WO2006038736A1 - Feuille d’acier zinguée à chaud et procédé de production idoine - Google Patents

Feuille d’acier zinguée à chaud et procédé de production idoine Download PDF

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Publication number
WO2006038736A1
WO2006038736A1 PCT/JP2005/018904 JP2005018904W WO2006038736A1 WO 2006038736 A1 WO2006038736 A1 WO 2006038736A1 JP 2005018904 W JP2005018904 W JP 2005018904W WO 2006038736 A1 WO2006038736 A1 WO 2006038736A1
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WIPO (PCT)
Prior art keywords
steel sheet
hot dip
plating
hot
dip galvanized
Prior art date
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PCT/JP2005/018904
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English (en)
Japanese (ja)
Inventor
Yoshitsugu Suzuki
Masahiko Tada
Yusuke Fushiwaki
Yoichi Tobiyama
Takashi Kawano
Hisato Noro
Hisanori Ando
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Jfe Steel Corporation
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Application filed by Jfe Steel Corporation filed Critical Jfe Steel Corporation
Priority to US11/664,490 priority Critical patent/US20080070060A1/en
Priority to CA002582762A priority patent/CA2582762A1/fr
Priority to EP05793822A priority patent/EP1806422A4/fr
Publication of WO2006038736A1 publication Critical patent/WO2006038736A1/fr

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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
    • 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
    • C23C2/02—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
    • 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
    • C23C2/026—Deposition of sublayers, e.g. adhesion layers or pre-applied alloying elements or corrosion protection
    • 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
    • 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]

Definitions

  • the present invention relates to a hot-dip galvanized steel sheet that can be suitably used in the fields of automobiles, building materials and household appliances, and a method for producing the same.
  • the present invention relates to a hot-dip galvanized steel sheet that has excellent adhesion and sliding properties even when steel with a high Si content is used.
  • the present invention relates to an alloyed hot dip zinc alloy obtained by alloying the molten bright lead galvanized steel sheet.
  • hot dip galvanized steel sheet is manufactured by the following process. After the slab is hot-rolled, it is further subjected to cold rolling and heat treatment to obtain a thin steel plate. The surface of the thin steel sheet is degreased and / or pickled and cleaned in the pretreatment process, or the pretreatment process is omitted and the oil content on the surface of the thin steel sheet is burned and removed in the preheating furnace. Recrystallization annealing is performed in a basic or reducing atmosphere to form a base steel sheet for plating. Then, after cooling the base steel plate to a temperature suitable for fitting in a non-oxidizing atmosphere or reducing atmosphere, a small amount of A1 (usually 0.:!
  • molten dumbbell-plated steel sheets and alloyed hot-dip galvanized steel sheets based on Si-containing high-strength steel sheets have the following problems.
  • the base steel sheet with hot dip zinc is annealed in a reducing atmosphere at a temperature of about 600 to 900 ° C., and then subjected to hot dumbbell plating.
  • Si in steel is an easily oxidizable element, it is selectively oxidized even in a reducing atmosphere that is generally used to form oxides and concentrate on the surface of the underlying steel plate. To do.
  • oxides of Si reduce the wettability with the molten dumbbell during the plating process and cause stagnation. Therefore, as the Si concentration in the steel increases for higher strength, the wettability decreases and non-plating occurs frequently. Moreover, there is a problem that the plating adhesion is deteriorated even when non-plating is not achieved.
  • the alloying temperature must be increased if the desired productivity is maintained at CGL where the length of the alloying furnace is limited. However, if alloying is performed at a high temperature, the above-mentioned deterioration of the powdering resistance is unavoidable.
  • the surface of a high-strength steel plate containing Mn, P and Si contains ammonium salt containing S in terms of S from 0.1 to L000m g / m 2 by the heat treatment after deposition, to diffuse the S component in the base steel of the steel sheet, techniques to produce sulfur compounds such as MnS reacted with Mn in the steel is disclosed.
  • This method suppresses the surface concentration of Mn and suppresses the surface concentration of Si by blocking the diffusion path of Si to the steel sheet surface due to the presence of the sulfur concentrated layer.
  • the present invention has been developed in view of the above-mentioned circumstances, and even when a high Si-containing steel sheet is used as a base, it is excellent enough to withstand even a steel sheet for automobiles that requires particularly strict plating characteristics.
  • An object of the present invention is to provide a hot-dip galvanized steel sheet having both properties and friction properties and a method for producing the same. We also provide alloyed hot-dip galvanized steel sheets that also have excellent powdering resistance. Disclosure of the invention
  • the present invention comprises a steel plate containing Si: 0.1 to 3.0 mass%, hot dip zinc plating, and an oxide containing Si between the steel plate and the hot dip zinc plating, And thickness: 0.01 to: a concentrated layer of at least one component selected from the group consisting of S, C, Cl, Na, K, ⁇ , ⁇ , F, and ⁇ which is! OOjU m Use steel bellows.
  • the hot dip galvanized steel sheet is preferably such that the concentration of the component in the concentrated layer is 10% or more higher than the concentration of the component in the steel sheet.
  • these molten dumbbell-plated steel plates are preferably those in which the amount of the oxide containing Si in the concentrated layer is 0.01 to 1 g / m 2 in terms of oxygen.
  • any one of the above-mentioned molten dumbbell-plated steel sheets preferably further has an Fe layer under the molten zinc galvanized sheet.
  • the concentrated layer is preferably a dispersion of the compound of the component and the component of the steel plate, in particular, the component is S, More preferably, the compound contains 5 or more granular MnS particles having a particle size of 50 nm or more per 20 m in a direction parallel to the interface between the molten dumbbell and the steel plate in an arbitrary cross section.
  • the molten zinc galvanizing is preferably an alloyed molten galvanizing.
  • the present invention provides a steel sheet containing S i: 0.1 to 3 mas S % on the surface of S, C, Cl, a, K, B, P, F, N and a group thereof.
  • a step of adhering at least one selected material a step of heating a steel plate to which the material is adhered, and forming an oxide film having a hematite content of 7 O m SS / o or less on the surface of the steel plate;
  • a method for producing a molten dumbbell-plated steel sheet comprising the steps of: reducing the oxide film; and galvanizing the reduced steel sheet.
