the present invention, while the specimens 12 to 16 are slabs which do not fall within the composition range of the present invention.
- hot-rolling step the slabs which are adjusted to the compositions corresponding to specimens 1 to 18 are heated at a temperature of 1230 °C, and hot-rolled steel sheets having a sheet thickness of 2.0 mm are manufactured at winding temperatures shown in Table 2. Properties of these hot-rolled steel sheets are shown in Table 2.
- the hot-rolled steel sheets are cold-rolled to a thickness of 0.5 mm. Thereafter, inacontinuousannealingstep, thecold-rolled steel sheets are soaked and held at a soaking temperature of 900 °C for 20 seconds and, thereafter, the cold-rolled steel sheets are cooled at a cooling rate of 20 °C/s thus forming cold-rolled steel sheets. Properties of these cold-rolled steel sheets are shown in Table 2.
- tensile strength of the hot-rolled steel sheets is 1000 MPa or less so that a thickness of the steel sheet can be reduced to targeted 0.5 mm in cold rolling which is performed after hot-rolling, and tensile strength of the cold-rolled steel sheet can be set to 1280 MPa or more and breaking elongation can be set to 3 % or more.
- tensile strength of the cold-rolled steel sheet can be set to 1280 MPa or more and breaking elongation can be set to 3 % or more.
- breaking elongation can be set to 3 % or more.
- cold-rolled steel sheets which have tensile strengths of 1320 MPa and 1405 MPa and have breaking elongation of 6.2 % and 6.0 % respectively can be obtained.
- a hot-rolled steel sheet of a comparison example 1 is manufactured using the specimen 1 from which a hot-rolled steel sheet of the example 1 is also manufactured.
- the winding temperature is set to a low temperature of 480 °C and hence, tensile strength of a hot-rolled steel sheet is increased to 1108 MPa whereby the hot-rolled steel sheet becomes hard. Accordingly, a thickness of the steel sheet cannot be reduced to targeted 0.5 mm in cold rolling which is performed after hot-rolling, and when a rolling load and the number of times that rolling is performed are increased, cracks occur in the steel sheet and hence, cold-rolling is stopped.
- a hot-rolled steel sheet of a comparison example 2 is manufactured using the specimen 2 from which hot-rolled steel sheets of the examples 2 to 4 are also manufactured.
- the winding temperature is set to a low temperature of 500 °C and hence, tensile strength of a hot-rolled steel sheet is increased to 1216 MPa whereby the hot-rolled steel sheet becomes hard. Accordingly, a thickness of the steel sheet cannot be reduced to targeted 0.5 mm in cold rolling which is performed after hot-rolling, and when a rolling load and the number of times that rolling is performed are increased, cracks occur in the steel sheet and hence, cold-rolling is stopped.
- the content of C is set to 0.10 or less in comparison examples 3, 4, the content of Cr is set to 1.2 % or less in a comparison example 5, and the content of Mn and the content of Ni are small and the content of Mn+Ni is set to 0.5 % or less in a comparison example 7.
- tensile strength of a cold-rolled steel sheet becomes 1280 MPa or less so that when the cold-rolled steel sheet is used for manufacturing gaskets or frame parts, the cold-rolled steel sheet has insufficient strength whereby the cold-rolled steel sheet is not applicable to the manufacture of the gaskets and the frame parts.
- the total content of Mn+Ni is large, that is, 3.4 and hence, tensile strength of the hot-rolled steel sheet is increased whereby the steel sheet cannot be rolled to 0.5 mm which is a target thickness in cold-rolling which is performed after hot-rolling.
- a thickness of the hot-rolled steel sheet cannot be reduced even when the hot-rolled steel sheet is rolled, or when a rolling load or the number of times that rolling is performed is increased, cracks occur in the steel sheet so that the cold-rolled steel sheet cannot be manufactured.
- composition value [wt%] slab specimen c si Mn P S Cu Ni Cr S.Al Ti N Mn+Ni 1 0.15 0.18 0.8 0.004 0.005 0.19 0.1 3.1 0.019 0.00 0.009 0.9 example 1 comparison example 1 2 0.14 0.17 1.6 0.006 0.003 0.20 0.1 2.5 0.026 0.10 0.010 1.7 example 2 example 3 example 4 comparison example 2 3 0.15 0.18 1.61 0.006 0.005 0.19 0.10 3.1 0.024 0.00 0.012 1.7 example 5 4 0.15 0.20 0.89 0.004 0.003 0.19 1.02 2.6 0.026 0.10 0.010 1.9 example 6 5 0.18 1.12 0.78 0.003 0.003 0.05 0.07 2.5 0.010 0.03 0.010 0.9 example 7 6 0.15 0.21 0.82 0.005 0.006 0.19 0.11 5.1 0.017 0.00 0.013 0.9 example 8 7 0.14 0.19 0.42 0.015 0.005 0.31 0.11 3.0 0.031 0.008
- the present invention it is possible to provide a cold-rolled steel sheet which undergoes a small load at the time of cold-rolling, has excellent press formability while ensuring high strength and ductility. Further, it is also possible to provide a cold-rolled steel sheet having both strength and formability which has a thickness of 0.05 mm to 0.6 mm, a tensile strength of 1280 MPa or more, and breaking elongation of 3 % or more, wherein these are conditions which a raw material used for manufacturing a gasket of a gasoline engine for an automobile, a liquid crystal frame or a frame part of anotebook-typepersonal computer, a mobile phone and a digital camera or the like is required to have. Accordingly, the present invention has an extremely high industrial applicability.
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)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
- The present invention relates to a method of manufacturing a cold-rolled steel sheet having excellent press formability and a cold-rolled steel sheet manufactured by the manufacturing method.
- It is often the case where liquid crystal frame parts used in a mobile phone or a notebook-type personal computer, gasket parts for an automobile engine and the like are formed by a cold press. Accordingly, a thin cold-rolled steel sheet which is used for forming these parts is required to have press formability.
