CN103443317A - Steel sheet for hot-tamped member and process for producing same - Google Patents

Steel sheet for hot-tamped member and process for producing same Download PDF

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Publication number
CN103443317A
CN103443317A CN2012800138006A CN201280013800A CN103443317A CN 103443317 A CN103443317 A CN 103443317A CN 2012800138006 A CN2012800138006 A CN 2012800138006A CN 201280013800 A CN201280013800 A CN 201280013800A CN 103443317 A CN103443317 A CN 103443317A
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China
Prior art keywords
steel sheet
steel plate
hot
layer
hardness
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CN2012800138006A
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Chinese (zh)
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棚桥浩之
真木纯
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Nippon Steel Corp
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Nippon Steel Corp
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    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0226—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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation 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
    • 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
    • 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
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12736—Al-base component
    • Y10T428/1275—Next to Group VIII or IB metal-base component
    • Y10T428/12757—Fe
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

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  • Heat Treatment Of Sheet Steel (AREA)

Abstract

Provided is a steel sheet for giving members by hot stamping, the members having excellent fatigue properties equal to those of ordinary high-strength steel sheets that have the same strength as the steel sheet. Also provided is a process for producing the steel sheet. The steel sheet for hot-stamped members contains, in terms of mass%, 0.15-0.35% C, 0.01-1.0% Si, 0.3-2.3% Mn, and 0.01-0.5% Al, with the remainder comprising Fe and incidental impurities, wherein the impurities comprise up to 0.03% P, up to 0.02% S, and up to 0.1% N as chemical components. The steel sheet is characterized in that the Vickers hardnesses of the steel sheet measured at sites located at a distance of 20 [mu]m from a surface of the steel sheet toward the sheet thickness direction have a standard deviation of 20 or less. This steel sheet is produced through a recrystallization annealing step comprising: a first stage in which a cold-rolled steel sheet obtained by hot-rolling and then cold-rolling a steel that contains the chemical components is heated from room temperature to 600-700 DEG C at an average heating rate of 8-25 DEG C/sec; and a second stage in which the steel sheet is successively heated to 720-820 DEG C at an average heating rate of 1-7DEG C/sec.

Description

Steel sheet for hot pressed member and manufacture method thereof
Technical field
The present invention relates to be suitable for steel sheet for hot pressed member and the manufacture method thereof as the pressure sintering of one of manufacturing process that can access high-intensity member.
Background technology
In fields such as automobile or building machineries, the effort reduced towards the quality of having used high-strength material is being carried out energetically.Automobile for example, follow the car body mass penalty with multifunction of guaranteeing of crashworthiness with counteracting, and then to make fuel efficiency improve the quantity discharged of cutting down carbonic acid gas be purpose, and the usage quantity of high tensile steel plate stably increases.
In the trend enlarged in the use of such high tensile steel plate, maximum problem be in the situation that the intensity that improves steel plate inevitably, be called as remarkableization of the phenomenon of " shape freezing deteriorated ".This phenomenon, be to increase because the springback capacity after being shaped is accompanied by high strength, thereby obtain the become general name of very difficult phenomenon of target shape.For addressing this problem, carried out appending (for example pressure-sizing (restrike)) or changing article shape of the unwanted manufacturing procedure of low-intensity material (shape freezing excellence or unquestioned material).
As a kind of method that solves such situation, the thermo shaping method that is called as hot pressing (hot stamping, hot stamping) method receives publicity.This is that (temperature (being generally the temperature that becomes the austenite phase) by steel plate (machined material) being heated to appointment reduces intensity, make to be shaped and become easy) after, for example, with machined material, being in a ratio of the die forming of low temperature (room temperature), thus when easily giving shape, the method for the intensity of the goods after having been utilized the chilling thermal treatment (quenching) of both temperature heads to guarantee to be shaped.
Some technology have been reported about steel plate and its manufacturing process of being suitable for such pressure sintering.
In patent documentation 1, disclose following steel plate: the pass between the amount of the element by steel plate is contained and the amount of element ties up to the scope of appointment, can access the member of impact characteristics and delayed fracture excellent after thermoforming processing (with the hot pressing synonym).
In patent documentation 2, following method is disclosed: by and the amount of the amount of the above-mentioned element that similarly makes steel plate contain and element between pass tie up to the scope of appointment, thereby and the heating of carrying out in nitriding atmosphere or carburizing atmosphere before the shaping of steel plate obtain high-strength parts.
In patent documentation 3, recorded and narrated by chemical composition and the microstructure of regulation steel plate, thereby and limited heating condition and molding condition obtains the method for hot-pressed product with high productivity.
Recently, its availability of pressure sintering is by extensive cognition, and the member of studied application also relates to many-side.Wherein, for example also start to comprise the parts that travel as automobile, not only as the intensity of parts, its fatigue characteristic are also the parts of one of important necessary characteristic.
The fatigue characteristic of steel plate, corresponding to static strength, improve, although therefore for the steel plate (goods) that adopts pressure sintering to carry out high strength, can expect corresponding fatigue characteristic, if but (control the chemical composition, manufacture method of steel plate and the high tensile steel plate manufactured with the steel plate that does not adopt pressure sintering of same intensity, below, be called " common high tensile steel plate ") (goods) compare, and according to the former fatigue characteristic of creating conditions, than the latter is poor, become obvious.
In addition after detailed research, found to compare with the deviation (fluctuation, uneven) of the hardness of the most surface of " common high tensile steel plate ", use pressure sintering to be carried out large this feature of deviation of hardness of most surface of the steel plate (goods) of high strength, drawn deviation and the related conclusion of fatigue characteristic of this hardness.
Although the deviation of hardness and the relation of fatigue characteristic are not necessarily clear and definite, but for example, impact for otch (stress concentration) susceptibility of fatigue characteristic in the high strength component (tensile strength is more than 1500MPa) that picture is manufactured by pressure sintering is very big, the index that the deviation of therefore inferring this hardness is equal to mutually with the Flatness on top layer just.
So, studied the result of the technology of the deviation for reduce as far as possible hardness after hot pressing, found that the deviation of the surface hardness of the steel plate before hot pressing has impact.Standing in the document that steel plate that such viewpoint uses for hot pressing studied not yet finds.
