WO2015029404A1 - 高強度溶融亜鉛めっき鋼板及びその製造方法 - Google Patents
高強度溶融亜鉛めっき鋼板及びその製造方法 Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
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- 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
- C23C2/50—Controlling or regulating the coating processes
- C23C2/52—Controlling or regulating the coating processes with means for measuring or sensing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/18—Layered products comprising a layer of metal comprising iron or steel
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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
- C21D1/26—Methods of annealing
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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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- 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
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
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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
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C18/00—Alloys based on zinc
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C18/00—Alloys based on zinc
- C22C18/04—Alloys based on zinc with aluminium as the next major constituent
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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
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
- C23C2/0222—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating in a reactive atmosphere, e.g. oxidising or reducing atmosphere
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- 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
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- 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
- C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
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- 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
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- 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
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
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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
- C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
- C21D3/02—Extraction of non-metals
- C21D3/06—Extraction of hydrogen
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- 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.]
- Y10T428/12771—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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- 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
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- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
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- Y10T428/12951—Fe-base component
- Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
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- 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
- Y10T428/12993—Surface feature [e.g., rough, mirror]
Definitions
- the present invention relates to a high-strength hot-dip galvanized steel sheet suitable as a rust-proof surface-treated steel sheet for automobiles and the like, and a method for producing the high-strength hot-dip galvanized steel sheet.
- the hot dip galvanized steel sheet whose surface is hot dip galvanized is widely used in the fields of automobiles, home appliances, building materials, etc. as a steel sheet that is inexpensive and excellent in rust prevention.
- annealing treatment is performed in a reducing atmosphere with H 2 -N 2 gas, and after reducing and activating the steel sheet surface, A hot dip galvanized steel sheet is manufactured by cooling the steel sheet to a temperature suitable for plating and immersing it in a hot dip galvanizing bath while preventing the steel sheet from being exposed to the atmosphere.
- Addition of solid solution strengthening elements such as Si and Mn is performed to increase the strength of the steel sheet.
- Si and Mn which are easily oxidizable elements, are present on the steel sheet surface in a reducing atmosphere during annealing. Thicken to form oxide. This oxide deteriorates the wettability between the hot dip galvanizing process and the steel sheet surface in the subsequent hot dip galvanizing process, and causes non-plating defects.
- Patent Document 1 discloses a technique for reducing the oxygen potential by setting the dew point in the furnace atmosphere during annealing to ⁇ 45 ° C. or less and plating without oxidizing Si and Mn.
- Patent Document 2 discloses a technique for increasing the reducing ability of a steel sheet with hydrogen gas by suppressing the hydrogen concentration in the furnace atmosphere during annealing to 25% or more, thereby suppressing non-plating of the steel sheet. Yes.
- Patent Document 3 Ti compounds such as TiC and TiN are precipitated by adding a small amount of Ti to the steel sheet and occluded from the atmosphere gas by voids around these precipitates.
- a technique is disclosed in which the generated hydrogen gas is trapped in steel as it is to suppress the release of hydrogen gas after the hot dip galvanizing treatment.
- Patent Document 1 Although it is possible to suppress non-plating without restriction on the Si and Mn contents in the steel, it is technically difficult to maintain the inside of the annealing furnace with a low dew point. New capital investment is required. Moreover, in the technique of patent document 2, excessive hydrogen is occluded in a steel plate by increasing the hydrogen concentration at the time of annealing, and generation
- the present invention has been made in view of such circumstances, and uses a steel sheet containing Si and Mn as a base steel sheet, and is a high-strength hot-dip galvanizing excellent in surface appearance without non-plating and blister defects (occurrence of blistering). It aims at providing a steel plate and its manufacturing method.
- the inventors of the present invention have obtained the following knowledge as a result of intensive studies to solve the above-described problems in high-strength hot-dip galvanized steel sheets.
- the Si and Mn concentration ratio between the surface layer of the underlying steel sheet and the interior of the underlying steel sheet is controlled appropriately, which causes deterioration of wettability. It is necessary to suppress the formation of Si oxide and Mn oxide in the surface steel plate surface layer.