Further, with respect to parts of an electronic device represented by a notebook-type personal computer, a mobile phone or a digital camera or parts such as a gasket for an automobile engine, these parts are required to satisfy a demand for the reduction of weight and the miniaturization. To realize the reduction of weight and for the miniaturization of these parts, it is necessary to make a steel sheet thin. On the other hand, when the steel sheet which is made thin has the same strength as the steel sheet which is not made thin, the steel sheet made thin cannot ensure a strength which a press product is required to have. Accordingly, it is necessary to provide a high strength steel sheet having a thin gauge and a high strength.
In view of such a technical background, as a steel sheet which is used in applications such as a reinforcing member for a bumper or a door of an automobile, there has been proposed an ultra high-strength steel sheet having the martensite or bainite structure and also having a tensile strength of 1180 MPa or more (see patent document 1).
Further, patent document 2 proposes a cold-rolled steel sheet for a gasket material having excellent spring property which is manufactured in such a manner where a steel sheet is heated at a recrystallization temperature or above in continuous annealing, is annealed after soaking, and is subjected to secondary cold rolling. -
- Patent document 1: Japanese Patent
3254106 - Patent document 2:
JP-A-9-194935 - However, the high-strength steel sheets which are disclosed in patent document 1 and patent document 2 aim for the acquisition of high strength so that ductility is lowered and cracks occur at the time of press forming thus giving rise to a drawback that press formability is low.
Further, to realize a thin gauge at the time of cold-rolling a high-strength hot-rolled steel sheet, a load at the time of coldrolling is increased thus giving rise to a drawback that productivity is impeded due to lowering of operability and the increase of a yield loss.
Accordingly, the present invention has been made to overcome the above-mentioned drawbacks, and it is an object of the present invention to provide a cold-rolled steel sheet which undergoes a small load at the time of cold-rolling, has excellent press formability and has high strength, and a method of manufacturing the cold-rolled steel sheet. -
- (1) A method of manufacturing a cold-rolled steel sheet according to the present invention is characterized in that a hot-rolled steel sheet which has the composition consisting of, by mass%, 0.10 to 0.30 C, 0.2 or more Mn, 0.01 or more Ni, 0.5 to 2.5 Mn+Ni, 1.2 to 9.0 Cr, and Fe and unavoidable impurities as a balance and has a tensile strength of 1000 MPa or less is subjected to pickling and, thereafter, is subjected to cold rolling at a total rolling reduction of 60 % or more thus forming a cold-rolled steel sheet, and final continuous annealing treatment is performed at a soaking temperature of 750°C or above and at a cooling rate of 3 °C/s to 100 °C/s thus manufacturing a cold-rolled steel sheet having a tensile strength of 1280 MPa or more, breaking elongation of 3 % or more and a thickness of 0.05 to 0.60 mm.
- (2) The method of manufacturing a cold-rolled steel sheet according to the present invention is, in the above-mentioned constitution (1), characterized in that a thickness of the hot-rolled steel sheet is 1. 2 to 3.0 mm.
- (3) A cold-rolled steel sheet according to the present invention is manufactured by a method where a hot-rolled steel sheet which has the composition consisting of, by mass%, 0.10 to 0.30 C, 0.2 or more Mn, 0.01 or more Ni, 0.5 to 2.5 Mn+Ni, 1.2 to 9.0 Cr, and Fe and unavoidable impurities as a balance and has a tensile strength of 1000 MPa or less is subjected to pickling and, thereafter, is subjected to cold rolling at a total rolling reduction of 60 % ormore thus forming a cold-rolled steel sheet, and final continuous annealing treatment is performed at a soaking temperature of 750°C or above and at a cooling rate of 3 °C/s to 100 °C/s, wherein
the cold-rolled steel sheet has a tensile strength of 1280 MPa or more, breaking elongation of 3 % or more and a thickness of 0.05 to 0.60 mm. - (4) The cold-rolled steel sheet according to the present invention is, in the above-mentioned constitution (3), a thickness of the hot-rolled steel sheet is 1. 2 to 3.0 mm.
- According to the present invention, it is possible to provide a cold-rolled steel sheet which undergoes a small load at the time of cold-rolling, and has excellent press formability while ensuring high strength and ductility.
Further, according to the method of manufacturing a cold-rolled steel sheet of the present invention, it is also possible to provide a cold-rolled steel sheet having both strength and formability which has a thickness of 0.05 mm to 0.6 mm, a tensile strength of 1280 MPa or more, and breaking elongation of 3 % or more, wherein these are conditions which a raw material used for manufacturing a gasket of a gasoline engine for an automobile, a liquid crystal frame or a frame part of a notebook-type personal computer, a mobile phone and a digital camera or the like is required to have. - The composition of hot-rolled steel sheet is set to the following range by mass%.
C: 0.10 to 0.30, Mn: 0.2 or more, Ni: 0.01 or more, Mn+Ni: 05 to 2.5, Cr: 1.2 to 9.0, balance: Fe and unavoidable elements.
C is an important element for forming the low-temperature transformed structure such as martensite in the steel sheet such that the steel sheet acquires high tensile strength.
When the content of C is extremely small, the required tensile strength cannot be acquired and hence, a lower limit of the content of C is set to 0.10. On the other hand, when the content of C is extremely large, a rolling load at the time of hot-rolling and a rolling load at the time of cold-rolling are increased so that the productivity is impeded due to the deterioration in shape or the like and hence, an upper limit of the content of C is set to 0.30. The content of C is more preferably set to a value which falls within a range from 0.15 to 0.25. - In the present invention, both Mn and Ni are elements which enhance hardenability and form the low-temperature transformed structure at the time of continuous annealing, and Mn and Ni impart high tensile strength to a cold-rolled steel sheet to which continuous annealing is applied. When a total amount of content of Mn and Ni is extremely small, the steel sheet cannot acquire strength after continuous annealing is applied to the steel sheet and hence, a lower limit of the total amount of content of Mn and Ni is set to 0.5. On the other hand, when the total amount of content of Mn and Ni is extremely large, the above-mentioned advantageous effect is saturated and, further, workability is lowered due to the segregation and the like and hence, an upper limit of the total amount of content of Mn and Ni is set to 2.5.
