EP2455499B1 - Processus de production d'une tôle d acier laminée à froid présentant une excellente aptitude au formage à la presse - Google Patents

Processus de production d'une tôle d acier laminée à froid présentant une excellente aptitude au formage à la presse Download PDF

Info

Publication number
EP2455499B1
EP2455499B1 EP10796868.7A EP10796868A EP2455499B1 EP 2455499 B1 EP2455499 B1 EP 2455499B1 EP 10796868 A EP10796868 A EP 10796868A EP 2455499 B1 EP2455499 B1 EP 2455499B1
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.)
Active
Application number
EP10796868.7A
Other languages
German (de)
English (en)
Other versions
EP2455499A1 (fr
EP2455499A4 (fr
Inventor
Satoshi Oi
Shigeyoshi Nishiyama
Fuyuki Yoshida
Yuji Kusumoto
Osamu Akisue
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nakayama Steel Works Ltd
Toyo Kohan Co Ltd
Original Assignee
Nakayama Steel Works Ltd
Toyo Kohan Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nakayama Steel Works Ltd, Toyo Kohan Co Ltd filed Critical Nakayama Steel Works Ltd
Publication of EP2455499A1 publication Critical patent/EP2455499A1/fr
Publication of EP2455499A4 publication Critical patent/EP2455499A4/fr
Application granted granted Critical
Publication of EP2455499B1 publication Critical patent/EP2455499B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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.
  • 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 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.
  • 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.
  • 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.
  • composition of hot-rolled steel sheet is set to the following range by mass%.
  • 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.
  • a lower limit of the content of C is set to 0.10.
  • 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.
  • 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.
  • 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 object 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 AlN 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.
  • 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.
  • 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 winding temperature is set to a value which falls within a range from 600 °C to 800 °C.
  • 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 a notebook-type personal 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 %.
  • 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 in the final continuous annealing, is soaked and held at a soaking temperature of 750°C or above for 1 second or more and 100 seconds or less.
  • a soaking temperature is below 750°C, 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
  • 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.
  • the cold-rolled steel sheet 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, these parts 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, in a continuous annealing step, the cold-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.
  • 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. 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.
  • 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 a notebook-type personal 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)

Claims (2)

  1. Procédé de fabrication d'une tôle d'acier laminée à froid, dans lequel une tôle d'acier laminée à chaud qui a la composition constituée, en % en masse, de 0,10 à 0,30 de C, de 0,2 ou plus de Mn, de 0,01 ou plus de Ni, de 0,5 à 2,5 de Mn + Ni, de 1,2 à 9,0 de Cr, de 2,0 ou moins de Si, de 0,5 ou moins de Cu, de 0,30 ou moins de Ti, et de Fe et d'impuretés inévitables pour le restant et a une résistance à la traction de 1000 MPa ou moins, est soumise à un décapage et est ensuite soumise à un laminage à froid avec une réduction par laminage totale de 60 % ou plus, en formant ainsi une tôle d'acier laminée à froid, et un traitement de recuit continu final est effectué à une température d'immersion de 750 °C ou plus et à un taux de refroidissement de 3 °C/s à 100 °C/s, en fabriquant ainsi une tôle d'acier laminée à froid ayant une résistance à la traction de 1280 MPa ou plus, un allongement à la rupture de 3 % ou plus et une épaisseur de 0,05 à 0,60 mm.
  2. Procédé de fabrication d'une tôle d'acier laminée à froid selon la revendication 1, dans lequel l'épaisseur de la tôle d'acier laminée à chaud est de 1,2 à 3,0 mm.
EP10796868.7A 2009-07-08 2010-06-17 Processus de production d'une tôle d acier laminée à froid présentant une excellente aptitude au formage à la presse Active EP2455499B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2009162198 2009-07-08
PCT/JP2010/004062 WO2011004554A1 (fr) 2009-07-08 2010-06-17 Processus de production d’une tôle d’acier laminée à froid présentant une excellente aptitude au formage à la presse, et tôle d’acier laminée à froid

Publications (3)

Publication Number Publication Date
EP2455499A1 EP2455499A1 (fr) 2012-05-23
EP2455499A4 EP2455499A4 (fr) 2016-02-10
EP2455499B1 true EP2455499B1 (fr) 2017-12-13

Family

ID=43428986

Family Applications (1)

Application Number Title Priority Date Filing Date
EP10796868.7A Active EP2455499B1 (fr) 2009-07-08 2010-06-17 Processus de production d'une tôle d acier laminée à froid présentant une excellente aptitude au formage à la presse

Country Status (5)

Country Link
US (1) US20120234438A1 (fr)
EP (1) EP2455499B1 (fr)
JP (1) JP5717631B2 (fr)
CN (1) CN102471821B (fr)
WO (1) WO2011004554A1 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103849820B (zh) * 2014-03-19 2017-01-04 武汉钢铁(集团)公司 高强度耐腐蚀含Cr钢筋的轧制工艺
MX2017014816A (es) 2015-05-21 2018-05-11 Ak Steel Properties Inc Aceros avanzados de alta resistencia de tercera generacion de alto manganeso.
CN105177458A (zh) * 2015-08-31 2015-12-23 铜陵市大明玛钢有限责任公司 一种冷轧钢板的制造方法
WO2020004561A1 (fr) * 2018-06-29 2020-01-02 東洋鋼鈑株式会社 Tôle d'acier laminée à chaud, tôle d'acier laminée à froid de résistance élevée et procédé de fabrication associé