- the hydrogen partial pressure (P H2 ) in the furnace atmosphere is set to 0.10 to 0.50
- the water vapor partial pressure (P H2O ) and the hydrogen partial pressure (P The ratio of H2 ) and log (P H2 / P H2O ) may be 2.5 or more and 4.0 or less.
- the hydrogen partial pressure (P H2 ) in the atmosphere is set to 0.10 or more and 0.30 or less, and the steel plate temperature is 400 ° C. or more and 600 ° C. or less. It is necessary to hold for 30 seconds or more.
- the present invention is based on the above findings, and features are as follows.
- High-strength hot-dip galvanized steel sheet characterized in that it. (Method 1) After removing the galvanized layer from the high-strength hot-dip galvanized steel sheet, the amount of hydrogen released from the base steel sheet when the base steel sheet is heated from room temperature to 250 ° C. is measured.
- the hydrogen partial pressure (P H2 ) of the base steel sheet having the steel composition described in (1) is 0.10 or more and 0.50 or less when the total pressure in the furnace atmosphere is 1.
- Log (P H2 / P H2O ) which is the ratio of the partial pressure of water vapor (P H2O ) to the partial pressure of hydrogen (P H2 ) when the total pressure in the atmosphere is 1, is 2.5 or more and 4.0 or less.
- the base steel plate After the annealing step for annealing and after the annealing step, the base steel plate is cooled, and after cooling, the hydrogen partial pressure (P H2 ) when the total pressure in the atmosphere is 1 is 0.10 or more and 0.30 or less, the steel plate temperature A cooling and holding step for holding the base steel plate under the conditions of 400 ° C. to 600 ° C. and a holding time of 20 seconds or more, and a hot dip galvanizing bath having an Al concentration of 0.15% or more after the cooling and holding step.
- the high-strength hot-dip galvanized steel sheet is a steel sheet having a tensile strength TS of 400 MPa or more.
- the high-strength hot-dip galvanized steel sheet of the present invention includes a plated steel sheet (hereinafter sometimes referred to as GI) that is not subjected to alloying after the hot-dip galvanizing process, and a plated steel sheet (hereinafter referred to as GA) that is subjected to the alloying process. In some cases).
- a high-strength hot-dip galvanized steel sheet excellent in surface appearance free from unplating and blister defects is obtained using a steel sheet containing Si and Mn as a base steel sheet.
- the present invention will be specifically described, but the present invention is not limited to the following embodiments.
- the unit of the content of each element of the steel component composition is “mass%”, and hereinafter, simply indicated by “%” unless otherwise specified.
- the high-strength hot-dip galvanized steel sheet of the present invention has a base steel sheet and a galvanized layer formed on the surface of the base steel sheet.
- the base steel plate is in mass%, C: 0.01% to 0.30%, Si: 0.01% to 1.5%, Mn: 0.1% to 3.0%, P: 0 0.003% or more and 0.1% or less, S: 0.01% or less, Al: 0.001% or more and 0.20% or less, with the balance being Fe and inevitable impurities.
- C 0.01% or more and 0.30% or less C is an element necessary for increasing the strength of the base steel sheet.
- the C content is 0.01% or more. It is necessary to make it.
- the upper limit is made 0.30%.
- a preferable range of the C content is 0.06% or more and 0.12%.
- Si 0.01% or more and 1.5% or less Si is effective as a solid solution strengthening element, and in order for the strengthening effect to appear, it is necessary to contain 0.01% or more of Si. On the other hand, if Si is contained in a large amount exceeding 1.5%, the amount of Si oxide formed on the surface of the underlying steel sheet during annealing is significantly increased and causes non-plating, so the upper limit is 1.5%. .
- Mn 0.1% or more and 3.0% or less Mn is added to increase the strength, and in order for the strengthening effect to appear, it is necessary to contain 0.1% or more of Mn.
- Mn 0.1% or more and 3.0% or less
- Mn is added to increase the strength, and in order for the strengthening effect to appear, it is necessary to contain 0.1% or more of Mn.
- Mn is contained exceeding 3.0%, the amount of Mn oxide formed on the surface of the underlying steel sheet during annealing is remarkably increased, causing non-plating. For this reason, the upper limit of the Mn content is 3.0%.
- a preferable range of the Mn content is 1.1% or more and 2.9% or less.