Here, with respect to respective ranges of the content of Mn and the content of Ni, it is necessary for the steel sheet to contain 0.20 or more of Mn since Mn prevents red heat caused by S which is an impurity, and it is necessary to add 0.01 or more of Ni to the steel sheet since Ni ensures toughness of the steel sheet after heat treatment. Since Ni is expensive, it is advantageous to adjust the total amount of content of Mn and Ni by adjusting the content of Mn in view of cost. - Cr is also an element which can enhance hardenability, and Cr forms the low-temperature transformed structure at the time of continuous annealing so that the steel sheet can acquire high tensile strength. When the content of Cr is extremely small, the steel sheet cannot acquire tensile strength after continuous annealing is applied to the steel sheet and hence, a lower limit of the content of Cr is set to 1.2. On the other hand, when the content of Cr is extremely large, the above-mentioned advantageous effect is saturated and, further, cost is increased wastefully and hence, an upper limit of the content of Cr is set to 9.0. The content of Cr is more preferably set to a value which falls within a range from 2.0 to 5.5.
- Si is an element effective for greatly increasing strength of a cold-rolled steel sheet. The larger content of Si, the more easily the obj ect canbe achieved. However, when the content of Si exceeds 2.0 %, a load in cold-rolling is increased and a shape of the steel sheet is deteriorated and hence, an upper limit value of the content of Si is set to 2.0 %.
- P is a component which makes crystal grains fine and hence, it is desirable to add a fixed amount of P to the steel sheet for enhancing strength of a cold-rolled steel sheet. However, P also causes segregation in a crystal grain boundary thus inducing brittleness of the steel sheet. Accordingly, the content of P is set to 0.06 % or less.
- S is an impurity component which generates red-brittleness during hot rolling and hence, it is desirable that the steel sheet contains as little S as possible. However, it is impossible to completely prevent the mixing of S from a raw material or the like into a steel sheet, and the desulfurization in the manufacturing steps is also limited and hence, it is unavoidable that S remains in the steel sheet to some extent. The red-brittleness caused by a small amount of residual S can be alleviated by Mn and hence, an upper limit value of the content of S is set to 0.06 %.
- A fixed amount of Cu may be added to the steel sheet for enhancing the strength of a steel sheet by solid solution strengthening or by precipitation strengthening. On the other hand, however, there exists a possibility that Cu will bring about brittleness in the steel sheet at the time of hot rolling. Accordingly, an upper limit of Cu is set to 0.5 %.
- Al is added to a steel bath as a deoxidizing agent in making steel. Al reacts with solid solution N and segregates as AIN thus contributing to making the crystal grain fine. On the other hand, when the content of Al exceeds 0.10 %, the solidification of N becomes conspicuous thus lowering solid solution strengthening brought about by N and hence, the content of Al is set to 0.10 % or less.
- The addition of Ti is effective for making the crystal grain fine, for suppressing a grain growth, for enhancing corrosion resistance and the like. However, even when the content of Ti added to the steel sheet is excessively large, the advantageous effect is saturated and hence, the content of Ti is set to 0.30 % or less.
- N is , in the same manner as C and Mn, a component necessary for imparting high strength to a cold-rolled steel sheet and for increasing durability of the cold-rolled steel sheet. However, setting the content of N to less than 0.002 % is difficult in terms of making steel. On the other hand, the addition of the content of N which exceeds 0.015 % remarkably lowers a yield rate of ferro-nitride at the time of making steel thus making the steel sheet unstable, and also remarkably deteriorates anisotropy of the steel sheet at the time of press forming.
Further, cracks occur on a surface of a continuously-cast slab and the cracks become a defect in casting. Accordingly, the content of N is desirably set to 0.015 % or less in the present invention. - Hereinafter, a method of manufacturing a cold-rolled steel sheet according to the present invention is explained.
- Raw materials are melted in a converter or an electric furnace to produce molten steel and molten steel is cast for producing a slab whose composition is adjusted to the above-mentioned range.
- A slab whose components are adjusted to the above-mentioned range is formed into a steel sheet having a sheet thickness of 1.2 to 3.0 mm by hot-rolling. When the sheet thickness is set small, a load at the time of hot-rolling is increased. Accordingly, a lower limit of the sheet thickness is set to 1.2. On the other hand, when the sheet thickness is set large, a load at the time of cold-rolling which is performed after hot-rolling is increased. Accordingly, an upper limit of the sheet thickness is set to 3.0.
In the hot-rolling step, a heat temperature of the slab having the above-mentioned composition is set to 1100 °C or above, and a coiling temperature (CT) is set to 600 °C or above. When the heating temperature of the slab is below 1100 °C, the positive decomposition solid solution of N becomes insufficient and a load at the time of hot-rolling is increased. Accordingly, such a heating temperature is not preferable.
Further, the winding temperature is set to a value which falls within a range from 600 °C to 800 °C. When the winding temperature is low, strength of the hot-rolled steel sheet is largely increased so that such a steel sheet is not preferable for cold-rolling. Accordingly, a lower limit of the winding temperature is set to 600°C.
On the other hand, when the winding temperature exceeds 800 °C, the generation of scales is accelerated at the time of hot rolling so that a load at the time of descaling by pickling is increased whereby an upper limit of the winding temperature is set to 800°C.