  • the heating is preferably performed in an oxidizing atmosphere with respect to Fe at a maximum temperature reached by the steel sheet of more than 500 ° C.
  • the present invention provides S i: 0.
  • a base steel sheet containing ⁇ 3 m ass% prior to performing the molten zinc plated on the surface of the steel plate, hematite content to the surface of the base steel sheet: 7 to form a O m ass% or less of the oxide film,
  • a method for producing a molten dumbbell-plated steel sheet is characterized in that after the reduction treatment is performed, molten zinc plating is performed.
  • Fig. 1 is a diagram showing an example of the Depth Profile obtained by EPMA line analysis of the cross section of an alloyed hot-dip galvanized steel sheet.
  • Fig. 2 shows an example of the depth profile obtained by GDS for the surface layer of a galvannealed steel sheet.
  • the inventors have intensively studied to solve the above problems.
  • a concentrated layer of a specific element is formed under the molten dumbbell layer, and an oxide containing Si in the concentrated layer of parentheses. It was found that the adhesion of the hot dip galvanized layer applied to a steel sheet with a high Si content was dramatically improved by forming the steel.
  • the presence of the Si-containing oxide layer and the concentration layer of the specific element promotes uniform alloying and suppresses the formation of irregularities in the plating layer, resulting in smoothness, resulting in significant friction. I found it to improve.
  • the inventors conducted extensive studies on means for suppressing non-plating of steel sheets with a Si concentration of 0.1 lmass ⁇ in steel and promoting alloying in combination with plating adhesion.
  • a steel plate with a high Si concentration even if the oxidation is promoted simply to form a sufficient amount of iron oxide, the wettability with molten zinc cannot be improved sufficiently, and the non-sticking is completely suppressed. I came to the conclusion that I can't.
  • the composition of the iron oxide was important after a sufficient amount of iron oxide was formed. That is, in the case of a steel sheet having a high Si concentration, it has been found that the above object can be achieved by controlling the composition of iron oxide formed on the surface when the steel sheet is oxidized. It came to lead.
  • a steel sheet containing S i: 0.1-3 ma SS % at least selected from the group consisting of S, C, CI, a, K, B, P, F, N and these compounds
  • a step of adhering one kind of substance a step of heating a steel sheet to which the substance is adhered, and forming an acid film having a hematite content of 7 Oma SS ° / 0 or less on the surface of the steel sheet, the oxide film
  • the present invention has invented a method for producing a molten dumbbell-plated steel sheet having the following process sequence: a step of reducing steel, and a step of hot-dip galvanizing the reduced steel sheet.
  • the Si content in the base steel sheet is limited to the range of 0.1 to 3.0 mass%.
  • the reason for this is that, when steel with a high Si content is used as the base steel plate, the plating adhesion is a problem where the mobility is a problem. This amount of Si is necessary to increase the strength of the steel plate.
  • elements other than Si are not particularly limited, and conventionally known component systems can be used.
  • the representative composition is as follows.
  • C is an element contained in steel and is generally contained in the range of 0.0001 to 0.5 mass%. Also in the present invention, C may be contained in the base steel plate within this range. C is not only useful for increasing strength, but is also an element useful for structural control, such as generating retained austenite to improve the strength ductility balance. In order to express these actions, it is preferable that the content is 0.05 mass ° / o or more. On the other hand, a content of 0.25 mass% or less is preferred because of its excellent weldability.
  • Mn is an element useful for strengthening, is 5 m a s S / D in the range in the base steel sheet in the range of M n may be contained. In particular, 0. lmass ° /. As mentioned above, the effect can be exhibited by containing 0.5 mass% or more preferably.
  • Mn like Si, is an element that forms an oxide film during annealing, and when the content is less than 3.0 ma SS %, a concentrated layer of a specific element below the plating layer will contain Si. When the oxide containing is formed, plating adhesion tends to be improved. It is also convenient for securing weldability and strength ductility balance. For this reason, the Mn content is preferably 3.0 mass% or less. More preferably, it is in the range of 0.5 to 3.0 mass%.
  • A1 5.0 mass o / o or less
  • A1 is an element added complementary to Si, and is preferably contained in an amount of 0.01% or more.
  • the amount of A1 is less than 5.0 ma S s%, the plating adhesion improves when an oxide containing the concentrated element of the specific element and Si is formed under the plating layer. Tend. It is also convenient for securing weldability and strength ductility balance. Therefore, A1 is preferably 5.0 mass% or less. More preferably, it is in the range of 0.01 to 3.0 mass%.
  • steel elements other than those exemplified above include Ti, Nb, V, Cr, S, Mo, Cu, Ni, B, Ca, N, P, and Sb.
  • the content of these elements is Ti: up to lmass%, Nb: up to lmass%, V: up to lmass%, Cr: 3mass ° /.
  • S up to 0.1 lmass%
  • Mo up to lmass%
  • Cu up to 3mass%
  • Ni up to 3mass%
  • B
  • One or more selected from these elements may be contained as long as the total content is in the range of 5 mass% or less.
  • the balance is Fe and inevitable impurities.
  • S, C, CI, Na, K, B, P, F, N are applied to the surface of the steel plate (underlying steel plate) before the annealing process of CGL (continuous mating line). And at least one substance selected from the group consisting of these compounds.
  • Phosphoric acid H 3 P0 4
  • potassium phosphate K 3 P0 4
  • ammonium phosphate ( ⁇ 4 ) 3 ⁇ 0 4
  • sodium phosphate Na 3 P0 4
  • sodium hydrogen phosphate Na 2 HP0 4
  • P-containing compounds such as iron phosphate (FeP0 4 ), phosphonic acid (3 ⁇ 4P0 3 ) and phosphinic acid (3 ⁇ 4P0 2 ),
  • Hydrochloric acid HC1
  • sodium chloride NaCl
  • ammonium chloride H 4 C1
  • antimony chloride SbCl 3
  • potassium chloride KC1
  • iron chloride FeCl 2 , FeCl 3
  • titanium chloride TiCl 4
  • C1-containing compounds such as copper chloride (CuCl), barium chloride (BaCl 2 ), molybdenum chloride (MoCl 5 ) and sodium chlorate (NaC10 3 ),
  • N-containing compounds such as oxalic acid and oxalate, citrate and citrate, nitric acid and nitrate can be used.