- P 0.003% or more and 0.1% or less
- P is one of the elements inevitably contained, and in order to make it less than 0.003%, there is a concern about an increase in cost. For this reason, content of P shall be 0.003% or more.
- P is contained in excess of 0.1%, weldability deteriorates, so the P content is 0.1% or less.
- a preferable P content is 0.015% or less.
- S 0.01% or less
- the lower limit of the S content is not particularly limited, and may be about the impurity level.
- Al 0.001% or more and 0.20% or less Al is added for the purpose of deoxidation of molten steel, but if the content is less than 0.001%, the purpose is not achieved. On the other hand, if the content exceeds 0.20%, a large amount of inclusions are generated, which causes wrinkling of the base steel sheet. Accordingly, the Al content is set to be 0.001% or more and 0.20% or less.
- the base steel plate is composed of the above essential components, Fe and inevitable impurities. Inevitable impurities include O and N.
- the galvanized layer is formed on the surface of the base steel plate, and the plating adhesion amount per side may be a normal adhesion amount excellent in corrosion resistance, adhesion, etc., and is 20 g / m 2 or more and 120 g / m 2 or less.
- the amount of hydrogen released from the base steel sheet The high-strength hot-dip galvanized steel sheet of the present invention has a total amount of hydrogen released from the base steel sheet of 0 when the base steel sheet after removing the galvanized layer is heated from room temperature to 250 ° C. It is 0.05 mass ppm or more and 0.40 mass ppm or less.
- the hydrogen gas occluded in the base steel sheet is mainly taken from the atmospheric hydrogen gas during annealing. In order to express the effect of suppressing the surface selective oxidation of Si and Mn by hydrogen gas, the lower limit of the amount of hydrogen occluded in the steel is 0.05 mass ppm.
- the upper limit is set to 0.40 mass ppm.
- the preferable total amount of hydrogen is 0.10 mass ppm or more and 0.38 mass ppm or less. The method for measuring the amount of hydrogen is as described in the examples.
- the high-strength hot-dip galvanized steel plate of the present invention is measured by glow discharge optical emission spectrometry (GDS) in the depth direction from the surface side after removing the galvanized layer.
- GDS glow discharge optical emission spectrometry
- the ratio of the average strength of Mn (I Mn bulk ), I Si sur / I Si bulk and I Mn sur / I Mn bulk are I Si sur / I Si bulk ⁇ 2.0 and I Mn sur / I Mn bulk ⁇ , respectively. It needs to be 3.0.
- the intensity ratio corresponds to the concentration ratio.
- a preferable range of I Si sur / I Si bulk is 1.0 or more and 1.5 or less, and a more preferable range of I Mn sur / I Mn bulk is 1.1 or more and 2.6 or less.
- the manufacturing method of the present invention includes an annealing process for annealing the base steel sheet, a cooling and holding process for cooling the base steel sheet after the annealing process, and holding the base steel sheet after the cooling, and a molten zinc in the base steel sheet after the cooling and holding process. It has a hot dip galvanizing process for plating.
- An annealing process is a water vapor when the partial pressure of hydrogen (P H2 ) is 0.10 or more and 0.50 or less when the total pressure in the furnace atmosphere is 1, and the total pressure in the furnace atmosphere is 1.
- the base steel sheet is annealed under the condition that log (P H2 / P H2O ), which is the ratio of the partial pressure (P H2O ) to the hydrogen partial pressure (P H2 ), is 2.5 or more and 4.0 or less.
- An increase in the hydrogen partial pressure and a decrease in the water vapor partial pressure in the annealing atmosphere both reduce the oxygen potential in the atmosphere and are effective in suppressing the surface selective oxidation of Si and Mn. If the hydrogen partial pressure is less than 0.10, the reducing ability of the underlying steel sheet with hydrogen gas is insufficient, so the lower limit of the hydrogen partial pressure is 0.10. On the other hand, if the hydrogen partial pressure exceeds 0.50, excess hydrogen gas accumulates in the steel and causes blistering, so the upper limit of the hydrogen partial pressure is set to 0.50.