Patent documentation 1 has been recorded and narrated and take a certain of Ni, Cu, Sn and use steel plate as thermoforming essential, that improved impact characteristics and delayed fracture characteristic processing, but does not mention for the deviation of the surface hardness before fatigue characteristic and hot pressing.
In patent documentation 2, thereby relate to the document of the technology by heated the intensity that improves molding in carburizing atmosphere, but do not mention for the deviation of the surface hardness before fatigue characteristic and hot pressing.Heating in carburizing atmosphere is essential, compare manufacturing cost with the atmosphere heating and rise, in addition, in the situation that use carbon monoxide as carbon source, also worry for guaranteeing that operational security needs a lot of expenses, thinks and can not become the technology that can implement simply.
Deviation for the surface hardness before fatigue characteristic and hot pressing in patent documentation 3 does not mention yet.
With respect to this as the technology that obtains having the steel plate of using with the hot pressing of the fatigue characteristic of " common high tensile steel plate " same degree, patent documentation 4 is arranged, in addition, although the technology known patent document 5 that the situation of having implemented the steel plate of plating Zn in use is inherent technology to be improved as the fatigue characteristic of the member that makes to adopt pressure sintering to be manufactured.
In patent documentation 4, thereby disclose minuteness particle by making to contain the Ce oxide compound and be dispersed in the slightly inboard technology of improving the fatigue characteristic after hot pressing by surface of steel plate, so even but because need the steel-smelting technology of height to exist those skilled in the art to implement also may not be easy to problem.
The technology of patent documentation 5, relate to the technology of the equipment of hot-pressing technique, if even exist do not have new facility investment those skilled in the art also can't enjoy the problem of its benefit.
Like this, practical situation are, although need steel plate (goods), the steel plate that pressure sintering is used that can guarantee with comparalive ease to carry out with the pressure sintering of the fatigue characteristic of " common high tensile steel plate " same degree of same intensity high strength for adopting, the technology that solves such problem does not find.
Technical literature formerly
Patent documentation
Patent documentation 1: TOHKEMY 2005-139485 communique
Patent documentation 2: TOHKEMY 2005-200670 communique
Patent documentation 3: TOHKEMY 2005-205477 communique
Patent documentation 4: TOHKEMY 2007-247001 communique
Patent documentation 5: TOHKEMY 2007-182608 communique
Summary of the invention
Problem of the present invention is in view of above-mentioned practical situation, a kind of steel sheet for hot pressed member and manufacture method thereof are provided, above-mentioned steel sheet for hot pressed member, when steel plate use heat platen press is manufactured to goods, can become the goods of high tensile steel plate of the fatigue characteristic of the excellence with high tensile steel plate (" common high tensile steel plate ") same degree of manufacturing with the chemical composition of controlling steel plate and/or manufacture method.
The inventor is for solving the conscientiously research repeatedly of such problem.Its result, improve very effective to the fatigue characteristic of the steel plate after hot pressing (goods) if found in scope that near the deviation of the hardness steel plate top layer before hot pressing is appointment.In addition, also find to obtain such steel plate, can reach by the condition of controlling when having carried out cold rolling steel plate recrystallization annealing, thereby and then repetition test completed the present invention.
Main idea of the present invention is as follows.
(1) a kind of steel sheet for hot pressed member, is characterized in that, is the steel plate that contains following chemical composition, in quality %, contains
C：0.15～0.35%、
Si：0.01～1.0%、
Mn:0.3～2.3% and
Al:0.01～0.5%, and,
Its surplus is Fe and inevitable impurity,
As this impurity, be defined as:
Below P:0.03%,
S:0.02% following and
Below N:0.1%,
Standard deviation apart from the Vickers' hardness of the position of this surface of steel plate 20 μ m on the thickness of slab direction is below 20.
(2) according to (1) described steel sheet for hot pressed member, it is characterized in that, in quality %, also contain and be selected from one or more in following chemical composition:
Cr：0.01～2.0%、
Ti：0.001～0.5%、
Nb：0.001～0.5%、
B：0.0005～0.01%、
Mo：0.01～1.0%、
W：0.01～0.5%、
V：0.01～0.5%、
Cu:0.01～1.0% and
Ni：0.01～5.0%。
(3) according to (1) or (2) described steel sheet for hot pressed member, it is characterized in that thering is any of zn-fe alloy layer of the thickness of the plating Zn layer of thickness of plating Al layer, 5 μ m～30 μ m of the thickness of 5 μ m～50 μ m or 5 μ m～45 μ m on the surface of above-mentioned steel plate.
(4) a kind of manufacture method of steel sheet for hot pressed member, is characterized in that, in the operation of the cold-rolled steel sheet recrystallization annealing that will contain following chemical composition, comprising:
Average rate of heating with 8～25 ℃/secs is heated to temperature M(℃ from room temperature) first stage; With
Then with the average rate of heating of 1～7 ℃/sec, be heated to temperature S(℃) subordinate phase,
Temperature M(℃) be 600～700(℃),
Temperature S(℃) be 720～820(℃),
Above-mentioned chemical composition, in quality %, contains
C：0.15～0.35%、
Si：0.01～1.0%、
Mn:0.3～2.3% and
Al:0.01～0.5%, and,
Its surplus is Fe and inevitable impurity,
As this impurity, be defined as:
Below P:0.03%,
S:0.02% following and
Below N:0.1%.
(5) according to the manufacture method of (4) described steel sheet for hot pressed member, it is characterized in that, above-mentioned steel is in quality %, also contains and is selected from one or more in following chemical composition:
Cr：0.01～2.0%、
Ti：0.001～0.5%、
Nb：0.001～0.5%、
B：0.0005～0.01%、
Mo：0.01～1.0%、
W：0.01～0.5%、
V：0.01～0.5%、
Cu:0.01～1.0% and
Ni：0.01～5.0%。
(6) according to the manufacture method of (4) or (5) described steel sheet for hot pressed member, it is characterized in that, the hot rolling rate of above-mentioned hot-rolled process is 60～90%, and the cold rolling rate of above-mentioned cold rolling process is 30～90%.
(7) manufacture method of the described steel sheet for hot pressed member of any one of basis (4)～(6), is characterized in that, also comprises: continue with above-mentioned recrystallization annealing operation, above-mentioned steel plate is immersed in the Al bath, form the operation of plating Al layer on surface.