  • the method for adhering the above substances to the steel sheet is not particularly limited, and may be physically adhered.
  • a solution or suspension in which the above substances are mixed with water or an organic solvent is used, and a steel plate is immersed in such a solution or suspension, or such a solution or suspension is sprayed.
  • a method of fogging, a method of applying with a roll coater or the like can be used.
  • the effect of the present invention does not change even after drying.
  • the same effect can be obtained by directly applying the compound.
  • pretreatments such as electrolytic degreasing and pickling can be applied as necessary before attaching the above substances. Further, even if the pretreatment is performed after the substance is adhered, the effect of the present invention can be obtained as long as the substance adheres to the steel sheet. Furthermore, a method of attaching at the time of rolling using a rolling oil containing the above compound may be used.
  • the adhesion amount of the substance is within a range of 0.01 to 1000 mg / m 2 in total (hereinafter also referred to as a specific element amount) in terms of the amount of elements specified in the present invention. This is because it is easier to control the hematite content to 7 O mass% or less in this range.
  • the specific element amount is O. Olmg / m 2 or more, it is easy to form the concentrated layer under the plating layer. Because. On the other hand, the reason why the specific element amount is set to lOOOmg / m 2 or less is not the reason for the effect of the present invention, but rather is economically advantageous.
  • the steel sheet to which at least one substance selected from the group consisting of the above-mentioned S, C, Cl, Na, K, B, P, F, N and these compounds is attached is heated.
  • An oxide film having a hematite content of 70 mas S % or less is formed on the surface of the steel sheet. For example, it can be easily achieved by heating a steel sheet to which the substance is attached.
  • the difference in the oxidation means does not affect the effect of the present invention, and any means may be used as long as the steel sheet can be oxidized.
  • the heating means may be a conventionally used heating method such as a panner heating, an induction heating, a radiant heating or a current heating, and is not particularly limited.
  • a heating furnace such as a conventional oxidation furnace or non-oxidation furnace can be used for the burner heating method.
  • the steel plate can be easily oxidized by setting the air-fuel ratio of the direct flame burner to more than 1.0.
  • the oxidation is preferably performed in an iron oxidizing atmosphere.
  • the steel plate can be easily oxidized by setting the atmosphere in the vicinity of the steel plate to be heated to an oxidizing atmosphere.
  • the oxidizing atmosphere is generally an atmosphere containing at least one oxidizing gas such as oxygen, water vapor and carbon dioxide, but is not particularly limited as long as the steel sheet can be oxidized.
  • the above shows a typical example, and in any case, it is sufficient that the steel sheet can be oxidized, and the means is not particularly limited.
  • the hematite content is reduced to 70 0 ⁇
  • the reason why it can be controlled to 3% or less is as follows. That is, in the case of a steel sheet with a high Si concentration in steel, with conventional oxidation means, Si in the steel is concentrated at the interface between the iron oxide and the underlying steel sheet to form a layered and dense si oxide film. End up. Since this layered Si oxide inhibits Fe diffusion from the base, it significantly suppresses the oxidation of iron on the surface, so hematite is a metal ion excess (n-type) oxide. Iron oxide with a high content of (F 0 3 ) is produced.
  • the upper limit is not particularly limited. However, it is more economical that the practical upper limit temperature is not more than the steel plate temperature required for the subsequent reduction treatment, for example, about 750 to 800 ° C.
  • oxidation of steel sheet produces an oxide film consisting of wustite (FeO), magnetite (Fe 3 0 4 ) and hematite () force, but the Si concentration in the steel is as high as 0.1 mass% or more.
  • FeO wustite
  • Fe 3 0 4 magnetite
  • hematite hematite
  • the Si concentration in the steel is as high as 0.1 mass% or more.
  • the content of hematite in the oxide film increases (see, for example, Nisshin Steel Making Technique No. 77, p. 1 (1998)).
  • the hematite content is 70 If it exceeds ma SS %, the wettability with molten zinc is reduced, and non-plating cannot be completely suppressed. Since it is preferable to suppress hematite in the oxide film as much as possible, it is needless to say that the hematite content may be O mass%. However, the hematite content is usually 10-70ma SS . /. It is preferably used in a degree.
  • the oxide film in the present invention rather than shall be limited to the above-mentioned Fe0, Fe 3 0 4 and Fe 2 0 3, includes oxide containing S i such an additive element for example in steel However, this does not impede the effects of the present invention.
  • the hematite content can be measured by the X-ray diffraction method (Cu tube, tube voltage: 50 kV and tube current: 250 mA) using a rotating vibration sample stage. Specifically, hematite (Fe 2 0 3 ), magnetite (Fe 3 0 4 ), and wustite (FeO) powder standard samples were prepared separately, and three types of samples with different mixing ratios (mass%) were prepared. Prepare and use for X-ray diffraction.
  • a calibration curve is created by calculating the relationship between the ratio ( fflaSS %) and diffraction peak intensity (cps). Based on this calibration curve, the hematite content (mass%) can be determined from the obtained diffraction peak intensity.
  • the oxide film obtained by the above method is preferably 0.01 to 5 g / m 2 of iron oxide in terms of oxygen amount.
  • the amount of oxygen is 0.01 g / m 2 , the amount of iron oxide is sufficient, and it becomes easier to suppress the surface concentration of Si.
  • the amount of oxygen is 5 g / m 2 or less, reduction in the post-process becomes easier, and alloying is promoted in the alloying process after the subsequent hot-dip galvanizing.
  • the following method can be illustrated as a quantification method of this oxygen amount in this oxide film. That is, it can be easily quantified by subtracting the oxygen content in the base steel plate from the total oxygen content in the molten dumbbell steel plate of the present invention by a wet analysis method. If a calibration curve is created in advance, a simple quantitative method using fluorescent X-rays or GDS is possible.
  • oxidation treatment is performed to contain hematite.