The hot-rolled steel sheet which is manufactured under the above-mentioned condition may have a tensile strength of 1000 MPa or less. This is because when tensile strength of the hot-rolled steel sheet exceeds 1000 MPa, a rolling load at the time of cold rolling is increased so that the tensile strength exceeding 1000 MPa is not preferable. - Scales generated on a surface of the steel sheet at the time of hot-rolling are removed in an acid bath in accordance with a normal method and, thereafter, the steel sheet is subjected to cold-rolling and continuous annealing.
- Cold-rolling is applied to the steel sheet once or several times at a rolling reduction of 60 % or more in total until the steel sheet, as a product, acquires a predetermined product thickness of 0.05 to 0.6 mm. This is because when the product thickness becomes 0.05 mm or less, rigidity of the steel sheet is lowered so that there may be a case where when the steel sheet is used for manufacturing products such as a gasket of a gasoline engine of an automobile, a liquid crystal frame or a frame part of a notebook-type personal computer, a mobile phone and a digital camera, the shape of the product is liable to be deformed and hence, the product cannot be manufactured.
On the other hand, when the product thickness becomes 0.6 mm or more, there may be a case where when the steel sheet is used for manufacturing a product such as a gasket of a gasoline engine of an automobile, a liquid crystal frame or a frame part of anotebook-typepersonal computer, a mobile phone and a digital camera, a weight of the product becomes larger than a designed value or the miniaturization of the product cannot be realized. - Although an upper limit of the total rolling reduction in cold-rolling is not particularly limited, the upper limit of the total rolling reduction is set to 98 %.
Further, by applying continuous annealing at a temperature of 500 °C or above or batch annealing at a temperature of 500 °C or above to the steel sheet after cold-rolling, the rolled sheet which is hardened by work hardening is softened so that cold-rolling can be applied to the steel sheet again.
A method of cold-rolling and the number of times that cold-rolling is performed are not particularly designated, and the method and the number of times that cold-rolling is performed can be suitably selected in accordance with a target sheet thickness. - Continuous annealing is applied to the steel sheet for removing strains in the sheet generated at the time of cold-rolling. When cold-rolling is performed plural times, continuous annealing can be performed in each cold-rolling.
According to the present invention, in the final continuous annealing, the steel sheet is soaked and held at a soaking temperature of 750°C or above for 1 second or more and 100 seconds or less. When the soaking temperature is below750°C, a temperature of the steel sheet does not exceed an Ae3 transformation temperature and hence, the steel sheet cannot acquire sufficient tensile strength.
On the other hand, even when the soaking temperature exceeds 1000°C, there is no particular advantageous effect, and such a temperature is wasteful from the industrial viewpoint and hence, an upper limit of the soaking temperature is set to 1000°C.
In the final continuous annealing, a part or the entire steel sheet is formed into austenite by heating the steel sheet and, thereafter, these parts are transformed into martensite or the like by cooling after such heating.
According to the present invention, corresponding to an amount of martensite and an amount of alloy element, the steel sheet can acquire a predetermined strength. - After the steel sheet is soaked and held at a soaking temperature of 750°C or above for 1 second or more and 100 seconds or less, the steel sheet is cooled at a cooling rate of 3°C/s to 100°C/s. Due to such cooling, the austenite structure of the steel sheet is formed into structures such as martensite, tempered martensite and bainite. When the cooling rate is 3°C/s or less, the formation of the low-temperature transformed structure such as martensite becomes insufficient and hence, the steel sheet cannot acquire sufficient strength. On the other hand, when the cooling rate exceeds 100°C/s, although the steel sheet can acquire required strength, a shape of the steel sheet is deteriorated and hence, such a steel sheet is not preferable for press application.
- In the present invention, after the continuous annealing, a steel sheet is cooled at a cooling rate which is remarkably slow compared with a cooling rate for general quenching using water or the like which is performed for ensuring a shape so that the low-temperature transformed structure is formed and thereby a high strength steel sheet is acquired.
With respect to Mn and Ni which are effective austenite stabilizing elements used as general quenching elements, it is necessary to add a considerable amount of Mn and Ni to the steel sheet to acquire a required strength at the above-mentioned cooling rate. However, the addition of a considerable amount of Mn and Ni to the steel sheet largely increases strength of the steel sheet after hot-rolling so that a load at the time of cold-rolling is increased whereby productivity is impeded thus inducing an increase in product cost.
According to the present invention, the content of Mn and the content of Ni are set relatively small, and Cr which is a ferrite stabilizing element is added to the steel sheet so as to form a composite and hence, it is possible to make the steel sheet relatively soft after hot-rolling and to manufacture a high-strength steel sheet by continuous annealing which is performed after cold-rolling whereby a load in the manufacture of the steel sheet can be significantly reduced. - Further, when necessary, tempering treatment below 600 °C may be applied to the steel sheet after the steel sheet is cooled after final continuous annealing. In the present invention, however, the steel sheet is formed into the quenched structure at a relatively low cooling rate and hence, an effect substantially equal to an effect obtained by tempering treatment can be acquired at the time of cooling whereby the tempering step can be omitted. The omission of the tempering step largely contributes to the reduction of a load in the manufacture of the steel sheet.
- Due to the above-mentioned continuous annealing applied to the steel sheet, tensile strength of a cold-rolled steel sheet acquired by the manufacturing method of the present invention can be increased to 1280 MPa or more. Since the cold-rolled steel sheet has such strength, when the cold-rolled steel sheet is used for manufacturing a gasket of a gasoline engine of an automobile, there is no possibility that a gas leak will occur.
Further, when a sheet thickness of the cold-rolled steel sheet is made small for reduction of weight and the cold-rolled steel sheet is used for manufacturing a liquid crystal frame or frame parts of a notebook-type personal computer, a mobile phone, or a digital camera, and particularly when the cold-rolled steel sheet is used inmobile applications, theseparts can ensure the required rigidity as the parts. - Further, in the manufacturing method of the present invention, breaking elongation of a cold-rolled steel sheet can be set to 3 % or more. A value of breaking elongation indicative of ductility is important when a cold-rolled steel sheet is press-formed for manufacturing products such as gaskets for an automobile engine and electronic parts. When breaking elongation is less than 3 %, cracks are liable to occur inportions which are subjected to some degree of bulging forming, bending at 90° or the like.