(8) manufacture method of the described steel sheet for hot pressed member of any one of basis (4)～(6), is characterized in that, also comprises: continue with above-mentioned recrystallization annealing operation, above-mentioned steel plate is immersed in the Zn bath, form the operation of plating Zn layer on surface.
(9) manufacture method of the described steel sheet for hot pressed member of any one of basis (4)～(6), it is characterized in that, also comprise: with above-mentioned recrystallization annealing operation, continue, above-mentioned steel plate is immersed in the Zn bath, after surface forms plating Zn layer, further be heated to below 600 ℃, form the operation of zn-fe alloy layer on above-mentioned surface.
Steel sheet for hot pressed member of the present invention, can be with existing ironmaking equipment manufacture, use in addition steel sheet for hot pressed member of the present invention, the fatigue characteristic of the molding (hot pressed member) obtained with extensively universal hot-press equipment shaping are also equal with " the common high tensile steel plate " of same intensity, therefore have the effect of the range of application of expansion hot pressed member (parts).
The accompanying drawing explanation
Fig. 1 means the stereographic map of the flat-plate compressed molding jig of using for the pressure sintering of embodiments of the invention.
Fig. 2 means the figure of fatigue sample.
Fig. 3 means that the be full of cracks in the fatigue sample with shown in Fig. 2 makes progress the measurement of hardness of regional same size with in test specimen, has measured the stereographic map in the place of hardness.
Fig. 4 means that the safe range of stress of the steel sheet for hot pressed member of embodiment 1 compares the associated figure of the standard deviation of the hardness front with hot pressing.
Fig. 5 is that pattern ground means to adopt pressure sintering to be configured as the stereographic map of the steel plate (member) of shape for hat.
Fig. 6 means that the safe range of stress of the steel sheet for hot pressed member of embodiment 2 compares the associated figure of the standard deviation of the hardness front with hot pressing.
Embodiment
The inventor uses in quality %, and the steel plate that contains C:0.23%, Si:0.5% and Mn:1.6% is made hot pressed member, has carried out estimating the research of its characteristic.Fatigue characteristic are also one of its characteristics, in this process, although found the hot pressed member that chemical composition is identical and the almost identical fatigue characteristic of tensile strength are different of existence steel plate.So, probe after their difference, learn that near the deviation of the hardness top layer of hot pressed member there are differences.Therefore, further also make the recrystallize condition of chemical composition and/or cold-rolled steel sheet change widely the fatigue characteristic of having investigated hot pressed member, the fatigue characteristic of having found hot pressed member exist strong associated with the deviation of its surface hardness, obtain the hot pressed member of excellent in fatigue characteristics, it is effective making the deviation of the surface hardness of the front steel plate of hot pressing in the scope of appointment, and then, in order to obtain such steel plate, can the condition by will carry out recrystallization annealing to the steel plate of cold rolling mistake the time be controlled in the scope of appointment.
Details are set forth among embodiment, are based on such experimental result, thereby experimentally clear and definite suitably scope and the annealing conditions of the deviation of hardness have completed the present invention.
the chemical composition of steel plate
At first, the chemical composition for steel plate describes.At this, for " % " of composition, refer to quality %.
<C：0.15～0.35%>
C is adopting pressure sintering by most important element aspect the steel plate high strength.In order to obtain at least intensity of 1200MPa left and right after hot pressing, must contain more than 0.15%.On the other hand, if contain, surpass 0.35%, thereby worry that the deteriorated of toughness take 0.35% as the upper limit.
<Si：0.01～1.0%>
Si is the solution strengthening element, until 1.0% can effectively utilize.If but more than containing it, produce unfavorable condition while worrying to carry out chemical conversion treatment reason or application after shaping, therefore take 1.0% as the upper limit.There is no particular limitation for lower limit, can access effect of the present invention.Only can improve the steel-making load so be made as more than 0.01% of benchmark that results from deoxidation and contain but exceed to reduce necessarily.
<Mn：0.3～2.3%>
Mn, outside playing a role as the solution strengthening element equally with Si, is the useful element that improves the hardenability of steel plate, and its effect can confirm more than 0.3%.Even but contain, to surpass 2.3% effect also saturated so take 2.0% as the upper limit.
<P:0.03% is following >,<S:0.02% is following >
Two elements are all inevitable impurity, because meeting exerts an influence and therefore must be limited in above-mentioned scope hot workability.
<Al：0.01～0.5%>
Therefore Al can contain more than 0.01% as deoxidant element due to suitable.If be made as 0.5% but contain in a large number mechanical properties so its upper limit that can form thick oxide compound infringement steel plate.
<N:0.1% is following >
N is inevitable impurity, owing to easily being combined with Ti, B and therefore must being controlled not reduce the target effect of those elements, so long as be tolerable below 0.1%.Be preferably below 0.01%.Therefore on the other hand, exceeding reduction meeting necessarily causes huge load to take to steel making working procedure 0.0010% to be lower limit benchmark gets final product.
<Cr：0.01～2.0%>
Cr is that therefore the element with the effect that improves hardenability can suitably be used.It is obviously more than 0.01% that its effect becomes.On the other hand, even surpass 2.0% ground, to add its effect also saturated so take 2.0% as the upper limit.
<Ti：0.001～0.5%>
So the effect that Ti plays by the formation of its nitride the effect that plays consistently aftermentioned B is the element that can effectively utilize.Need the interpolation more than 0.001% for this reason, if but add nitride becomes superfluous superfluously, and can cause the deteriorated of toughness and shear surface proterties so take 0.5% as the upper limit.
<Nb：0.001～0.5%>
Therefore Nb forms carbonitride raising intensity is the element that can effectively utilize.Its effect can confirm more than 0.001%, if but therefore the misgivings that contain the controllability that surpasses 0.5% existence infringement hot rolling take 0.5% as the upper limit.
<B：0.0005～0.01%>
B is the element that improves hardenability, in its effect more than 0.0005%, becomes obvious.On the other hand, superfluous interpolation can cause the reduction of the deteriorated and ductility of hot workability therefore to take 0.01% as the upper limit.
<Mo：0.01～1.0%>、<W：0.01～0.5%>、<V：0.01～0.5%>
These elements are all that therefore the element with the effect that improves hardenability can suitably be used.Its effect becomes obviously, and which is all more than 0.01% for.On the other hand, because be the element of high price, the saturated concentration of effect of take so preferred is the upper limit.For Mo, being 1.0%, is 0.5% for W and V.