  • the oxide film formed on the steel sheet surface as described above is reduced.
  • This reduction method may be performed by applying a conventionally used method and is not particularly limited.
  • a reduction treatment is generally performed at a temperature of about 600 to 900 ° C. in a reducing atmosphere containing hydrogen in a radiant heating type annealing furnace.
  • a reducing atmosphere containing hydrogen in a radiant heating type annealing furnace.
  • any method may be used as long as the oxide layer on the steel sheet surface can be reduced.
  • the base steel sheet reduced by the above is immersed in a plating bath to give molten dumbbells.
  • This hot dip galvanizing treatment may be performed in accordance with a conventional method.
  • the base steel sheet is cooled in a non-oxidizing or reducing atmosphere to a temperature suitable for plating, usually approximately equal to the plating bath temperature.
  • the temperature of the plating bath is generally about 440 to 520 ° C, and the A1 concentration in the bath is generally about 0.1 to 0.2%.
  • the plating conditions such as the fitting temperature and the bathing composition may be changed depending on the application of the product, but the difference in the plating conditions does not affect the effect of the present invention and is not particularly limited. Absent. For example, other than A1 in the plating bath, Pb, Even if elements such as Sb, Fe, Mg, Mn, Ni, Ca, Ti, V, Cr, Co, and Sn are mixed, the effect of the present invention is not changed.
  • the method for adjusting the thickness of the plated layer after plating is not particularly limited.
  • gas wiping is used, and the thickness of the plating layer is adjusted by adjusting the gas pressure of the gas wiping, the distance between the wiping nozzles Z and the steel plate.
  • the thickness of the plating layer is not particularly limited, but is preferably about 3 to 15 jum. This is because sufficient weather resistance can be obtained at 3 m or more.
  • the length is 15 m or less, processability and economy are more advantageous.
  • any heating method conventionally used such as gas heating, induction heating, and current heating may be used, and it is not particularly limited.
  • the present inventors have made S, C, CI, a, K, B, P, F, N and S on the surface of the base steel sheet containing Si of 0.;! To 3 mass %.
  • the steel sheet is preferably oxidized in a CGL annealing furnace to form an oxide film, followed by reduction annealing to form the oxide film.
  • the present invention by attaching the substance to the base steel plate before annealing the base steel plate, that is, before the oxidation, even in the steel plate having a high Si content, a larger amount of iron oxide film than in the past can be obtained in the oxidation process. So that after the subsequent reduction annealing, Generation of Si surface enrichment that appeared on the surface of the underlying steel sheet can be effectively suppressed. As a result, when the base steel sheet after reduction annealing in accordance with the method of the present invention is melted, it is possible to obtain a plating layer with a good surface appearance without non-plating, and with excellent plating adhesion and slidability. A galvanized steel sheet is obtained.
  • the adhered substance can enter the surface layer of the steel sheet by a heat treatment such as an oxidation treatment.
  • a heat treatment such as an oxidation treatment.
  • the concentrated layer of the present invention refers to the concentration of at least one component selected from the group consisting of S, C, CI, Na, K, B, P, F and soot (hereinafter also referred to as a concentrated component). Means a region 10% or more higher than the concentration of the component in the base steel sheet.
  • the depth profile of the concentration component (element) in the depth direction is obtained from the surface of the plated steel sheet using GDS as shown in the examples, or the thickened layer of the plated steel sheet is obtained.
  • Depth profile obtained by performing line analysis of the cross section using EPMA shows the peak intensity appearing in the vicinity of the interface as a region that is 10% or more higher than the component strength of the underlying steel sheet.
  • the reason why the concentrated layer is defined as a region where the peak strength of the concentrated component in the vicinity of the interface is 10% or more higher than the strength of the component of the underlying steel sheet is that the reduction annealing is performed when this increment is less than 10%. This is because the surface concentration of Si at the time cannot be sufficiently suppressed.
  • the depth profile of the concentrated layer may be measured using the above GDS or the cross-sectional line analysis by EPMA.
  • the concentrated layer contains the concentrated component. It is preferable that the compound of the base steel plate and the component is dispersed. Care must be taken when performing line analysis by EPMA. That is, when the compound with the component of the base steel sheet is dispersed, the EPMA cross-sectional line analysis may analyze a portion where no compound exists. Therefore, EPMA line analysis is used. In this case, measurement is performed at five arbitrary locations on the cross section of the steel sheet, and the thickness of the region where the strength of the concentrated component is 10% or more higher than the strength of the component of the base steel sheet is obtained.
  • the concentrated layer is measured by obtaining an average value of the thickness of the film.
  • the amount of iron oxide formed increases, while the oxide of Si appears at the interface Z between the iron oxide and the iron or the iron. It is formed inside the side.
  • the iron oxide is reduced and converted into iron by the subsequent reduction treatment, the oxide of Si remains inside the ground iron.
  • the “oxide containing Si” of the present invention must contain Si and oxygen.
  • oxides of the components in steel may contain these double-salt complex salts, so it is not limited to Si oxides, and the types are not limited.
  • Typical “oxides containing Si” include Si0 2 , FeSi0 3 , Fe 2 Si0 4 , MnSi0 3, or a mixture thereof.
  • molten zinc plated steel sheet of the present invention 'Si:. 0. 1 ⁇ 3 steel plate containing 0 m aS s%, molten zinc plated, between Oyopi steel sheet and the molten zinc plated, Si-containing oxide and thickness: 0.01 to: 100 / m at least one selected from the group consisting of S, C, CI, Na, K, B, P, F and N It has a thickened layer of ingredients.
  • the hot-dip galvanized steel sheet according to the present invention is excellent and the adhesiveness and slidability are not yet clearly elucidated, but the present inventors speculate as follows. Yes.
  • the reason why the plating adhesion and the sliding property are improved by the presence of the oxide containing Si in the concentrated layer is considered as follows.
  • a concentrated layer of the component is formed under the plating layer, and the concentrated layer of parentheses is formed.