- log (P H2 / P H2O ) when log (P H2 / P H2O ) is less than 2.5, the oxygen potential in the atmosphere is not sufficiently reduced, and the surface selective oxidation suppressing effect of Si and Mn is small, so log (P H2 / P H2O). ) Is set to 2.5. On the other hand, if the log (P H2 / P H2O ) exceeds 4.0, it is necessary to introduce excess hydrogen gas into the atmosphere or to lower the dew point, and blister generation and stable operability are problems. 4.0.
- the cooling and holding step refers to cooling the underlying steel plate after the annealing step, the hydrogen partial pressure (P H2 ) when the total pressure in the atmosphere is 1 after the cooling is 0.10 to 0.30, the steel plate temperature In this step, the base steel sheet is held under conditions of 400 ° C. or higher and 600 ° C. or lower and a holding time of 20 seconds or longer.
- the hydrogen partial pressure (P H2 ) when the total pressure in the atmosphere is 1 is 0.10 or more and 0.30 or less, the steel plate temperature
- the base steel sheet is held in a temperature range of 400 ° C. or higher and 600 ° C. or lower for 20 seconds or longer.
- the amount of hydrogen released from the base steel plate into the atmosphere exceeds the amount of hydrogen occluded from the atmosphere into the base steel plate.
- the hydrogen gas accumulated in the steel is released and blister defects are suppressed.
- the upper limit of the holding time is not particularly limited.
- a preferable holding time is not less than 32 seconds and not more than 50 seconds.
- the steel plate temperature is lower than 400 ° C.
- the base steel plate is immersed in a hot dip galvanizing bath at a plate temperature lower than the freezing point of zinc, and it becomes difficult to control the adhesion amount after plating.
- the lower limit is 400 ° C.
- the hydrogen partial pressure when the total pressure in the atmosphere at this time is 1, the lower limit is set to 0.10 from the viewpoint of suppressing surface selective oxidation of Si and Mn, and the amount of hydrogen occluded from the atmosphere to the base steel plate Therefore, the upper limit is set to 0.30.
- a preferable hydrogen partial pressure is 0.13 or more and 0.30 or less.
- the hot dip galvanizing step is a step of performing hot dip galvanizing treatment on the base steel sheet after the cooling and holding step.
- a normal hot dip galvanizing bath may be used.
- a hot dip galvanizing bath containing a small amount of Al is used.
- a small amount of Al has the effect of suppressing the formation of the Fe—Zn alloy layer at the interface between the hot dip galvanized layer and the base steel plate (underlying steel plate) and improving the adhesion of the hot dip galvanized layer.
- a hot dip galvanizing bath having an Al concentration of 0.15% or more is preferably used.
- the amount of the galvanized layer plated can be adjusted to a desired range by gas wiping or the like in this step.
- the average strength from the sputtering time of 450 seconds to 500 seconds was taken as the strength inside the base steel plate, and the ratio of the maximum strength to the average strength inside the base steel plate was determined from the Si and Mn strength profiles. This was performed with three sets of test pieces for each specimen, and the average value was obtained.
- the examples of the present invention all have a good plating appearance.
- the comparative example that does not satisfy the scope of the present invention has a low evaluation of either “evaluation of non-plating” or “evaluation of blister”.