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5825733B2 (ja) * 1979-11-27 1983-05-30 新日本製鐵株式会社 塗装性、溶接性及び加工性の良い高強度冷延鋼板の製造方法
JP3254107B2 (ja) * 1995-05-19 2002-02-04 株式会社神戸製鋼所 耐遅れ破壊特性にすぐれる超高強度鋼板及びその製造方法
JP3254106B2 (ja) 1995-05-19 2002-02-04 株式会社神戸製鋼所 耐水素脆化特性にすぐれる超高強度鋼板及びその製造方法
JPH09194935A (ja) 1996-01-10 1997-07-29 Toyo Kohan Co Ltd ばね性に優れたガスケット材用冷延鋼板の製造法およびガスケット材
JPH101740A (ja) * 1996-06-12 1998-01-06 Kobe Steel Ltd 耐遅れ破壊特性にすぐれる超高強度鋼板及びその製造方法
JP3958921B2 (ja) * 2000-08-04 2007-08-15 新日本製鐵株式会社 塗装焼付硬化性能と耐常温時効性に優れた冷延鋼板及びその製造方法
TWI290177B (en) * 2001-08-24 2007-11-21 Nippon Steel Corp A steel sheet excellent in workability and method for producing the same
JP4288201B2 (ja) * 2003-09-05 2009-07-01 新日本製鐵株式会社 耐水素脆化特性に優れた自動車用部材の製造方法
TWI302572B (en) * 2003-09-30 2008-11-01 Nippon Steel Corp High yield ratio, high strength steel sheet, high yield ratio, high strength hot dip galvanized steel sheet and high yield ratio, high strength alloyed hot dip galvanized steel sheet and process for producing same
JP4639996B2 (ja) * 2004-07-06 2011-02-23 住友金属工業株式会社 高張力冷延鋼板の製造方法
JP2007016296A (ja) * 2005-07-11 2007-01-25 Nippon Steel Corp 成形後の延性に優れたプレス成形用鋼板及びその成形方法、並びにプレス整形用鋼板を用いた自動車用部材
JP5194878B2 (ja) * 2007-04-13 2013-05-08 Ｊｆｅスチール株式会社 加工性および溶接性に優れる高強度溶融亜鉛めっき鋼板およびその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
JPWO2011004554A1 (ja) 2012-12-13
CN102471821B (zh) 2014-07-16
US20120234438A1 (en) 2012-09-20
WO2011004554A1 (fr) 2011-01-13
JP5717631B2 (ja) 2015-05-13
CN102471821A (zh) 2012-05-23
EP2455499A1 (fr) 2012-05-23
EP2455499A4 (fr) 2016-02-10

Similar Documents

Publication Publication Date Title
EP2554699B1 (fr) Tôle d'acier présentant une résistance à la traction élevée et une meilleure ductilité et procédé de fabrication de cette dernière
KR101706485B1 (ko) 고강도 냉연 강판 및 그 제조 방법
EP2508639A1 (fr) Feuille en acier inoxydable austénitique à grains fins présentant d'excellentes caractéristiques de façonnage et de résistance à la fissuration par corrosion sous tension
KR102096190B1 (ko) 향상된 기계적 물성을 갖는 성형 가능한 경량 강 및 상기 강으로부터 반제품을 제조하기 위한 방법
EP2792763A1 (fr) Feuille d'acier ayant une excellente résistance au vieillissement et son procédé de fabrication
US20100326572A1 (en) Method for producing low yield strength cold rolled steel sheet excellent in uniformity
CN110408861A (zh) 一种具较低Mn含量的冷轧高强塑积中锰钢及其制备方法
EP2868762B1 (fr) Tôle d'acier destinée à la nitruration douce et son procédé de production
EP2455499B1 (fr) Processus de production d'une tôle d acier laminée à froid présentant une excellente aptitude au formage à la presse
KR101701652B1 (ko) 연질화 처리용 강판 및 그 제조 방법
CN114040990B (zh) 具有改善的强度的奥氏体不锈钢和用于制造其的方法
EP4159887A9 (fr) Acier biphasé électro-galvanisée à super-résistance résistant à la fissuration différée et son procédé de fabrication
US20220403491A1 (en) Austenitic stainless steel having increased yield ratio and manufacturing method thereof
EP3231886B1 (fr) Tôle d'acier a phases complexes ayant une excellente formabilité et son procédé de fabrication
JP5614330B2 (ja) 軟窒化処理用鋼板およびその製造方法
CN109440004B (zh) 罐用钢板及其制造方法
EP2527481B1 (fr) Feuille d'acier trempé ayant une excellente aptitude au formage à chaud par pression, et son procédé de fabrication
KR102403849B1 (ko) 생산성 및 원가 절감 효과가 우수한 고강도 오스테나이트계 스테인리스강 및 이의 제조방법
CN111315907B (zh) 钢板
KR20220084555A (ko) 고온 연화저항성이 향상된 오스테나이트계 스테인리스강
EP4397781A1 (fr) Feuille d'acier inoxydable ferritique laminée à chaud présentant une excellente aptitude au formage et procédé associé de fabrication
KR20110062899A (ko) 냉간압연성 및 도금성이 우수한 열간성형 가공용 강판 및 그 제조방법과 고강도 자동차용 구조부재 및 그 제조방법
JPH06220546A (ja) 深絞り性に優れた高強度冷延鋼板の製造方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 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

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

Free format text: STATUS: EXAMINATION IS IN PROGRESS

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

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

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20170719

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 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: DE

Payment date: 20240619

Year of fee payment: 15

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

Ref country code: TR

Payment date: 20240607

Year of fee payment: 15