  • the thickness of the concentrated layer of the present invention must be controlled in the range of 0.01 to 100 / m. This is because if the thickness of the concentrated layer is less than 0.01 mm, the effect of improving the adhesiveness is not sufficiently exhibited, while if it exceeds 100 / m, the fatigue characteristics are deteriorated. More preferably, it is in the range of more than l m and 50 / z m or less.
  • the concentration of the component in the concentrated layer is preferably higher by 10% or more than the concentration of the component in the underlying steel plate.
  • such a concentrated layer has a depth profile obtained by performing a line analysis using depth profaile obtained from the cross-section of the steel plate using GDS or EPMA.
  • the peak intensity that appears in the vicinity of the interface is shown as a region that is 10% higher than the peak intensity of the railway.
  • the concentrated layer is preferably a dispersion of the compound of the concentrated component and the component of the underlying steel plate.
  • the component of the base steel sheet is not only Fe,
  • MnS is a very stable compound in steel among various assumed compounds, so it is easy to be produced and manufacturing conditions can be controlled easily.
  • S is selected as an element to be attached to the steel plate before the above-described oxidation treatment, S is formed on the surface layer of the steel plate (under fitting after plating) in the oxidation treatment and reduction treatment steps. Combines with Mn and thickens.
  • the appropriate amount of the compound produced is that MnS with a particle size of 50 nm or more exists in an arbitrary cross-section in a direction parallel to the interface between the plating layer and the base steel sheet, at least 5 per 20 m. It is preferable to do.
  • MnS here means that the main component is formed by Mn and S, and there is no problem even if other elements such as Fe are mixed.
  • identification of the compound and determination of the dispersed state and number can be performed using EDS, electron beam diffraction (TED), etc. as necessary. .
  • the amount of Si-containing oxide contained in the concentrated layer is preferably in the range of 0.01 to 1 g / m 2 in terms of oxygen.
  • the amount of the Si-containing oxide is 0.01 g / m 2 or more, the plating adhesion and sliding properties are remarkably improved.
  • it is more economical that the amount of the Si-containing oxide is 1 g / m 2 or less.
  • the oxide contains Si by EDX analysis of Samnole adjusted by TEM replication force method.
  • the hot dip galvanized steel sheet of the present invention When the above-described hot dip galvanized steel sheet of the present invention is alloyed, it can be carried out at a low alloying temperature, and it has not only excellent adhesiveness and frictional resistance but also excellent puffing resistance. Combined alloyed molten dumbbell steel plate is obtained.
  • a conventional hot-dip galvanized steel sheet is alloyed, a phase with a higher hardness than that of the base steel sheet is formed at the interface between the dumbbell and the base steel sheet.
  • the hot dip galvanized steel sheet of the present invention when the hot dip galvanized steel sheet of the present invention is alloyed, it has an enriched layer under the plating layer, so the interface between the dumbbell and the base steel sheet.
  • the mechanical properties in the vicinity, especially the hardness of the underlying steel sheet, is "a value close to that of the phase, so the strain imparted to the interface when the underlying steel sheet is deformed is effectively reduced. As a result, plating adhesion is improved. It is thought to do.
  • the surface concentration of Si during annealing is suppressed, so that alloying is possible at a relatively low temperature. There is also an advantage that is suppressed.
  • the slidability of alloyed molten zinc is manifested by changes in alloying behavior. That is, as described above, the Si surface enrichment generated on the surface of the underlying steel sheet during annealing slows the alloying rate. This is because the surface concentrate which selectively oxidizes and concentrates on the surface after annealing suppresses the alloying reaction between Zn and Fe. As a result, the plated layer after alloying becomes a plated layer with severe irregularities because the uniform reaction between Zn and Fe is inhibited. In addition, the crystal of the alloy of Zn and Fe becomes coarse. The slidability of the plating layer deteriorates due to unevenness of the plating layer and coarsening of the crystal grains due to this alloying suppression.
  • the concentrated layer of the component exists below the adhesive layer, so that the Si surface concentration during annealing is higher than in the normal case. Alloying is suppressed and alloying is promoted. As a result, the reaction between Zn and Fe is uniform, and the plating layer becomes smooth. Also, the crystal grains become finer and show better slidability than the Si-containing steel produced by the conventional manufacturing method described above.
  • the hot dip galvanized steel sheet of the present invention a (reduced) iron layer exists under the plating layer, and the concentrated layer containing an oxide containing Si exists under the plated layer. And described above.
  • the dumbbell metallization and (reduced) iron alloying naturally proceeds. Therefore, in the obtained alloyed hot-dip galvanized steel sheet, an iron layer can be confirmed under the zinc-plated layer. It may disappear.
  • the “concentrated layer of the component containing an oxide containing Si” exists under the plating layer. Belongs to a range.
  • Oxidation treatment conditions are also shown in Table 2_1, Table 3_1 and Table 4-11. '
  • annealing and plating without heat treatment were also performed.
  • the heating condition was to change the maximum temperature of the steel sheet in the atmosphere.
  • the holding time at the highest temperature was 1 second, and then quenched with nitrogen gas.
  • the annealing conditions were 10 vol% hydrogen + nitrogen atmosphere (dew point: 35 ° C), plate temperature: 830 ° C, and holding time: 45 seconds.
  • Plating conditions include 0.14 mass% of A 1 (Fe saturation) 4 60 ° C zinc plating bath, penetration plate temperature: 4 60 ° C and immersion time: 1 second, plating The subsequent surface appearance was evaluated. After plating, the amount of adhesion was adjusted to 45 g / m 2 on one side with a nitrogen gas wiper.
  • the thickness and concentration of the concentrated component were measured, and the oxide containing Si under the plating layer was quantified. According to the evaluation preparations, the adhesion and plating adhesion were evaluated.
  • the properties of the thickened layer are shown in Table 2-2, Table 3-2 and Table 4-12.
  • some plated steel sheets are subjected to alloying treatment (heating rate: 40 ° C / s) for 10 seconds in an electric heating furnace after plating, and the Fe content in the plating layer is 10
  • the alloying rate was evaluated.
  • the evaluation criteria are as described later.
  • a 90 ° bending test was performed using a sample having an Fe content of 10 ⁇ 0.5 mass% in the plating layer, and the pudding resistance was evaluated according to the evaluation criteria described later.