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Abstract
Description
(方法1)
高強度溶融亜鉛めっき鋼板から亜鉛めっき層を除去後、下地鋼板を室温から250℃まで加熱した際に下地鋼板から放出される水素量を測定する。
(方法2)
高強度溶融亜鉛めっき鋼板から亜鉛めっき層を除去後、グロー放電発光分析法(GDS)により測定した、下地鋼板表層部のSiの最大強度(ISi sur)及びMnの最大強度(IMn sur)と、下地鋼板内部のSiの平均強度(ISi bulk)及びMnの平均強度(IMn bulk)に基づいて、ISi sur/ISi bulk及びIMn sur/IMn bulkを算出する。
Cは下地鋼板の高強度化に必要な元素であり、下地鋼板の高強度化を実現するためには、Cの含有量を0.01%以上にすることが必要である。一方、Cの含有量が0.30%を超えると溶接性が劣化するため、上限は0.30%とする。Cの含有量の好ましい範囲は0.06%以上0.12%である。
Siは固溶強化元素として有効であり、強化効果が現れるためにはSiを0.01%以上含有する必要がある。一方、Siを1.5%を超えて多量に含有させると焼鈍時に下地鋼板表面に形成されるSi酸化物量が顕著に増加し不めっき発生の原因となるため、上限は1.5%とする。
Mnは強度上昇のために添加し、強化効果が現れるためには0.1%以上のMnを含有する必要がある。一方、3.0%を超えてMnを含有させると、焼鈍時に下地鋼板表面に形成されるMn酸化物量が顕著に増加し不めっき発生の原因となる。このため、Mn含有量の上限は3.0%とする。Mn含有量の好ましい範囲は、1.1%以上2.9%以下である。
Pは不可避的に含有される元素のひとつであり、0.003%未満とするためには、コストの増大が懸念される。このため、Pの含有量は0.003%以上とする。一方、Pを0.1%を超えて含有させると溶接性が劣化するため、Pの含有量は0.1%以下とする。好ましいPの含有量は0.015%以下である。
Sは粒界に偏析するか、又はMnSを多量に生成した場合、靭性を低下させる。以上より、Sの含有量は0.01%以下とする必要がある。Sの含有量の下限は特に限定するものではなく、不純物程度であってもよい。
Alは溶鋼の脱酸を目的に添加されるが、その含有量が0.001%未満の場合、その目的が達成されない。一方、0.20%を超えて含有させると、介在物が多量に発生し、下地鋼板の疵の原因となる。以上より、Alの含有量は0.001%以上0.20%以下とする。
本発明の高強度溶融亜鉛めっき鋼板は、亜鉛めっき層を除去後の下地鋼板を室温から250℃まで加熱した際に下地鋼板から放出される水素量の合計が0.05質量ppm以上0.40質量ppm以下である。下地鋼板に吸蔵される水素ガスは主に焼鈍時の雰囲気水素ガスから取り込まれる。水素ガスによるSi及びMnの表面選択酸化抑制効果を発現させるため、鋼中に吸蔵される水素量の下限は0.05質量ppmとする。一方、上記水素量合計が0.40質量ppmを超えた場合、鋼中に過剰の水素ガスが蓄積し、ブリスター発生の原因となるため、上限は0.40質量ppmとする。好ましい上記水素量合計は、0.10質量ppm以上0.38質量ppm以下である。なお、水素量の測定方法は実施例に記載の通りである。
本発明の高強度溶融亜鉛めっき鋼板は、亜鉛めっき層を除去後、表面側から深さ方向にグロー放電発光分析法(GDS)により測定を行ったところ、表層部近傍でSi,Mnが高く、深さ方向に深くなるに従いSi,Mnが低下していき、一定値になることを確認した。この表層部近傍のSiの最大強度(ISi sur)及びMnの最大強度(IMn sur)と、下地鋼板内部でSi,Mn量が一定となった部分のSiの平均強度(ISi bulk)及びMnの平均強度(IMn bulk)の比、ISi sur/ISi bulk及びIMn sur/IMn bulkがそれぞれISi sur/ISi bulk≦2.0、IMn sur/IMn bulk≦3.0である必要がある。各々の強度比を上記に制御することで、焼鈍過程において下地鋼板表層部に形成されたSi酸化物量及びMn酸化物量が適正となり、亜鉛めっき層と下地鋼板との濡れ性が良好となり、不めっき欠陥が抑制される。ここで、強度比は濃度比と対応する。好ましいISi sur/ISi bulkの範囲は1.0以上1.5以下であり、より好ましいIMn sur/IMn bulkの範囲は1.1以上2.6以下である。
溶融亜鉛めっき鋼板の表面外観を目視評価し、不めっきの有無を評価した。不めっきが全くない場合は最良(◎)、軽微な不めっきが存在するが表面品質を損ねる程度ではない場合は良好(○)、不めっきがあり表面品質が劣る場合は不良(×)とし、「◎」、及び「○」を合格とした。