- A steel sheet manufactured by the above-mentioned manufacturing method has the structure formed of martensite, tempered martensite, bainite structure and the like by a volume% of 60 % or more, has high tensile strength of 1280 MPa or more, and ensures ductility.
- The steel sheet obtained in this manner is, whennecessary, subjected to temper rolling for surface roughness adjustment or subjected to electro plating and chemical conversion coating using Zn, Ni or the like for rust prevention.
- The steel sheet obtained by the manufacturing method of the present invention can be used as a raw material for press forming. However, the steel sheet obtained by the manufacturing method of the present invention largely differs from a generally-used cold-rolled steel sheet in a strength range and hence, it is necessary to take into account spring-back or the like.
- To explain a cold-rolled steel sheet of the present invention in further detail in conjunction with examples and comparison examples, slabs having compositions corresponding to specimens 1 to 18 shown in Table 1 are prepared. The specimens 1 to 11, 17, 18 are slabs having the compositions which fall within a composition range of the present invention, while the specimens 12 to 16 are slabs which do not fall within the composition range of the present invention.
In hot-rolling step, the slabs which are adjusted to the compositions corresponding to specimens 1 to 18 are heated at a temperature of 1230 °C, and hot-rolled steel sheets having a sheet thickness of 2.0 mm are manufactured at winding temperatures shown in Table 2. Properties of these hot-rolled steel sheets are shown in Table 2.
Next, after pickling these hot-rolled steel sheets, the hot-rolled steel sheets are cold-rolled to a thickness of 0.5 mm. Thereafter, inacontinuousannealingstep, thecold-rolled steel sheets are soaked and held at a soaking temperature of 900 °C for 20 seconds and, thereafter, the cold-rolled steel sheets are cooled at a cooling rate of 20 °C/s thus forming cold-rolled steel sheets. Properties of these cold-rolled steel sheets are shown in Table 2.
As can be understood from Table 2, in the examples 1 to 15, tensile strength of the hot-rolled steel sheets is 1000 MPa or less so that a thickness of the steel sheet can be reduced to targeted 0.5 mm in cold rolling which is performed after hot-rolling, and tensile strength of the cold-rolled steel sheet can be set to 1280 MPa or more and breaking elongation can be set to 3 % or more.
In the examples 3, 4, by changing a cooling rate after soaking to 3 °C/s, 100 °C/s respectively, cold-rolled steel sheets which have tensile strengths of 1320 MPa and 1405 MPa and have breaking elongation of 6.2 % and 6.0 % respectively can be obtained. - A hot-rolled steel sheet of a comparison example 1 is manufactured using the specimen 1 from which a hot-rolled steel sheet of the example 1 is also manufactured. However, the winding temperature is set to a low temperature of 480 °C and hence, tensile strength of a hot-rolled steel sheet is increased to 1108 MPa whereby the hot-rolled steel sheet becomes hard. Accordingly, a thickness of the steel sheet cannot be reduced to targeted 0.5 mm in cold rolling which is performed after hot-rolling, and when a rolling load and the number of times that rolling is performed are increased, cracks occur in the steel sheet and hence, cold-rolling is stopped.
A hot-rolled steel sheet of a comparison example 2 is manufactured using the specimen 2 from which hot-rolled steel sheets of the examples 2 to 4 are also manufactured. However, the winding temperature is set to a low temperature of 500 °C and hence, tensile strength of a hot-rolled steel sheet is increased to 1216 MPa whereby the hot-rolled steel sheet becomes hard. Accordingly, a thickness of the steel sheet cannot be reduced to targeted 0.5 mm in cold rolling which is performed after hot-rolling, and when a rolling load and the number of times that rolling is performed are increased, cracks occur in the steel sheet and hence, cold-rolling is stopped.
The content of C is set to 0.10 or less in comparison examples 3, 4, the content of Cr is set to 1.2 % or less in a comparison example 5, and the content of Mn and the content of Ni are small and the content of Mn+Ni is set to 0.5 % or less in a comparison example 7. Accordingly, in the respective comparison examples, tensile strength of a cold-rolled steel sheet becomes 1280 MPa or less so that when the cold-rolled steel sheet is used for manufacturing gaskets or frame parts, the cold-rolled steel sheet has insufficient strength whereby the cold-rolled steel sheet is not applicable to the manufacture of the gaskets and the frame parts.