<Cu：0.01～1.0%>
Cu has the effect of the intensity that improves steel plate by adding Cu more than 0.01%.Therefore but superfluous interpolation can damage the surperficial grade of hot-rolled steel sheet take 1.0% as the upper limit.
<Ni：0.01～5.0%>
Therefore Ni has the effect that improves hardenability is the element that can effectively utilize, and its effect is becoming obvious more than 0.01%.On the other hand, due to the element that is high price, therefore take its effect saturated 5.0% be the upper limit.In addition, also there is the effect that the surperficial grade that suppresses the hot-rolled steel sheet caused by above-mentioned Cu reduces, therefore preferably and Cu contain simultaneously.
Moreover the composition beyond above-mentioned in the present invention is Fe, allow the inevitable impurity of sneaking into from the melting raw material of scrap iron etc. or refractory materials etc.
the deviation of surface of steel plate hardness
Deviation for surface of steel plate hardness describes.
At first, determine that for the hardness of surface of steel plate (mensuration) method is set forth.
The hardness of surface of steel plate, it is desirable to should be using surface of steel plate as top, thickness of slab direction and vertical direction one sclerometer (for example Vickers hardness tester) of applying is measured, but, for identification impression (precision is measured the size of impression well) significantly, need certain processing such as effects on surface (mensuration face) is ground.For example, in such processing (mechanicalness grinding), from original surface, at least tens of μ m left and right is removed.In addition, even the chemical ground such as use acid grind also not variation on removing, mostly understand on the contrary Flatness and worsen.Therefore, determine that by such method the hardness of (mensuration) surface of steel plate is unpractical.
So being chosen on the cross section of the thickness of slab direction that is parallel to steel plate, the present inventors determine hardness.Surface of steel plate can not measured without processing (can not be removed) like this.But in this case, the position that available sclerometer as above is measured just becomes the summary inside apart from surface along the thickness of slab direction.So as time good scheme, thereby by obtaining the information closer to surperficial position to hang down the additional impression of load as much as possible.
Specifically can be with reference to Fig. 3.At first will measure face (steel plate cross section) and grind to form minute surface.Use Vickers hardness tester, test load (being pressed into the load of pressure head) is made as 10gf, and the time of being pressed into is 15 seconds, and locating of thickness of slab direction elected as apart from surface of steel plate 20 μ m places." hardness of surface of steel plate " used in this specification sheets refers to the definite hardness of method based on above.
In addition, as the top layer of steel plate, there is the hardness of the surface of steel plate in any steel plate of plating Al layer, plating Zn layer and zn-fe alloy layer, in the position finding of boundary (interface) the 20 μ m of distance coating and steel plate.
For example, the plating Al layer of the steel plate used in embodiment, think by usining Al as the layer in the outside of principal constituent and being considered to layer two-layer formation of the inboard (steel plate side) of the responding layer of Al and Fe, therefore in the position finding hardness of boundary 20 μ m on the thickness of slab direction of the layer apart from inboard and steel plate, the surface hardness using it as steel plate.
Then, the plating Zn layer of the steel plate used in embodiment, think that Zn forms as the inboard of the layer in the outside of principal constituent and Fe and the responding layer of the Al in Zn bathes by indium addition layer two-layer by usining, therefore in the position finding hardness of boundary 20 μ m on the thickness of slab direction of the layer apart from inboard and steel plate, the surface hardness using it as steel plate.
Moreover, the zn-fe alloy layer of the steel plate used in embodiment, think to be formed by a plurality of alloy layers that form with Zn and Fe, therefore in the position finding hardness of boundary 20 μ m on the thickness of slab direction of the layer apart from the most inboard and steel plate, the surface hardness using it as steel plate.
For the purpose of the deviation of obtaining hardness, in the zone corresponding to fatigue cracking progress zone (21) of the fatigue sample shown in Fig. 2, carried out above-mentioned mensuration.Fig. 3 means the stereographic map in the place of measuring hardness.On the surface of distance steel plate or the position of interface 20 μ m on the thickness of slab direction of steel plate and coating, be pressed into the pressure head of Vickers hardness tester.As shown in Figure 3, with the impression interval of 0.1mm, this is operated in to each mensuration test portion of the direction parallel with the surface of steel plate and carry out 300 points (in measured length, spreading all over 30mm) (the first mensuration face).And then carry out same operation for the first mensuration face from producing in advance at a distance of 5mm another (second mensuration face).
So for amounting at 600, obtain hardness, calculate and using this as overall standard deviation, as the index of deviation.
Moreover, with above-mentioned measured length 30mm 2 positions at a distance of 5mm, determine so that regional consistent with the be full of cracks progress of fatigue sample described later.
In the experiment of following embodiment explanation, for the steel plate of the ratio of the safe range of stress after hot pressing demonstration more than 0.4 and the steel plate below it, compared the deviation of the hardness on steel plate top layer, the former standard deviation is below 40.So investigate in further detail, the deviation of clear and definite hardness after hot pressing becomes below 40 in standard deviation, is to use the same method the deviation of hardness of the steel plate before definite hot pressing when counting below 20 with standard deviation.
In the present invention, being defined as apart from the standard deviation of surface of steel plate Vickers' hardness of the position of 20 μ m on the thickness of slab direction is to be based on such experimental result below 20 to come.
the manufacture method of steel sheet for hot pressed member
Finally, the manufacture method for steel sheet for hot pressed member of the present invention describes.
Steel sheet for hot pressed member of the present invention based on well-established law made steel, casting, hot rolling, pickling process, cold rolling each operation, make cold-rolled steel sheet.After carrying out the adjustment of chemical composition in steel making working procedure in above-mentioned scope of the present invention, make slab in continuous casting working procedure, for example, with the Heating temperature below 1300 ℃, start hot rolling, 900 ℃ of left and right, rolling is completed.The coiling temperature is such as selecting 600 ℃ etc.The hot rolling calibration is 60～90% to get final product.Through pickling process, carry out cold rolling.The rolling rate can be selected from 30～90% scope.
For making the annealing operation of the cold-rolled steel sheet recrystallize of manufacture like this, be very important.Annealing operation is used continuous annealing apparatus to carry out, and comprises that the average rate of heating with 8～25 ℃/secs is heated to temperature M(℃ from room temperature) first stage and then with the average rate of heating of 1～7 ℃/sec, be heated to temperature S(℃) the formation in two stages of subordinate phase.At this, temperature M is 600～700(℃), temperature S is 720～820(℃) be necessary.These conditions are based on that the experimental result that illustrates in the embodiment of following record determines.