  • the evaluation of slidability was evaluated according to the evaluation criteria described later.
  • Table 2-3 Table 3-3, and Table 4-3.
  • Table 2-1 to Table 4-3 at least selected from the group consisting of S, C, CI, Na, K, B, P, F, N and these compounds on the steel sheet surface It is obtained by attaching a compound containing one kind of substance, and then oxidizing it to form an oxide film with a hematite content of 70 maSS % or less and then annealing under reducing conditions. It can be seen that even when the steel plate is used as a base, there is no plating, no significant alloying delay, and excellent powdering resistance and sliding properties.
  • the obtained molten dumbbell-plated steel sheet or alloyed hot-dip galvanized steel sheet has a concentrated layer under the plating layer, and the concentrated layer contains an oxide containing Si. You can see that In addition, it was confirmed that the oxide film formed after the oxidation treatment had a structure mainly composed of magnetite and wustite except for hematite.
  • Example B These substances include (o) potassium chloride (50 g / l), (p) ammonium oxalate (lOOg / 1), (q) sulfuric acid (50 gZl), (r) sodium hydroxide (30 g / 1) and (S) Same as Example A, except that sodium tetraborate (3 g / 1) was applied in the amount shown in Table 5_1, and the heat treatment was performed in 0.1 lvol% oxygen + nitrogen atmosphere. Plated steel sheets were produced under the same conditions and evaluated in the same manner. Table 5-2 shows the properties of the concentrated layer. The evaluation results of the plated steel sheet thus obtained are also shown in Table 5-3.
  • the substance is adhered to the steel sheet surface, and then oxidized to form an oxide film having a hematite content of 70 mass% or less, followed by reduction.
  • the high Si-containing base steel sheet obtained by annealing under the conditions shows no powdering, no significant delay in alloying, and excellent powdering resistance and slidability after plating. Recognize.
  • the obtained hot dip galvanized steel sheet or alloyed hot dip galvanized steel sheet has a concentrated layer below the plating layer, and the concentrated layer contains an oxide containing Si. You can see that It was confirmed that the oxide film formed after the oxidation treatment had a structure mainly composed of magnetite and wustite, except for hematite.
  • the substance was adhered to the steel plate surface, and then oxidized to form an oxide film with a hematite content of 70 mas S % or less.
  • Substrate steel sheets with high Si content which are obtained by annealing under reducing conditions later, have no unplating, no significant alloying delay after the plating, and exhibit excellent powdering resistance and sliding properties. Recognize.
  • the obtained hot-dip galvanized steel sheet It can also be seen that the alloyed hot-dip galvanized steel sheet has a concentrated layer under the plating layer, and the concentrated layer contains an oxide containing Si. It was confirmed that the oxide film formed after the oxidation treatment had a structure mainly composed of magnetite and wustite except for hematite.
  • each evaluation standard of plating quality is as follows.
  • the concentration layer thickness represents the thickness of the region where the depth profile is slightly higher than the strength B of the concentration component in the steel for the Depth Profile. Described in.
  • the concentration layer thickness represents the thickness of the region where the depth profile is slightly higher than the strength B of the concentration component in the steel for the Depth Profile. Described in.
  • For line analysis by EPMA measurements were taken at five arbitrary locations on the cross section of the steel sheet, and the thickness of the region where the strength of the concentrated component was 10% or more higher than the strength of the steel was calculated. By calculating the average value of the thickness and the average value of the peak intensity A, the thickness of the concentrated layer and the degree of concentration were obtained.
  • the conversion from the sputter time to the thickened layer thickness is iron shear under the following GDS conditions. Kuta speed: Converted from 0.04 / x m / sec.
  • Beam current 0.05 ⁇
  • the plating layer is dissolved and removed with the alkaline solution shown below, and the oxygen of this steel sheet and steel sheet mechanically ground on both sides of the steel sheet is 100 / m. It was determined from the difference between the analytical values. The inclusion of Si in the oxide has been confirmed by EDX analysis of samples prepared by the TEM replica method.
  • Trietano Lamine 2 ⁇ 1%
  • a ball impact test was performed using the obtained molten dumbbell-plated steel sheet to evaluate the plating peeling state when the tape was peeled off.
  • the test conditions were as follows: a 2.8 kg weight was dropped from a height of 1 m onto a hot-dip galvanized steel plate placed on a hemispherical projection with a diameter of 1/2 inch, and then the tape was peeled off on the convex side. did.
  • Example Steel plates were produced under the same conditions as those of Example IV.
  • the evaluation method is almost the same as in Example A.
  • ⁇ excellent (count: less than 400 0 0) in order to evaluate finer differences
  • Table 7 shows the results obtained along with the adhered substances, oxidation treatment, and concentrated layer properties.
  • the concentrated layer should be in a state in which the compound of the concentrated component and the component in the underlying steel is sufficiently dispersed. Thus, more excellent characteristics can be obtained.