In a comparison example 6, the total content of Mn+Ni is large, that is, 3.4 and hence, tensile strength of the hot-rolled steel sheet is increased whereby the steel sheet cannot be rolled to 0.5 mm which is a target thickness in cold-rolling which is performed after hot-rolling. To be more specific, due to high hardness, a thickness of the hot-rolled steel sheet cannot be reduced even when the hot-rolled steel sheet is rolled, or when a rolling load or the number of times that rolling is performed is increased, cracks occur in the steel sheet so that the cold-rolled steel sheet cannot be manufactured. -
[Table 1] composition value [wt%] slab specimen c si Mn P S Cu Ni Cr S.Al Ti N Mn+Ni 1 0.15 0.18 0.8 0.004 0.005 0.19 0.1 3.1 0.019 0.00 0.009 0.9 example 1 comparison example 1 2 0.14 0.17 1.6 0.006 0.003 0.20 0.1 2.5 0.026 0.10 0.010 1.7 example 2 example 3 example 4 comparison example 2 3 0.15 0.18 1.61 0.006 0.005 0.19 0.10 3.1 0.024 0.00 0.012 1.7 example 5 4 0.15 0.20 0.89 0.004 0.003 0.19 1.02 2.6 0.026 0.10 0.010 1.9 example 6 5 0.18 1.12 0.78 0.003 0.003 0.05 0.07 2.5 0.010 0.03 0.010 0.9 example 7 6 0.15 0.21 0.82 0.005 0.006 0.19 0.11 5.1 0.017 0.00 0.013 0.9 example 8 7 0.14 0.19 0.42 0.015 0.005 0.31 0.11 3.0 0.031 0.00 0.008 0.5 example 9 8 0.16 0.28 1 60 0.012 0.005 0.19 0.66 3.0 0.012 0.00 0.011 2.3 example 10 9 0.10 0.31 1.62 0.005 0.002 0.18 0.13 2.9 0.025 0.00 0.009 1.8 example 11 10 0.30 0.55 1.19 0.003 0.004 0.15 0.12 2.0 0.031 0.00 0.008 1.3 example 12 11 0.11 0.25 0.44 0.011 0.010 0.11 0.05 8.9 0.025 0.00 0.011 0.5 example 13 12 0.08 0.21 0.82 0.006 0.005 0.19 0.11 7.2 0.008 0.00 0.016 0.9 comparison example 3 13 0.07 0.18 1.60 0.006 0.003 0.19 0.10 2.5 0.025 0.10 0.010 1.7 comparison example 4 14 0.18 1.17 0.72 0.004 0.005 0.12 0.09 1.0 0.017 0.11 0.008 0.8 comparison example 5 15 0.15 0.20 0.84 0.004 0.003 0.18 2.51 2.6 0.023 0.10 0.009 3.4 comparison example 6 16 0.19 1.17 0.36 0.001 0.005 0.05 0.06 2.1 0.020 0.01 0.010 0.4 comparison example 7 17 0.18 0.21 1.49 0.005 0.003 0.19 0.09 1.5 0.022 0.00 0.006 1.6 example 14 18 0.18 0.22 1.82 0.004 0.004 0.18 0.11 1.2 0.028 0.01 0.009 1.9 example 15 -
[Table 2] mechanical properties of hot-rolled steel sheet properties after continuous annealing winding temperature [°C] tensile strength [MPa] breaking elongation [%] temperature [°C] cooling rate [°C/s] tensile strength [MPa] breaking elongation [%] example 1 650 684 20.8 900 20 1304 6.1 comparison example 1 480 1108 12.2 - 20 - - example 2 650 646 19.6 900 20 1348 6.1 example 3 900 3 1320 6.2 example 4 900 100 1405 6.0 comparison example 2 500 1216 10.4 - 20 - - example5 650 585 22.8 900 20 1392 6.3 Example6 650 672 19.4 900 20 1439 7.1 example 7 620 635 18.8 900 20 1501 6.9 example 8 650 621 21.7 900 20 1359 6.0 example 9 650 584 22.2 900 20 1371 6.4 example 10 650 712 17.7 900 20 1381 6.2 example 11 650 532 22.8 900 20 1327 6.3 example 12 650 694 19.1 900 20 1588 6.0 example 13 650 579 18.9 900 20 1388 6.7 comparison example 3 650 547 26.7 900 20 1214 6.4 comparison example 4 650 625 19.8 900 20 1052 7.4 comparison example 5 620 532 21.3 900 20 853 18.5 comparison example 6 650 1282 7.7 900 20 - - comparison example 7 650 551 20.9 900 20 1227 8.3 example 14 650 588 21.1 900 20 1388 6.1 example 15 650 655 19.2 900 20 1421 6.5 - According to the present invention, it is possible to provide a cold-rolled steel sheet which undergoes a small load at the time of cold-rolling, has excellent press formability while ensuring high strength and ductility. Further, it is also possible to provide a cold-rolled steel sheet having both strength and formability which has a thickness of 0.05 mm to 0.6 mm, a tensile strength of 1280 MPa or more, and breaking elongation of 3 % or more, wherein these are conditions which a raw material used for manufacturing a gasket of a gasoline engine for an automobile, a liquid crystal frame or a frame part of anotebook-typepersonal computer, a mobile phone and a digital camera or the like is required to have. Accordingly, the present invention has an extremely high industrial applicability.
Claims (4)
- A method of manufacturing a cold-rolled steel sheet in which a hot-rolled steel sheet which has the composition consisting of, by mass%, 0.10 to 0.30 C, 0.2 or more Mn, 0.01 or more Ni, 0.5 to 2.5 Mn+Ni, 1.2 to 9.0 Cr, and Fe and unavoidable impurities as a balance and has a tensile strength of 1000 MPa or less is subjected to pickling and, thereafter, is subjected to cold rolling at a total rolling reduction of 60 % or more thus forming a cold-rolled steel sheet, and final continuous annealing treatment is performed at a soaking temperature of 750 °C or above and at a cooling rate of 3 °C/s to 100 °C/s thus manufacturing a cold-rolled steel sheet having a tensile strength of 1280 MPa or more, breaking elongation of 3 % or more and a thickness of 0.05 to 0.60 mm.
- The method of manufacturing a cold-rolled steel sheet according to claim 1, wherein a thickness of the hot-rolled steel sheet is 1. 2 to 3.0 mm.
- A cold-rolled steel sheet which is manufactured by a method where a hot-rolled steel sheet which has the composition consisting of, by mass%, 0.10 to 0.30 C, 0.2 or more Mn, 0.01 or more Ni, 0.5 to 2.5 Mn+Ni, 1.2 to 9.0 Cr, and Fe and unavoidable impurities as a balance and has a tensile strength of 1000 MPa or less is subjected to pickling and, thereafter, is subjected to cold rolling at a total rolling reduction of 60 % or more thus forming a cold-rolled steel sheet, and final continuous annealing treatment is performed at a soaking temperature of 750 °C or above and at a cooling rate of 3 °C/s to 100 °C/s, wherein the cold-rolled steel sheet has a tensile strength of 1280 MPa or more, breaking elongation of 3 % or more and a thickness of 0.05 to 0.60 mm.