Although in the situation that with such condition recrystallization annealing, can access the reason that the standard deviation in distance surface of steel plate Vickers' hardness of the position finding of 20 μ m on the thickness of slab direction is the steel plate that deviation below 20, hardness is little might not be clear, but because preferably the distribution of crystallization particle diameter as far as possible evenly and the size of carbide and distribute even as far as possible too, so infer as follows from the distribution in recrystal grain footpath and the size of carbide and the viewpoint of distribution.
Because the recrystallization process of the steel plate of cold rolling mistake is complicated, the meaning that will have for rate of heating and the maximum heating temperature under this rate of heating of the phenomenon that is called recrystallize separately independently explanation be inappropriate.Therefore, at first for the first stage, for example, for some temperature M(℃), the situation that the consideration rate of heating is little and large situation.Think in the situation that the former although to be the density (relatively) of the little recrystallization nucleus of rate of heating low; each recrystal grain is freely grown; but approaching M(℃) high-temperature area; small recrystal grain generates from remaining non-recrystallization zone; arrive M(℃ in the temperature of steel plate) stage, become the state that crystal grain that (relatively) is large and little crystal grain mix.
On the other hand; think in the situation that the latter to be rate of heating large; the density of recrystallize nucleus is high; a lot of recrystal grains are grown rapidly, the crystal boundary connection that becomes, and then approaching M(℃) high-temperature area; the result of the competition of the growth of each recrystal grain; crystal grain with specific crystalline orientation eat crystalline orientation with other crystal grain and grow, therefore arrive M(℃) stage, still can become the state that large crystal grain and little crystal grain mix.Therefore, in temperature, arrive M(℃) stage, just make recrystal grain be connected to each other suitable rate of heating and the M(℃ of crystal boundary) combination, become necessary for the distribution that realizes more uniform recrystal grain footpath.Think 8～25 ℃/secs and the temperature M(℃ of average rate of heating of first stage) 600～700 ℃ be the combination that meets this suitable condition.
Next, in the temperature of steel plate, arrive M(℃) after for the competition of the growth that suppresses recrystal grain, the rate of heating of subordinate phase need to be less than the first stage.Then from temperature M(℃) to temperature S(℃) temperature province the forming and come to life again of the carbide that caused by the diffusion of carbon, so the top temperature S(℃ of annealing operation) setting and until the combination of the rate of heating of this temperature have great importance.
For some S(℃), think in the situation that rate of heating is little, at temperature M(℃) the lower carbide existed similarly grows, therefore becomes and arrive temperature M(℃) the carbide of the sizes that exists of stage keep the same steel plate existed diversifiedly.On the other hand, in the situation that rate of heating is large, little carbide disappears and causes the growth of large carbide, and the size of carbide approaches evenly relatively, but density diminishes, and therefore causes resulting from hardness inhomogeneous of steel plate of carbide.To this, think in the situation that the rate of heating of subordinate phase and temperature S(℃) combination suitable, the growth of little carbide preferentially occurs, and becomes the steel plate that the more uniform carbide of size disperses with suitable density, and the inhomogeneous of hardness of steel plate of carbide of therefore resulting from diminishes.Think 1～7 ℃/sec and the temperature S(℃ of rate of heating of subordinate phase) 720～820 ℃ be the combination that meets this suitable condition.
After arriving temperature S, temperature S can be kept the short period of time, also ensuing refrigerating work procedure can be entered immediately.In the situation that keep temperature S, be preferably below 180 seconds from the viewpoint hold-time of thickization that suppress the crystallization particle diameter, more preferably below 120 seconds.
There is no particular limitation for the speed of cooling from temperature S in refrigerating work procedure, but preferably avoid cooling fast more than 30 ℃/secs.Therefore, the speed of cooling from temperature S is lower than 30 ℃/secs, is preferably below 20 ℃, more preferably below 10 ℃.This is that the steel plate of using because of hot pressing is processed to designated shape in hot pressing by shearing mostly, worries that cooling meeting improves the cause that shear-type load makes the Efficiency Decreasing of production fast.
After annealing, can be cooled to room temperature, also can in cooling, impregnated in melting Al bath and form plating Al layer.
Melting Al bathes the Si that can contain 0.1～20%.
The Si contained in plating Al layer, can hanker the Al that produces and the reaction of Fe brings impact to adding before carrying out hot pressing.There is the danger of the press formability of infringement coating itself in excessive reaction, and the inhibition of excessive reaction on the other hand worries to cause the risk of adhering to of Al to compacting tool set.For fear of such problem, the Si in plating Al layer is preferably 1～15%, and more preferably 3～12%.
In addition, also can be after annealing cooling in impregnated in melting Zn and form plating Zn layer in bathing.
And then, after also can being immersed in melting Zn and forming plating Zn layer in bathing, be heated to below 600 ℃ and form the zn-fe alloy layer.
In bathing, melting Zn can contain 0.01～3% Al.
The existence of this Al, affect the reaction of Zn and Fe consumingly.In the situation that form plating Zn layer, the responding layer of Fe and Al becomes obstruction, suppresses the phase mutual diffusion of Zn and Fe.On the other hand, the zn-fe alloy layer is by the alloy layer that is rich in Zn (ζ phase, δ 1 phase) be rich in the alloy layer (Γ of Fe 1phase, Γ phase) form, the adaptation of the former and substrate iron is good but workability is poor, latter's excellent workability but adaptation is insufficient.Therefore, need to make by the component ratio of suitably controlling this 4 phase and meet target property (preferential adaptation, preferential workability or make both balances etc.), thereby it can be undertaken by making 0.01～3% Al contain the diffusion of controlling Fe in melting Zn bathes.Be made as which type of concentration, the producer can select according to ability and/or the purpose of the equipment of manufacturing.
Although the thickness of plating Al layer, plating Zn layer and zn-fe alloy layer does not affect steel plate after hot pressing or the fatigue characteristic of parts, in the situation that excessively thick, worry is brought impact to compression moulding.As shown in embodiment, in the situation that the thickness of plating Al layer surpasses the generation that 50 μ m confirm adhesion (か じ り) phenomenon, in the situation that the thickness of plating Zn layer frequently occurs to the adhesion of mould over 30 μ m Zn, in the situation that the cracking that the thickness of zn-fe alloy layer surpasses 45 μ m alloy layers is visible etc. everywhere, infringement productivity.Therefore preferably the thickness of these layers is elected respectively as to plating Al layer: below 50 μ m, plating Zn layer: below 30 μ m, zn-fe alloy layer: below 45 μ m.