  • Example 1 A 0.62 50
  • Example 2 B 0.58 50
  • Example 3 C 0.59 55 Phosphoric acid 100 70 Yes 650
  • Example 4 D 0.6 60
  • Example 5 G 0.55 60
  • Example 6 H 0.57 65
  • Example 7 B 0.45 0
  • Example 8 C 0.48 0
  • Example 9 G 0.52 5
  • Example 10 H Hydrochloric acid 1 0.1 Yes 550
  • Example 11 I 0.49 10
  • Example 12 J 0.5 10
  • Example 13 A 0.75 0
  • Example 14 B 0.71 0
  • Example 15 C 0.68 0
  • Sodium fluoride 2 1 Yes 700
  • Example 16 E 0.77 0
  • Example 17 F 0.69 0
  • Example 18 H 0.69 0
  • Example 19 A 0.55 0
  • Example 20 B 0.52 0
  • Example 21 C 0.54 0
  • Example 22 D 0.5 0
  • Example 23 G 0.52 5
  • Example 24 H 0.53 5
  • Example 25 A 0.51 0
  • Example 26 B 0.49 0
  • Example 27 C 0.48 5 Potassium hydroxide 100 100 Yes 600
  • Example 28 E 0.45 5
  • Example 29 F 0.45 10
  • Example 30 H 0.45 20 Comparative Example 1
  • B 0.18 90
  • Comparative Example 2 C 0.12 90
  • Comparative Example 3 G 0.07 90 None None None Yes 600
  • Comparative Example 4 H 0.05 95 Comparative Example 5 I 0.2 90 Comparative Example 6 J 0.08 95 Comparative Example 7
  • A--Comparative Example 8 B--Comparative Example 9 C--
  • Comparative Example 16 D 0.05 85 Comparative Example 17 G 0.06 85 Comparative Example 18 H 0.05 85 Comparative Example 19
  • a 0.006 80 Comparative Example 20 B 0.007 80 Comparative Example 21 C 0.006 75 is acid 1 0.1 Yes 400 Comparative Example 22 D 0.006 80 Ratio shelf 23 G 0.005 80 Comparative example 24 H 0.002 75 Comparative example 25 A 0.01 85 Comparative example 26 B 0.02 85 Comparative example 27 C 0.02 85 Phosphoric acid 100 70 Yes 400 Comparative example 28 D 0.01 85 Comparison 3 ⁇ 429 G 0.005 90 Comparison i row 30 H 0.005 90 Ratio drum 31 A 0.01 80 Ratio drum 1 row 32 B 0.02 80 Ratio drum 1 row 33 C 0.02 80 Ammonium thiocyanate :: 50 50 Yes 500
  • Example 34 5.1 5 300 300 0.9
  • Example 35 4.9 5 300 300 0.7
  • Example 36 5.3 5 300 300 0.7
  • Example 37 10.5 10 500 500 0.12
  • Example 38 10.4 10 500 500 0.12
  • Example 39 10.2 10 500 500 0.1
  • Example 40 10.1 10 500 500 0.1
  • Example 41 9.8 10 500 500 0.9
  • Example 42 10.0 10 500 500 0.9
  • Example 43 3.1 3 400 400 0.08
  • Example 44 3.0 3 400 400 0.08
  • Example 45 3.0 3 400 400 0.07
  • Example 46 2.8 3 400 400 0.07
  • Example 47 3.5 3 400 400 0.06
  • Example 48 3.2 3 400 400 0.06
  • Example 49 15.1 15 100 100 0.03
  • Example 50 14.8 15 100 100 0.03
  • Example 51 15.0 15 100 100 0.03
  • Example 52 15.8 15 100 100 0.02
  • Example 53 15.3 15 100 100 0.02
  • Example 54 15.4 15 100 100 0.02
  • Example 55 20.0 20 600 600 0.2
  • Example 56 20.1 20 600 600 0.2
  • Example 57 20.1 20 600 600 600
  • Comparative Example 40 One One--0.001 Comparative Example 43 (0.006) (0.006) 8 8 0.006 Comparative Example 44 (0.005) (0.005) 8 8 0,005 Comparison Example 45 (0.004) (0.004) 8 8
  • Comparative Example 52 (0.004) (0.004) 7 7 0.004 Comparative Example 53 (0.003) (0.003) 7 7 0.003 Comparative Example 54 (0.003) (0.003) 7 7 0.003 Comparative Example 55 (0.005) (0.005) 5 5 0.005 Comparative Example 56 (0.004) (0.004) 5 5 0.004 Comparative Example 57 (0.004) (0.004) 5 5 5
  • Oxide content thickening component GDS EPMA GDS EP A (g / m z) carried 61 three to 300 - 0.15 embodiments Italy 62 3 - 300 - 0.15 Real ⁇ 63 3 - 300 - 0.16 embodiment 64 3 - 300 one 0.15 real ⁇ 65 3 -300 1 0.12 Implementation 66 3-300 1 0.1 Implementation 67 3-300-0.18
  • Example 105 A 0.35 0
  • Example 106 B 0.39 0
  • Example 107 C 0.4 0
  • Example 108 D 0.36 0
  • Example 109 G 0.37
  • Example 110 H 0.39
  • Example 111 B 0.54 0
  • Example 1 12 C 0.52 0
  • Example 113 G 0.49 0
  • Example 1 15 I 0.51 0
  • Example 1 16 J 0.5 0
  • Example 1 17 A 0.59 45
  • Example 1 18 B 0.6 45
  • Example 1 19 C 0.62 50
  • Example 120 E Lead chloride 1 1 650
  • Example 125 C 0.55 0
  • a hot-dip galvanized steel sheet having excellent plating adhesion and slidability can be obtained even when a base steel sheet having a high Si content is used. Further, the alloyed hot-dip galvanized steel sheet obtained by alloying the hot metal plating is excellent in powdering resistance. In addition, double-sided steel sheets can be obtained with high productivity.

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Abstract

L’invention concerne une feuille d’acier zinguée à chaud comprenant une feuille d’acier contenant de 0,1 à 3,0 % en masse de Si, une couche de zingage à chaud, et, formée entre ladite feuille d’acier et ladite couche de zingage à chaud, une couche enrichie en au moins un composant sélectionné parmi le groupe consistant en S, C, Cl, Na, K, B, P, F et N englobant un oxyde contenant du Si et d’une épaisseur de 0,01 à 100 µm. Ladite feuille d’acier zinguée à chaud est exempte du phénomène de non-placage, présente un fin aspect superficiel, une excellente adhérence d’une couche de placage et d’excellentes caractéristiques de glissement, même si elle utilise une feuille d’acier de base d’une teneur relativement importante en Si. De plus, une feuille d’acier alliée zinguée à chaud produite par alliage de ladite feuille d’acier zinguée à chaud est également excellente en matière de résistance au poudrage.
