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ES2575997T3 - Extra-thin hard steel sheet and its manufacturing method - Google Patents

Extra-thin hard steel sheet and its manufacturing method Download PDF

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Publication number
ES2575997T3
ES2575997T3 ES07741011.6T ES07741011T ES2575997T3 ES 2575997 T3 ES2575997 T3 ES 2575997T3 ES 07741011 T ES07741011 T ES 07741011T ES 2575997 T3 ES2575997 T3 ES 2575997T3
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extra
steel sheet
carburization
phase
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Spanish (es)
Inventor
Hidekuni Murakami
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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    • 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
    • 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
    • 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
    • C21D1/06—Surface hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0457—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/40—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling foils which present special problems, e.g. because of thinness
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0442—Flattening; Dressing; Flexing

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)

Abstract

Una lámina de acero dura, extra-delgada que tiene un espesor de lámina de 0,400 mm o menor, que comprende, en % en masa, C: 0,800 % o menos; N: 0,600 % o menos; Si: 2,0 % o menos; Mn: 2,0 % o menos; P: 0,10 % o menos; S: 0,100 % o menos; Al: 3,0 % o menos; opcionalmente uno o más seleccionados de O: 0 a 0,200 %; Ti: 0 a 4,00 %; Nb: 0 a 4,00 %; REM: 0 a 4,00 %; B: 0 a 0,0300 %; Cu: 0 a 8,00 %; Ca: 0 a 1,00 %; Ni: 0 a 8,00 %; Cr: 0 a 20,00 %, y Sn, Sb, Mo, Ta, V y W cada uno en una cantidad de 0,10 % o menor, y siendo el resto Fe e impurezas inevitables, en la que la lámina de acero dura, extra-delgada contiene 0,05 % o más, en fracción de volumen, de una segunda fase que tiene un eje mayor medio de 0,10 μm o mayor y un eje menor medio de 0,05 μm o mayor y que cumple que eje mayor medio / eje menor medio >= 2,0 en la que la segunda fase es una sustancia simple de un compuesto de óxido, sulfuro, carburo, nitruro o un compuesto intermetálico.A hard, extra-thin steel sheet having a sheet thickness of 0.400mm or less, comprising, in mass%, C: 0.800% or less; N: 0.600% or less; Yes: 2.0% or less; Mn: 2.0% or less; P: 0.10% or less; S: 0.100% or less; Al: 3.0% or less; optionally one or more selected from O: 0 to 0.200%; Ti: 0 to 4.00%; Nb: 0 to 4.00%; REM: 0 to 4.00%; B: 0 to 0.0300%; Cu: 0 to 8.00%; Ca: 0 to 1.00%; Ni: 0 to 8.00%; Cr: 0 to 20.00%, and Sn, Sb, Mo, Ta, V and W each in an amount of 0.10% or less, and the remainder being Fe and unavoidable impurities, in which the steel sheet hard, extra-thin contains 0.05% or more, by volume fraction, of a second phase that has a mean major axis of 0.10 μm or greater and a mean minor axis of 0.05 μm or greater and that complies that mean major axis / mean minor axis> = 2.0 where the second phase is a simple substance of an oxide, sulfide, carbide, nitride compound or an intermetallic compound.

Description

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acuerdo con un ensayo de tracción realizado con el uso de una muestra de ensayo de tracción JIS5. according to a tensile test performed with the use of a JIS5 tensile test sample.