In the situation that these coating are thin, although fully out of question on plasticity, from the corrosion proof viewpoint as giving the purpose of these coating, preferably the lower limit of each coating is set as follows.That is, plating Al layer: more than being preferably 5 μ m, more preferably more than 10 μ m, plating Zn layer: more than being preferably 5 μ m, more preferably more than 10 μ m, zn-fe alloy layer: more than being preferably 5 μ m, more preferably more than 10 μ m.
Embodiment
Below explain the present invention based on embodiment.
(embodiment 1)
Refined and cast the steel disc a～f with the chemical composition shown in table 1.These steel discs are heated to 1250 ℃ and carry out hot-rolled process, the temperature that completes of 900 ℃, obtain the hot-rolled steel sheet of thickness 3.2mm at the coiling temperature of 600 ℃.By the cold rolling cold-rolled steel sheet that obtains thickness 1.6mm after this hot-rolled steel sheet pickling.
By above-mentioned cold-rolled steel sheet recrystallization annealing, obtain the steel sheet for hot pressed member 1～32 shown in table 3 with the condition of i～xviii of record in table 2.Produce 2 measurement of hardness test specimens hot pressing from its part.Test specimen is produced position.
The average rate of heating 1(first stage in table 2) and average rate of heating 2(subordinate phase), mean respectively from room temperature to temperature M(℃) and from temperature M(℃) to temperature S(℃) average rate of heating.
These steel sheet for hot pressed members after 10 minutes, by flat-plate compressed molding jig clamping for the experiment with shown in Fig. 1, thereby are carried out to hot pressing 900 ℃ of maintenances.Each steel sheet for hot pressed member carries out the hot-pressing processing of 10 pieces.Produce 2 tensile test specimens in accordance with the regulation of No. JIS5 and 2 test specimens for measurement of hardness (with main points identical before hot pressing) from wherein one piece.Then produce the fatigue sample shown in each 2 pieces of Fig. 2 from 9 pieces of being left, amount to 18 pieces.For the working method of producing, by electrodischarge machining(E.D.M.), undertaken.
Carry out tension test, obtained tensile strength sigma b(mean values of 2 tensile test pieces).On the other hand, use 18 pieces of test specimens to carry out the plain bending fatigue experiment, carried out 1 * 10 7inferior time intensity σ wdetermine.Test conditions is stress ratio-1, recurrence rate 5Hz.
The measurement of hardness test specimen is the test specimen that it(?) all will the cross section parallel with the rolling direction of cold-rolled steel sheet before and after the hot pressing grinds to form minute surface.
Use Vickers hardness tester (HM-220D of the ミ of Co., Ltd. Star ト ヨ system) to measure the hardness apart from 20 μ m inside on the thickness of slab direction, surface of these test specimens.Loading of pressing in is 10gf, and the time of being pressed into is 15 seconds, and the measuring interval of the direction parallel with surface selects 0.1mm to measure 300 points.
Similarly measure for 2 test specimens, from the data that amount to the Vickers' hardness of 600, fall into a trap and calculated the standard deviation of hardness.
In table 3, standard deviation and the tensile strength sigma of the hardness before expression steel symbol, treatment condition, hot pressing b(mean values of 2), intensity σ w, safe range of stress compares σ w/ σ bstandard deviation with hardness after hot pressing.Safe range of stress is compared to σ w/ σ bassociated Fig. 4 that is shown in the standard deviation of hardness before hot pressing.
Learn the tensile strength sigma of the steel plate after hot pressing bin the steel plate (symbol b) of same chemical composition, by the recrystallization annealing condition, affected hardly.On the other hand, fatigue characteristic (σ w/ σ b) be subject to very doughtily the impact of recrystallization annealing condition.
Used in the steel plate of i, iii, iv, vii, viii, xv and xviii of annealing conditions of the present invention, in the scope of the tensile strength of about 1200～1500MPa, obtained relatively high fatigue characteristic, the safe range of stress more than 0.4 is than (σ w/ σ b).On the other hand, take in the steel plate of extraneous condition annealing of the present invention the safe range of stress that obtains than the inferior grade that is 0.3 left and right.
Such difference is that safe range of stress exists associated than the standard deviation of the hardness with after hot pressing, depend on significantly the standard deviation of the front hardness of hot pressing simultaneously, as shown in No.1～6,8,9,12,13,16,17,20,21 and 23～28, in the situation that the standard deviation of hardness is below 20, can accesses and there are excellent fatigue characteristic the hot pressed member of (high safe range of stress ratio) becomes clear and definite.
In addition, become the condition of the recrystallization annealing of the steel plate below 20 as the standard deviation for obtaining the hardness before hot pressing, clear and definite is that the average rate of heating had with 15～25 ℃/secs is heated to temperature M(℃ from room temperature) first stage and then with the average rate of heating of 2～5 ℃/secs, be heated to temperature S(℃) subordinate phase, M is 620～680(℃), S is 780～820(℃).
Table 1
The steel symbol C Si Mn P S Al ?N Other
?a 0.25 0.7 1.9 0.02 0.002 0.03 0.004 Ti:0.03、B.0.003
b 0.23 0.5 1.6 0.02 0.002 0.03 0.003 ?
c 0.21 0.3 1.4 0.02 0.002 0.03 0.002 B：0.004
d 0.20 0.2 1.2 0.02 0.002 0.03 0.004 Cr：0.2、Ti：0.02、B：0.002
e? 0.18 0.2 1.3 0.02 0.002 0.03 0.003 Cr:1.4、Ti:0.02、B:0.002
?f 0.15 0.3 1.1 0.02 0.002 0.03 0.003 Cr:0.1、B:0.004
Unit is quality %.
Figure BDA0000383256180000171
Table 3
Figure BDA0000383256180000181
Draw outside numeral scope of the present invention
(embodiment 2)
Refined and cast the steel disc 2a～2h with the chemical composition shown in table 4.These steel discs are obtained to the hot-rolled steel sheet of thickness 3.0mm with the condition identical with embodiment 1.By cold rolling one-tenth 1.2mm after these hot-rolled steel sheet pickling.