- The cold-rolled steel sheet according to claim 3, wherein a thickness of the hot-rolled steel sheet is 1. 2 to 3.0 mm.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2009162198 | 2009-07-08 | ||
PCT/JP2010/004062 WO2011004554A1 (en) | 2009-07-08 | 2010-06-17 | Process for production of cold-rolled steel sheet having excellent press moldability, and cold-rolled steel sheet |
Publications (3)
Publication Number | Publication Date |
---|---|
EP2455499A1 true EP2455499A1 (en) | 2012-05-23 |
EP2455499A4 EP2455499A4 (en) | 2016-02-10 |
EP2455499B1 EP2455499B1 (en) | 2017-12-13 |
Family
ID=43428986
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP10796868.7A Active EP2455499B1 (en) | 2009-07-08 | 2010-06-17 | Process for production of cold-rolled steel sheet having excellent press moldability |
Country Status (5)
Country | Link |
---|---|
US (1) | US20120234438A1 (en) |
EP (1) | EP2455499B1 (en) |
JP (1) | JP5717631B2 (en) |
CN (1) | CN102471821B (en) |
WO (1) | WO2011004554A1 (en) |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103849820B (en) * | 2014-03-19 | 2017-01-04 | 武汉钢铁(集团)公司 | The rolling mill practice of high-strength corrosion-resisting Li-adding Al alloy muscle |
WO2016187577A1 (en) | 2015-05-21 | 2016-11-24 | Ak Steel Properties, Inc. | High manganese 3rd generation advanced high strength steels |
CN105177458A (en) * | 2015-08-31 | 2015-12-23 | 铜陵市大明玛钢有限责任公司 | Manufacturing method of cold-rolled steel plate |
CN112313352B (en) * | 2018-06-29 | 2023-06-27 | 东洋钢钣株式会社 | Hot-rolled steel sheet, high-strength cold-rolled steel sheet, and method for producing same |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH08311601A (en) * | 1995-05-19 | 1996-11-26 | Kobe Steel Ltd | Ultrahigh strength steel sheet excellent in delayed fracture resistance and its production |
JPH101740A (en) * | 1996-06-12 | 1998-01-06 | Kobe Steel Ltd | Ultrahigh strength steel sheet excellent in delayed fracture resistance, and its production |
JP2005097725A (en) * | 2003-09-05 | 2005-04-14 | Nippon Steel Corp | Steel sheet for hot press having hydrogen embrittlement resistance, automobile member and its production method |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5825733B2 (en) * | 1979-11-27 | 1983-05-30 | 新日本製鐵株式会社 | Method for manufacturing high-strength cold-rolled steel sheet with good paintability, weldability, and workability |
JP3254106B2 (en) | 1995-05-19 | 2002-02-04 | 株式会社神戸製鋼所 | Ultra-high-strength steel sheet excellent in hydrogen embrittlement resistance and method for producing the same |
JPH09194935A (en) | 1996-01-10 | 1997-07-29 | Toyo Kohan Co Ltd | Production of cold rolled steel sheet for gasket material, excellent in spring characteristic, and gasket material |
JP3958921B2 (en) * | 2000-08-04 | 2007-08-15 | 新日本製鐵株式会社 | Cold-rolled steel sheet excellent in paint bake-hardening performance and room temperature aging resistance and method for producing the same |
TWI290177B (en) * | 2001-08-24 | 2007-11-21 | Nippon Steel Corp | A steel sheet excellent in workability and method for producing the same |
EP2309012B1 (en) * | 2003-09-30 | 2012-09-12 | Nippon Steel Corporation | High yield ratio and high-strength cold rolled thin steel sheet superior in weldability and ductility, high-yield ratio high-strength hot-dip galvanized cold rolled thin steel sheet, high-yield ratio high-strength hot-dip galvannealed cold rolled thin steel sheet, and methods of production of same |
JP4639996B2 (en) * | 2004-07-06 | 2011-02-23 | 住友金属工業株式会社 | Manufacturing method of high-tensile cold-rolled steel sheet |
JP2007016296A (en) * | 2005-07-11 | 2007-01-25 | Nippon Steel Corp | Steel sheet for press forming with excellent ductility after forming, its forming method and automotive parts using the steel sheet for press forming |
JP5194878B2 (en) * | 2007-04-13 | 2013-05-08 | Jfeスチール株式会社 | High-strength hot-dip galvanized steel sheet excellent in workability and weldability and method for producing the same |
-
2010
- 2010-06-17 EP EP10796868.7A patent/EP2455499B1/en active Active
- 2010-06-17 US US13/383,193 patent/US20120234438A1/en not_active Abandoned
- 2010-06-17 JP JP2011521800A patent/JP5717631B2/en active Active
- 2010-06-17 CN CN201080028024.8A patent/CN102471821B/en active Active
- 2010-06-17 WO PCT/JP2010/004062 patent/WO2011004554A1/en active Application Filing
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH08311601A (en) * | 1995-05-19 | 1996-11-26 | Kobe Steel Ltd | Ultrahigh strength steel sheet excellent in delayed fracture resistance and its production |
JPH101740A (en) * | 1996-06-12 | 1998-01-06 | Kobe Steel Ltd | Ultrahigh strength steel sheet excellent in delayed fracture resistance, and its production |
JP2005097725A (en) * | 2003-09-05 | 2005-04-14 | Nippon Steel Corp | Steel sheet for hot press having hydrogen embrittlement resistance, automobile member and its production method |
Non-Patent Citations (2)
Title |
---|
None * |
See also references of WO2011004554A1 * |
Also Published As
Publication number | Publication date |
---|---|
JPWO2011004554A1 (en) | 2012-12-13 |
EP2455499B1 (en) | 2017-12-13 |
JP5717631B2 (en) | 2015-05-13 |
CN102471821B (en) | 2014-07-16 |
EP2455499A4 (en) | 2016-02-10 |
CN102471821A (en) | 2012-05-23 |
WO2011004554A1 (en) | 2011-01-13 |
US20120234438A1 (en) | 2012-09-20 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US11390929B2 (en) | Hot-stamped part and method for manufacturing same | |
EP2554699B1 (en) | Steel sheet with high tensile strength and superior ductility and method for producing same | |
KR101706485B1 (en) | High-strength cold-rolled steel sheet and method for producing the same | |
EP2508639A1 (en) | Fine grained austenitic stainless steel sheet exhibiting excellent stress corrosion cracking resistance and processability | |
KR102096190B1 (en) | Moldable lightweight steel with improved mechanical properties and method for manufacturing semi-finished products from the steel | |
US20100326572A1 (en) | Method for producing low yield strength cold rolled steel sheet excellent in uniformity | |
CN110408861A (en) | A kind of cold rolling high strength and ductility medium managese steel and preparation method thereof having lower Mn content | |
EP2623625A2 (en) | Steel plate for line pipe, having excellent hydrogen induced crack resistance, and preparation method thereof | |
EP2455499B1 (en) | Process for production of cold-rolled steel sheet having excellent press moldability | |
KR101701652B1 (en) | Steel sheet for soft-nitriding and method for manufacturing the same | |