Más adelante, se representará un ejemplo preferido del método de fabricación parta cada tipo de segunda fase en el acero de la presente invención. En primer lugar, será representado un caso en el que se utiliza un óxido como segunda fase especial. Una realización preferida incluye el laminado y el alargamiento de un óxido mediante laminado en una etapa de laminado en caliente para ser modificado a una forma preferible. Para realizar esto, se requiere cierto grado de cantidad de trabajo, y un espesor de un bloque de acero sometido a fundición está establecido preferiblemente en 50 mm o mayor, más preferiblemente 150 mm o mayor. Con el fin de que el óxido laminado y alargado tenga un tamaño aproximado, un tamaño del óxido antes de ser sometido a laminado y alargamiento está preferiblemente comprendido entre 10 µm y 25 µm. si el tamaño es demasiado pequeño, el laminado y el alargamiento se hacen difíciles, y si el tamaño es demasiado grande, un estado de dispersión espacial después del laminado se hace lineal de este modo no es preferible desde el punto de vista de presentar el efecto de la presente invención. A continuación, es efectico realizar el laminado a una deformación total real de 0,4 o superior bajo las condiciones de 1000 ºC o por encima y a una velocidad de deformación de 1/seg; y después realizar un laminado a una deformación total real de 0,7 o mayor, bajo las condiciones de 1000 ºC y una velocidad de deformación de 10/seg o mayor. Un mecanismo para esto no está claro, pero se puede suponer como sigue. En una región de alta temperatura de 1000 ºC, el óxido se ablanda y da una pequeña diferencia de dureza cuando se compara con la de la ferrita endurecida. Por lo tanto, el óxido es laminado y alargado mediante laminado y por consiguiente se obtiene un óxido acicular que es preferible para la presente invención. El óxido es apenas laminado y alargado a un temperatura inferior a 1000 ºC, tal como 900 ºC o inferior, se fisura en parte, y el óxido que tiene una morfología razonable acicular se dispersa a un intervalo apropiado en el lámina de acero. Para el laminado, alargamiento y dispersión apropiadas de tal manera, una temperatura de control después del laminado en caliente, una cantidad de deformación para cada región de temperatura y también una velocidad de deformación de manera que se controle el ablandamiento de la ferrita endurecida por trabajo, también es importante. Below, a preferred example of the manufacturing method will be shown for each type of second phase in the steel of the present invention. First, a case in which an oxide is used as the second special phase will be represented. A preferred embodiment includes the rolling and elongation of an oxide by rolling in a hot rolling stage to be modified to a preferable form. To do this, a certain amount of work is required, and a thickness of a cast steel block is preferably set at 50 mm or more, more preferably 150 mm or more. In order that the laminated and elongated oxide has an approximate size, a size of the oxide before being subjected to rolling and elongation is preferably between 10 µm and 25 µm. if the size is too small, the rolling and elongation become difficult, and if the size is too large, a state of spatial dispersion after rolling becomes linear in this way is not preferable from the point of view of presenting the effect of the present invention. Next, it is effective to perform the rolling at a real total deformation of 0.4 or higher under the conditions of 1000 ° C or above and at a deformation rate of 1 / sec; and then perform a rolling at a real total deformation of 0.7 or greater, under the conditions of 1000 ° C and a deformation rate of 10 / sec or greater. A mechanism for this is unclear, but it can be assumed as follows. In a high temperature region of 1000 ° C, the oxide softens and gives a small hardness difference when compared to that of the hardened ferrite. Therefore, the oxide is laminated and elongated by rolling and therefore an acicular oxide is obtained which is preferable for the present invention. The oxide is barely laminated and elongated at a temperature below 1000 ° C, such as 900 ° C or less, is partially cracked, and the oxide having a reasonable acicular morphology is dispersed at an appropriate range in the steel sheet. For proper lamination, elongation and dispersion in such a way, a control temperature after hot rolling, an amount of deformation for each temperature region and also a deformation rate so that the softening of the work-hardened ferrite is controlled It is also important.

Mediante aplicación de temperatura, la cantidad de deformación y las condiciones de velocidad de deformación para el caso del sulfuro, se obtiene un efecto preferible como en el caso del óxido. By application of temperature, the amount of deformation and the deformation speed conditions for the case of the sulfide, a preferable effect is obtained as in the case of the oxide.

A continuación, será ilustrado un caso en el que se utiliza un carburo como segunda fase característica. Next, a case in which a carbide is used as the second characteristic phase will be illustrated.