Those steel plates are obtained to the steel plate that hot pressed member is used by i, the ix of table 2 and the condition recrystallization annealing of xviii.
Produced from those steel plates the test specimen that measurement of hardness is used with the main points identical with embodiment 1.
These steel sheet for hot pressed members after 5 minutes, are configured as to shape for hat Fig. 5 shown in by pressure sintering 900 ℃ of maintenances.As shown in the drawing, produced the fatigue sample shown in Fig. 2 and JIS5 tensile test specimen from crown section.
Use these test specimens, with the main points identical with embodiment 1, obtained the standard deviation of the hardness before hot pressing and the tensile strength sigma of the steel plate after hot pressing (member) b(mean values of 2) and 1 * 10 7inferior time intensity σ w.
By their table 5 that the results are shown in.Safe range of stress is compared to σ w/ σ bassociated Fig. 6 that is shown in the standard deviation of hardness before hot pressing.
In the condition i with in scope of the present invention and xviii carry out the steel sheet for hot pressed member of recrystallization annealing, even the steel plate that contains Mo, W, V, Cu and Ni, the deviation of the hardness on the top layer before hot pressing is also in standard deviation below 20.Use them if clear and definite in addition can access safe range of stress than being the hot pressed member of the excellent in fatigue characteristics more than 0.4.
On the other hand, in with extraneous condition ix of the present invention, having carried out the steel plate of recrystallization annealing, the deviation of the hardness on the top layer before hot pressing surpasses 20 in standard deviation, and the safe range of stress ratio of the hot pressed member that uses them to obtain is 0.26～0.31, and fatigue characteristic are poor becomes obvious.
Figure BDA0000383256180000201
Table 5
Figure BDA0000383256180000211
Outside underscore numeral scope of the present invention
(embodiment 3)
Refined and cast the steel plate 3a～3d with the chemical composition shown in table 6.These steel discs are obtained to the hot-rolled steel sheet of thickness 2.5mm with the condition identical with embodiment 1.By cold rolling one-tenth 1.2mm after these hot-rolled steel sheet pickling.
These steel plates are heated to 655 ℃ with the average rate of heating of 19 ℃/secs, then are heated to after 800 ℃ cooling with the average cooling rate of 6.5 ℃/secs immediately with the average rate of heating of 2.5 ℃.Then the melting Al that is immersed in 670 ℃ bathed in (contain 10% Si and inevitably impurity), within 5 seconds, took out afterwards, adjust adhesion amount by air knife (gas wiper) after air cooling to room temperature.
Produced the measurement of hardness test specimen with the main points identical with embodiment 1 from the steel plate obtained.In order to measure hardness, with the main points identical with embodiment 1, measured apart from plating layer (responding layer of Al and Fe) inboard in the Al layer and the hardness of the position of the boundary 20 μ m of steel plate.When this is measured, also carried out the thickness measurement of plating Al layer (totals of 2 layers).The measurement range of thickness is that the length identical with the measurement of hardness scope is selected 30mm, and measuring interval is that 5mm measures 7 points, and the first mensuration face and second is measured 14 of the total the located mensuration of face and obtained its mean value.
These steel plates are hot pressed into to shape for hat with the main points identical with embodiment 2.Heating condition is made as at 900 ℃ and keeps 1 minute.
The fatigue sample shown in Fig. 2 and JIS5 tensile test specimen have been produced from crown section.
Obtained tensile strength sigma with these test specimens b(mean values of 2) and 1 * 10 7inferior time intensity σ w.By their table 7 that the results are shown in.
Although all obtained safe range of stress than being the steel sheet for hot pressed member of the excellence more than 0.4 in which embodiment, in the thickness of plating Al layer surpasses the No.57,62,67 and 72 of 50 μ m, adherent phenomenon occurs with high frequency in the longitudinal wall part of shape for hat.In example below 50 μ m, adherent phenomenon does not occur fully.Therefore, judge surface of steel plate implement plating Al situation thickness on be limited to below 50 μ m.
Figure BDA0000383256180000231
Table 7
Figure BDA0000383256180000241
Outside underscore numeral scope of the present invention
(embodiment 4)
Refined and cast the steel plate 3a～3d with the chemical composition shown in table 6.These steel discs are obtained to the hot-rolled steel sheet of thickness 2.5mm with the condition identical with embodiment 1.By cold rolling one-tenth 1.2mm after these hot-rolled steel sheet pickling.
These steel plates are heated to 655 ℃ with the average rate of heating of 19 ℃/secs, then are heated to after 800 ℃ cooling with the average cooling rate of 6.5 ℃/secs immediately with the average rate of heating of 2.5 ℃.Then the melting Zn that is immersed in 460 ℃ bathed in (contain 0.15% Al and inevitably impurity), within 3 seconds, took out afterwards, adjust adhesion amount by air knife after air cooling to room temperature.
Produced the measurement of hardness test specimen with the main points identical with embodiment 1 from the steel plate obtained.In order to measure hardness, with the main points identical with embodiment 1, measured apart from the layer (responding layer of Al and Fe) of the inboard of plating the Zn layer and the hardness of the position of the boundary 20 μ m of steel plate.When this is measured, also carried out only having the thickness measurement of plating Zn layer.The measurement range of thickness is that the length identical with the measurement of hardness scope is selected 30mm, and measuring interval is that 5mm measures 7 points, and the first mensuration face and second is measured 14 of the total the located mensuration of face and obtained its mean value.
These steel plates are hot pressed into to shape for hat with the main points identical with embodiment 2.Be heated to 880 ℃ and keep after 5 seconds, air cooling to 700 ℃ is suppressed.
The fatigue sample shown in Fig. 2 and JIS5 tensile test piece have been produced from crown section.
Obtained tensile strength sigma with these test specimens b(mean values of 2) and 1 * 10 7inferior time intensity σ w.By their table 8 that the results are shown in.
Although all obtained safe range of stress than being the steel sheet for hot pressed member of the excellence more than 0.4 in which embodiment, in the thickness of plating Zn layer surpasses the No.77,82,87 and 92 of 30 μ m Zn stick on mould by high frequency confirm.In example below 30 μ m, the adhesion of Zn does not occur fully.Therefore, judge surface of steel plate implement plating Zn situation thickness on be limited to below 30 μ m.