CN114040990B (en) | Austenitic stainless steel having improved strength and method for manufacturing the same | |
US20220403491A1 (en) | Austenitic stainless steel having increased yield ratio and manufacturing method thereof | |
EP4159887A9 (en) | Electro-galvanized super-strength dual-phase steel resistant to delayed cracking, and manufacturing method therefor | |
EP2527481B1 (en) | Quenched steel sheet having excellent hot press formability, and method for manufacturing same | |
KR101060782B1 (en) | Hot forming steel plate with excellent impact resistance and its manufacturing method and high strength automobile structural member and its manufacturing method | |
JP2012177176A (en) | Steel sheet for soft nitriding treatment, and its manufacturing method | |
KR102403849B1 (en) | High strength austenitic stainless steel with excellent productivity and cost saving effect, and method for manufacturing the same | |
CN111315907B (en) | Steel plate | |
EP3708691B1 (en) | Manufacturing method for ultrahigh-strength and high-ductility steel sheet having excellent cold formability | |
KR20220084555A (en) | Austenitic stainless steel with improved high temperature softening resistance | |
EP4397781A1 (en) | Hot-rolled ferritic stainless steel sheet having excellent formability and method for manufacturing same | |
KR20110062899A (en) | Steel sheet with excellent cold rolling property and coatability, method for manufacturing the same, high strength structural member for vehicles and method for manufacturing the same | |
JP2023527390A (en) | 780 MPa grade cold rolled and annealed duplex steel and its manufacturing method | |
JPH06220546A (en) | Production of high strength cold rolled steel sheet excellent in deep drawability |
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: 20120113 |
|
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 SE SI SK SM TR |
|
DAX | Request for extension of the european patent (deleted) | ||
RA4 | Supplementary search report drawn up and despatched (corrected) |
Effective date: 20160113 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C21D 8/02 20060101ALI20160107BHEP Ipc: C22C 38/50 20060101ALI20160107BHEP Ipc: C22C 38/04 20060101ALI20160107BHEP Ipc: C22C 38/42 20060101ALI20160107BHEP Ipc: C22C 38/02 20060101ALI20160107BHEP Ipc: C22C 38/06 20060101ALI20160107BHEP Ipc: C21D 9/00 20060101ALI20160107BHEP Ipc: C22C 38/00 20060101ALI20160107BHEP Ipc: C21D 9/46 20060101AFI20160107BHEP Ipc: C21D 1/26 20060101ALI20160107BHEP Ipc: C22C 38/58 20060101ALI20160107BHEP |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C21D 1/26 20060101ALI20170324BHEP Ipc: C22C 38/42 20060101ALI20170324BHEP Ipc: C21D 8/02 20060101ALI20170324BHEP Ipc: C21D 9/00 20060101ALI20170324BHEP Ipc: C22C 38/58 20060101ALI20170324BHEP Ipc: C22C 38/04 20060101ALI20170324BHEP Ipc: C22C 38/06 20060101ALI20170324BHEP Ipc: C21D 9/46 20060101AFI20170324BHEP Ipc: C22C 38/02 20060101ALI20170324BHEP Ipc: C22C 38/50 20060101ALI20170324BHEP Ipc: C22C 38/00 20060101ALI20170324BHEP |
|
17Q | First examination report despatched |
Effective date: 20170428 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
INTG | Intention to grant announced |
Effective date: 20170719 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO 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: AT Ref legal event code: REF Ref document number: 954425 Country of ref document: AT Kind code of ref document: T Effective date: 20171215 Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602010047381 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20171213 |
|
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: 20171213 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: 20180313 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: 20171213 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: 20171213 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 954425 Country of ref document: AT Kind code of ref document: T Effective date: 20171213 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180314 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: 20171213 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: 20171213 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: 20180313 |
|
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: 20171213 |
|
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: 20171213 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: 20171213 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: 20171213 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: 20171213 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: 20171213 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20171213 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: 20171213 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: 20180413 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: 20171213 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: 20171213 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: 20171213 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602010047381 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: 20180914 |
|
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: 20171213 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20180617 |
|
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: 20171213 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20180630 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: 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: 20171213 Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180617 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180630 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180630 Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180617 Ref country code: FR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180630 Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180617 |
|
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: 20180630 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180617 |
|
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: 20100617 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: 20171213 |
|
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 NON-PAYMENT OF DUE FEES Effective date: 20171213 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20171213 |
|
P01 | Opt-out of the competence of the unified patent court (upc) registered |
Effective date: 20230524 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: TR Payment date: 20230616 Year of fee payment: 14 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20240619 Year of fee payment: 15 |