En este caso, es posible producir un carburo que tenga una configuración más preferible a partir de C y elementos adictivos que están previamente contenidos en el acero mediante tratamiento de calor o similar en los procesos de fabricación. Sin embargo, en la presente invención, se ilustrará un método de utilización de carburización como la configuración más preferible. Mediante el uso de la carburización, como se ha descrito anteriormente, es posible dispersar la segunda fase característica sólo en la superficie de la placa de acero y la concentración de C aumenta gradualmente; de manera que el carburo que tiene un crecimiento de configuración anisotrópica en una orientación preferida se puede formar fácilmente. La condición incluye después del laminado en frío, realizar un tratamiento de carburización a una temperatura comprendida entre 600 y 700 ºC bajo una condición de proporcionar {(tiempo de carburización (seg)) * (temperatura de carburización (ºC))}/{(concentración de gas de carburización (%))*(velocidad de enfriamiento en el tratamiento de carburización (ºC/seg))} ≥ 20, simultáneamente con o después del templado de recristalización, con lo que se incrementa una cantidad de C en 0,0002 % o más. Si la temperatura está fuera del rango anterior la eficiencia de carburización disminuye a un lado de la temperatura baja, y por el contrario si la temperatura es demasiado alta, la configuración del carburo puede ser fácilmente isotrópica. Bajo una condición en la que {(tiempo de carburización (seg)) * (temperatura de carburización (ºC))}/{(concentración de gas de carburización (%))*(velocidad de enfriamiento en el tratamiento de carburización (ºC/seg))} sea 20 o más, se puede conseguir la configuración preferible de la segunda fase. Básicamente, dado que el carburo puede crecer suficientemente con un tratamiento de enfriamiento gradual a una temperatura elevada durante un largo tiempo mientras se suprime en crecimiento de los núcleos de deposición del carburo en una baja concentración de C, el desarrollo de la segunda fase anisotrópica es notable. Sin embargo, cuando la carburización es realizada a una temperatura elevada durante largo tiempo, el C introducido en el acero a partir de una superficie de la placa alcanza en centro de un espesor de placa dispersándose de manera que la promoción del efecto de la presente invención debido a la estructura de múltiples capas anteriormente descrita desaparece. Por lo tanto, de acuerdo con la condición de carburización, es preferible contralar el valor de la fórmula anterior de manera qué solo parte de la superficie sea carburizada. Este valor también depende del espesor de placa y es preferible que sea 500 o menor, más preferible 200 o menor. La condición de atmósfera que incluye el tipo de gas de carburización puede ser generalmente una condición conocida. Además, el método de carburización no está limitado al gas de carburización ilustrado aquí, y se puede aplicar el método de carburización generalmente conocido. Además, el 0,0002 % o más que aumenta la cantidad de C puede parecer muy pequeña como la cantidad aumentada, pero esta cantidad es sufriente para presentar el efecto de la presente invención en consideración de la cantidad aumentada en una capa de superficie de la placa de acero en una material extra delgado. In this case, it is possible to produce a carbide having a more preferable configuration from C and addictive elements that are previously contained in the steel by heat treatment or the like in the manufacturing processes. However, in the present invention, a method of using carburization as the most preferable configuration will be illustrated. By using carburization, as described above, it is possible to disperse the second characteristic phase only on the surface of the steel plate and the concentration of C gradually increases; so that carbide having an anisotropic configuration growth in a preferred orientation can be easily formed. The condition includes after cold rolling, performing a carburization treatment at a temperature between 600 and 700 ° C under a condition of providing {(carburization time (sec)) * (carburization temperature (ºC))} / {( concentration of carburization gas (%)) * (cooling rate in the carburization treatment (ºC / sec))} ≥ 20, simultaneously with or after recrystallization tempering, thereby increasing a quantity of C by 0, 0002% or more. If the temperature is outside the previous range the carburization efficiency decreases to one side of the low temperature, and conversely if the temperature is too high, the carbide configuration can be easily isotropic. Under a condition where {(carburization time (sec)) * (carburization temperature (ºC))} / {(concentration of carburization gas (%)) * (cooling rate in the carburization treatment (ºC / sec))} be 20 or more, the preferable configuration of the second phase can be achieved. Basically, since carbide can grow sufficiently with a gradual cooling treatment at an elevated temperature for a long time while suppressing growth of the carbide deposition nuclei at a low concentration of C, the development of the second anisotropic phase is remarkable. However, when the carburization is carried out at a high temperature for a long time, the C introduced into the steel from a plate surface reaches in the center of a plate thickness dispersing so that the promotion of the effect of the present invention due to the multilayer structure described above disappears. Therefore, according to the condition of carburization, it is preferable to compare the value of the above formula so that only part of the surface is carburized. This value also depends on the plate thickness and is preferably 500 or less, more preferably 200 or less. The atmosphere condition that includes the type of carburization gas can generally be a known condition. In addition, the carburization method is not limited to the carburization gas illustrated herein, and the generally known carburization method can be applied. In addition, 0.0002% or more that increases the amount of C may seem very small as the amount increased, but this amount is sufficient to present the effect of the present invention in consideration of the amount increased in a surface layer of the Steel plate in an extra thin material.

Además, mediante la aplicación de la condición de carburización a una condición en la que un nitruro obtenido por nitruración es utilizado para la segunda fase, se puede obtener el efecto preferible similar al carburo. A saber, la condición incluye después del laminado en frío, realizar un tratamiento de nitruración a una temperatura comprendida entre 600 y 700 ºC bajo una condición de dar {(tiempo de nitruración (seg)) * (temperatura de nitruración (ºC))}/{(concentración de gas de nitruración (%))*(velocidad de enfriamiento en el tratamiento de nitruración (ºC/seg))} ≥ 20, simultáneamente con o después de un templado de recristalización, con lo que se Furthermore, by applying the carburization condition to a condition in which a nitride obtained by nitriding is used for the second phase, the preferable effect similar to carbide can be obtained. Namely, the condition includes after cold rolling, to perform a nitriding treatment at a temperature between 600 and 700 ° C under a condition of giving {(nitriding time (sec)) * (nitriding temperature (ºC))} / {(concentration of nitriding gas (%)) * (cooling rate in nitriding treatment (ºC / sec))} ≥ 20, simultaneously with or after a recrystallization tempering, thereby

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Claims (1)

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ES07741011.6T 2006-04-04 2007-04-04 Extra-thin hard steel sheet and its manufacturing method Active ES2575997T3 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2006102766 2006-04-04
JP2006102766 2006-04-04
PCT/JP2007/057575 WO2007116913A1 (en) 2006-04-04 2007-04-04 Very thin hard steel sheet and method for producing the same

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KR20080106330A (en) 2008-12-04
EP2003221A1 (en) 2008-12-17
EP2003221A4 (en) 2014-12-03
JP5058978B2 (en) 2012-10-24
JPWO2007116913A1 (en) 2009-08-20
CN101415851A (en) 2009-04-22
EP2003221B1 (en) 2016-05-25
CN101415851B (en) 2011-06-08
KR101065545B1 (en) 2011-09-19

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