300mm×300mmに切り出した溶融亜鉛めっき鋼板を熱風式焼付け炉にて加熱処理を行った。熱処理条件は、鋼板温度が250℃に到達後、30分間保持後に空冷を行い、室温まで冷却後、目視によりブリスターの有無を評価した。ブリスターが全くない場合は良好(○)、ブリスターが発生した場合は不良(×)とし、「○」を合格とした。
5mm×100mmに切り出した溶融亜鉛めっき鋼板を液体窒素に浸漬し約-196℃で冷却し、鋼中水素量測定用試験片とした。この試験片を-100℃以下に保ちながら、表裏面の亜鉛めっき層を研削除去し、アルコール洗浄を行った後にガスクロマトグラフにセットし、水素量測定を行った。測定条件は、加熱速度200℃/hrで250℃まで昇温した後、250℃で30分間保持を行い、昇温から保持過程において放出された全水素量を測定した。これを各供試材につき3組の試験片で行い、その平均値を求めた。
30mm×30mmに切り出した溶融亜鉛めっき鋼板を、20質量%NaOH-10質量%トリエタノールアミン水溶液195ccと、35質量%過酸化水素溶液7ccの混合液に浸漬してめっき層を溶解し、試験片とした。試験片をGDSにセットし、Arガス流量250cc、電流20mAの条件で500秒間スパッタを行った。スパッタ時間450秒から500秒までの平均強度を下地鋼板内部の強度とし、Si、Mnの強度プロファイルから、その最大強度と下地鋼板内部の平均強度の比を求めた。これを各供試材につき3組の試験片で行い、その平均値を求めた。
Claims (2)
- 質量%で、C:0.01%以上0.30%以下、Si:0.01%以上1.5%以下、Mn:0.1%以上3.0%以下、P:0.003%以上0.1%以下、S:0.01%以下、Al:0.001%以上0.20%以下を含有し、残部がFeおよび不可避的不純物からなる成分組成の下地鋼板と、
前記下地鋼板の表面に形成された、片面あたりのめっき付着量が20g/m2以上120g/m2以下の亜鉛めっき層と、を有し、
下記方法1で測定される水素量の合計が、0.05質量ppm以上0.40質量ppm以下であり、
下記方法2で算出されるISi sur/ISi bulk及びIMn sur/IMn bulkが、それぞれISi sur/ISi bulk≦2.0、IMn sur/IMn bulk≦3.0であることを特徴とする高強度溶融亜鉛めっき鋼板。
(方法1)
高強度溶融亜鉛めっき鋼板から亜鉛めっき層を除去後、下地鋼板を室温から250℃まで加熱した際に下地鋼板から放出される水素量を測定する。
(方法2)
高強度溶融亜鉛めっき鋼板から亜鉛めっき層を除去後、グロー放電発光分析法(GDS)により測定した、下地鋼板表層部のSiの最大強度(ISi sur)及びMnの最大強度(IMn sur)と、下地鋼板内部のSiの平均強度(ISi bulk)及びMnの平均強度(IMn bulk)に基づいて、ISi sur/ISi bulk及びIMn sur/IMn bulkを算出する。 - 請求項1に記載の鋼組成を有する下地鋼板を、炉内雰囲気中の全圧力を1としたときの水素分圧(PH2)が0.10以上0.50以下、かつ炉内雰囲気中の全圧力を1としたときの水蒸気分圧(PH2O)と水素分圧(PH2)の比であるlog(PH2/PH2O)が2.5以上4.0以下の条件で焼鈍する焼鈍工程と、
前記焼鈍工程後、下地鋼板を冷却し、該冷却後に雰囲気中の全圧力を1としたときの水素分圧(PH2)が0.10以上0.30以下、鋼板温度400℃以上600℃以下、保持時間が30秒以上の条件で下地鋼板を保持する冷却保持工程と、
前記冷却保持工程後に、Al濃度が0.15%以上の溶融亜鉛めっき浴で、下地鋼板に溶融亜鉛めっき処理を施す溶融亜鉛めっき工程と、を有することを特徴とする高強度溶融亜鉛めっき鋼板の製造方法。
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KR20160048882A (ko) | 2016-05-04 |
KR101824823B1 (ko) | 2018-02-01 |
EP3040440B1 (en) | 2019-03-06 |
EP3040440A4 (en) | 2016-08-17 |
JPWO2015029404A1 (ja) | 2017-03-02 |
US20160214351A1 (en) | 2016-07-28 |
EP3040440A1 (en) | 2016-07-06 |
JP6128223B2 (ja) | 2017-05-17 |
CN105531388A (zh) | 2016-04-27 |
MX2016002449A (es) | 2016-06-24 |
US9895863B2 (en) | 2018-02-20 |
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