Table 8
Figure BDA0000383256180000251
Outside underscore numeral scope of the present invention
(embodiment 5)
Refined and cast the steel plate 3a～3d with the chemical composition shown in table 6.These steel discs are obtained to the hot-rolled steel sheet of thickness 2.5mm with the condition identical with embodiment 1.By cold rolling one-tenth 1.2mm after these hot-rolled steel sheet pickling.
These steel plates are heated to 655 ℃ with the average rate of heating of 19 ℃/secs, then are heated to after 800 ℃ cooling with the average cooling rate of 6.5 ℃/secs immediately with the average rate of heating of 2.5 ℃.Then the melting Zn that is immersed in 460 ℃ bathed in (contain 0.13% Al, 0.03% Fe and inevitably impurity), within 3 seconds, take out afterwards, after adjusting adhesion amount by air knife, be heated to 480 ℃ of formation zn-fe alloy layers after air cooling to room temperature.
Produced the measurement of hardness test specimen with the main points identical with embodiment 1 from the steel plate obtained.In order to measure hardness, measured the hardness of innermost layer (responding layer of Zn and Fe) apart from the zn-fe alloy layer and the position of the boundary 20 μ m of steel plate with the main points identical with embodiment 1.When this is measured, also carried out the aggregate thickness of zn-fe alloy layer (forming by 4 layers) and measured.When this is measured, also carried out the thickness measurement of plating Al layer (totals of 2 layers).The measurement range of thickness is that the length identical with the measurement of hardness scope is selected 30mm, and measuring interval is that 5mm measures 7 points, and the first mensuration face and second is measured 14 of the total the located mensuration of face and obtained its mean value.
These steel plates are hot pressed into to shape for hat with the main points identical with embodiment 2.Be heated to 880 ℃ and keep after 5 seconds, air cooling to 700 ℃ is suppressed.
The fatigue sample shown in Fig. 2 and JIS5 tensile test specimen have been produced from crown section.
Obtained tensile strength sigma with these test specimens b(mean values of 2) and 1 * 10 7inferior time intensity σ w.By their table 9 that the results are shown in.
Although all obtained safe range of stress than being the steel sheet for hot pressed member of the excellence more than 0.4 in which embodiment, the alloy layer in the thickness of zn-fe alloy layer surpasses the No.97,102,107 and 112 of 45 μ m after compacting has produced trickle cracking.In example below 45 μ m, trickle cracking does not occur fully.Therefore, judge surface of steel plate form the zn-fe alloy layer situation thickness on be limited to below 45 μ m.
Table 9
Figure BDA0000383256180000271
Outside underscore numeral scope of the present invention
Description of reference numerals
11a: mold
11b: bed die
12: steel plate
21: fatigue cracking progress zone
51: test specimen is produced position

Claims (9)

1. a steel sheet for hot pressed member, is characterized in that, is the steel plate that contains following chemical composition, in quality %, contains
C：0.15～0.35%、
Si：0.01～1.0%、
Mn:0.3～2.3% and
Al:0.01～0.5%, and,
Its surplus is Fe and inevitable impurity,
As this impurity, be defined as:
Below P:0.03%,
S:0.02% following and
Below N:0.1%,
Standard deviation apart from the Vickers' hardness of the position of this surface of steel plate 20 μ m on the thickness of slab direction is below 20.
2. steel sheet for hot pressed member according to claim 1, is characterized in that, in quality %, also contains and be selected from one or more in following chemical composition:
Cr：0.01～2.0%、
Ti：0.001～0.5%、
Nb：0.001～0.5%、
B：0.0005～0.01%、
Mo：0.01～1.0%、
W：0.01～0.5%、
V：0.01～0.5%、
Cu:0.01～1.0% and
Ni：0.01～5.0%。
3. steel sheet for hot pressed member according to claim 1, it is characterized in that thering is any of zn-fe alloy layer of the thickness of the plating Zn layer of thickness of plating Al layer, 5 μ m～30 μ m of the thickness of 5 μ m～50 μ m or 5 μ m～45 μ m on the surface of described steel plate.
4. the manufacture method of a steel sheet for hot pressed member, is characterized in that, will, to the steel hot rolling that contains following chemical composition, in the operation of the cold rolling cold-rolled steel sheet recrystallization annealing obtained, comprise thereafter:
Average rate of heating with 8～25 ℃/secs is heated to temperature M(℃ from room temperature) first stage; With
Then with the average rate of heating of 1～7 ℃/sec, be heated to temperature S(℃) subordinate phase,
Temperature M(℃) be 600 ℃～700 ℃,
Temperature S(℃) be 720 ℃～820 ℃,
Described chemical composition, in quality %, contains
C：0.15～0.35%、
Si：0.01～1.0%、
Mn:0.3～2.3% and
Al:0.01～0.5%, and,
Its surplus is Fe and inevitable impurity,
As this impurity, be defined as:
Below P:0.03%,
S:0.02% following and
Below N:0.1%.
5. the manufacture method of steel sheet for hot pressed member according to claim 4, is characterized in that, described steel is in quality %, also contains and be selected from one or more in following chemical composition:
Cr：0.01～2.0%、
Ti：0.001～0.5%、
Nb：0.001～0.5%、
B：0.0005～0.01%、
Mo：0.01～1.0%、
W：0.01～0.5%、
V：0.01～0.5%、
Cu:0.01～1.0% and
Ni：0.01～5.0%。
6. the manufacture method of steel sheet for hot pressed member according to claim 5, is characterized in that, the hot rolling rate of described hot-rolled process is 60～90%, and the cold rolling rate of described cold rolling process is 30～90%.
7. the manufacture method of steel sheet for hot pressed member according to claim 4, is characterized in that, also comprises: continue with described recrystallization annealing operation, described steel plate is immersed in the Al bath, form the operation of plating Al layer on surface.
8. the manufacture method of steel sheet for hot pressed member according to claim 4, is characterized in that, also comprises: continue with described recrystallization annealing operation, described steel plate is immersed in the Zn bath, form the operation of plating Zn layer on surface.
9. the manufacture method of steel sheet for hot pressed member according to claim 4, it is characterized in that, also comprise: with described recrystallization annealing operation, continue, described steel plate is immersed in the Zn bath, after surface forms plating Zn layer, further be heated to below 600 ℃, form the operation of zn-fe alloy layer on described surface.
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