PCT/JP2005/018904 2004-10-07 2005-10-07 Feuille d’acier zinguée à chaud et procédé de production idoine WO2006038736A1 (fr)

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US11/664,490 US20080070060A1 (en) 2004-10-07 2005-10-07 Hot-Dip Galvanized Sheet and Method for Manufacturing Same
CA002582762A CA2582762A1 (fr) 2004-10-07 2005-10-07 Feuille d'acier zinguee a chaud et procede de production idoine
EP05793822A EP1806422A4 (fr) 2004-10-07 2005-10-07 Feuille d'acier zinguée à chaud et procédé de production idoine

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008144267A (ja) * 2006-11-16 2008-06-26 Jfe Steel Kk 合金化溶融亜鉛めっき鋼板の製造方法

Families Citing this family (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4411326B2 (ja) * 2007-01-29 2010-02-10 株式会社神戸製鋼所 リン酸塩処理性に優れた高強度合金化溶融亜鉛めっき鋼板
JP5119903B2 (ja) * 2007-12-20 2013-01-16 Ｊｆｅスチール株式会社 高強度溶融亜鉛めっき鋼板および高強度合金化溶融亜鉛めっき鋼板の製造方法
KR101008117B1 (ko) * 2008-05-19 2011-01-13 주식회사 포스코 표면특성이 우수한 고가공용 고강도 박강판 및용융아연도금강판과 그 제조방법
KR101027250B1 (ko) * 2008-05-20 2011-04-06 주식회사 포스코 고연성 및 내지연파괴 특성이 우수한 고강도 냉연강판,용융아연 도금강판 및 그 제조방법
JP2010126757A (ja) * 2008-11-27 2010-06-10 Jfe Steel Corp 高強度溶融亜鉛めっき鋼板およびその製造方法
CN105908069B (zh) * 2009-04-14 2018-03-06 新日铁住金株式会社 切削性优异的低比重热锻造用棒钢
JP2011224584A (ja) * 2010-04-16 2011-11-10 Jfe Steel Corp 熱延鋼板の製造方法及び溶融亜鉛めっき鋼板の製造方法
TWI554645B (zh) * 2012-04-17 2016-10-21 杰富意鋼鐵股份有限公司 鍍敷密黏性及滑動特性優異之合金化熔融鍍鋅鋼板之製造方法
EP2851440A1 (fr) * 2013-09-19 2015-03-25 Tata Steel IJmuiden BV Acier pour formage à chaud
US10890363B2 (en) 2015-09-07 2021-01-12 Panasonic Intellectual Property Management Co., Ltd. Refrigerant compressor and refrigeration device including refrigerant compressor
KR102493977B1 (ko) * 2020-12-13 2023-01-31 주식회사 포스코 도금품질이 우수한 고강도 용융아연도금강판, 도금용 강판 및 이들의 제조방법
KR20230171085A (ko) * 2022-06-10 2023-12-20 주식회사 포스코 도금품질이 우수한 강판 및 그 제조방법
KR20230171083A (ko) * 2022-06-10 2023-12-20 주식회사 포스코 도금품질이 우수한 열간 프레스 성형용 도금강판, 강판 및 이들의 제조방법
KR20230171082A (ko) * 2022-06-10 2023-12-20 주식회사 포스코 도금품질이 우수한 열간 프레스 성형용 도금강판, 강판 및 이들의 제조방법
WO2023239208A1 (fr) * 2022-06-10 2023-12-14 주식회사 포스코 Tôle d'acier galvanisée par immersion à chaud et à résistance élevée présentant une excellente qualité de placage, tôle d'acier de placage et ses procédés de fabrication
KR20230171084A (ko) * 2022-06-10 2023-12-20 주식회사 포스코 도금품질이 우수한 강판 및 그 제조방법
WO2023239206A1 (fr) * 2022-06-10 2023-12-14 주식회사 포스코 Tôle d'acier galvanisée par immersion à chaud à haute résistance ayant une excellente qualité de placage, tôle d'acier de placage, et procédés de fabrication associés

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05106001A (ja) * 1991-10-15 1993-04-27 Sumitomo Metal Ind Ltd 珪素含有鋼板の溶融亜鉛めつき方法
JPH08170160A (ja) * 1994-12-19 1996-07-02 Sumitomo Metal Ind Ltd Ｓｉ含有高張力（合金化）溶融亜鉛めっき鋼板の製造方法
JPH0941110A (ja) * 1995-07-31 1997-02-10 Kawasaki Steel Corp 高張力溶融亜鉛めっき鋼板の製造方法
JPH1046304A (ja) * 1996-07-26 1998-02-17 Sumitomo Metal Ind Ltd 合金化溶融亜鉛めっき鋼板の製造方法
JPH1150223A (ja) * 1997-08-05 1999-02-23 Nkk Corp Ｓｉ含有高強度溶融亜鉛めっき鋼板およびその製造方法

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA2110281C (fr) * 1992-03-30 2001-05-15 Yoichi Tobiyama Tole d'acier a traitement de surface reduisant les defauts de placage, et sa fabrication
KR960013481B1 (ko) * 1993-06-29 1996-10-05 니홍고오깡 가부시키가이샤 표면처리강판 및 그 제조방법
JP4886118B2 (ja) * 2001-04-25 2012-02-29 株式会社神戸製鋼所 溶融亜鉛めっき鋼板
EP2343393B2 (fr) * 2002-03-01 2017-03-01 JFE Steel Corporation Plaque d'acier traitée en surface et son procédé de production

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05106001A (ja) * 1991-10-15 1993-04-27 Sumitomo Metal Ind Ltd 珪素含有鋼板の溶融亜鉛めつき方法
JPH08170160A (ja) * 1994-12-19 1996-07-02 Sumitomo Metal Ind Ltd Ｓｉ含有高張力（合金化）溶融亜鉛めっき鋼板の製造方法
JPH0941110A (ja) * 1995-07-31 1997-02-10 Kawasaki Steel Corp 高張力溶融亜鉛めっき鋼板の製造方法
JPH1046304A (ja) * 1996-07-26 1998-02-17 Sumitomo Metal Ind Ltd 合金化溶融亜鉛めっき鋼板の製造方法
JPH1150223A (ja) * 1997-08-05 1999-02-23 Nkk Corp Ｓｉ含有高強度溶融亜鉛めっき鋼板およびその製造方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008144267A (ja) * 2006-11-16 2008-06-26 Jfe Steel Kk 合金化溶融亜鉛めっき鋼板の製造方法

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KR100883245B1 (ko) 2009-02-10
CA2582762A1 (fr) 2006-04-13
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