EP0632140B1 - Verfahren zum Herstellen eines verzinkten Bleches - Google Patents

Verfahren zum Herstellen eines verzinkten Bleches Download PDF

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Publication number
EP0632140B1
EP0632140B1 EP94109981A EP94109981A EP0632140B1 EP 0632140 B1 EP0632140 B1 EP 0632140B1 EP 94109981 A EP94109981 A EP 94109981A EP 94109981 A EP94109981 A EP 94109981A EP 0632140 B1 EP0632140 B1 EP 0632140B1
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EP
European Patent Office
Prior art keywords
coating layer
alloy
zinc
layer
steel sheet
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
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EP94109981A
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English (en)
French (fr)
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EP0632140A1 (de
Inventor
Masaki C/O Intellectual Property Dept. Abe
Satoru C/O Intellectual Property Dept. Ando
Toyofumi C/O Intellectual Pty Dept. Watanabe
Yuiimitsu C/O Intellectual Pty Dept. Shiohara
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JFE Engineering Corp
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NKK Corp
Nippon Kokan Ltd
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Publication date
Priority claimed from JP5158503A external-priority patent/JPH0711409A/ja
Priority claimed from JP5218565A external-priority patent/JPH0770788A/ja
Priority claimed from JP5311937A external-priority patent/JPH0770763A/ja
Application filed by NKK Corp, Nippon Kokan Ltd filed Critical NKK Corp
Publication of EP0632140A1 publication Critical patent/EP0632140A1/de
Application granted granted Critical
Publication of EP0632140B1 publication Critical patent/EP0632140B1/de
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Classifications

    • 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
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/021—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material including at least one metal alloy layer
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • 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
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/023—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material only coatings of metal elements only
    • C23C28/025—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material only coatings of metal elements only with at least one zinc-based layer
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D3/00—Electroplating: Baths therefor
    • C25D3/02—Electroplating: Baths therefor from solutions
    • C25D3/12—Electroplating: Baths therefor from solutions of nickel or cobalt
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/48—After-treatment of electroplated surfaces
    • C25D5/50—After-treatment of electroplated surfaces by heat-treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0478—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular surface treatment

Definitions

  • the present invention relates to a method for producing zinc coated steel sheet having excellent corrosion resistance suitable for automobile sheets.
  • Steel sheets of automobile body are mainly rust-resistant steel sheets from the viewpoint of reliability to sustaining rust preventive performance for a long period of service.
  • rust-resistant steel sheets zinc coated steel sheet and alloyed zinc coated steel sheet are most widely used.
  • corrosion-resistant steel sheets which improve their own corrosion resistance by their composition are also used. Examples of that type of corrosion-resistant steel sheet are disclosed in JP-A-54-75421 and JP-A-56-9356 (the term "JP-A-" referred to herein signifies "unexamined Japanese patent publication").
  • the corrosion resistance is maintained with a stable rust layer which is formed on the surface of the steel sheet during the corrosion process.
  • various kinds of additives are required, and a significant amount of those additives are needed to obtain a satisfactory corrosion resistance.
  • the additives effectively used to form the stable rust layer are, however, limited to those applied during steelmaking process and existing in the surface layer among those uniformly distributed within the steel sheet. In other words, those additives remained inside the steel sheet are useless in terms of corrosion resistance.
  • the additives also play a role to control the mechanical characteristics of the steel sheet. Accordingly, a restriction of the mechanical characteristics sometimes limits the amount of the additives for improving the corrosion resistance, which suppresses the sufficient effect of corrosion resistance.
  • a method disclosed in JP-A-59-170288 improves the corrosion resistance by forming a zinc coating layer on a corrosion-resistant steel sheet.
  • the presented zinc coating is an alloy electroplating, and the method has a disadvantage of high production cost compared with hot dip galvanizing method.
  • the hot dip galvanizing has an advantage of lower cost than the electroplating, but the former has a disadvantage of rather poor workability and poor adhesiveness of the coating layer under a certain combination of steel sheet composition and amount of additives.
  • the reason of the disadvantage is that the workability and adhesiveness of the hot dip galvanizing largely depend on the alloy layer formed by the reaction between the hot dip galvanized layer and the steel sheet and that a part of the additives interfere the reaction to induce irregular formation of the alloy layer.
  • JP-A-3-24255 and JP-A-62-139860 disclose a method for improving the adhesiveness of coating layer by applying "pre-coating" on the steel sheet surface by electroplating followed by hot dip galvanizing.
  • This method aims mainly to improve the adhesiveness of the coating layer by "pre-coating", and very little effect of corrosion resistance is expected. In other words, this method does not consider the composition, amount, and mode of the "pre-coating" necessary to improve the corrosion resistance.
  • JP-A-57-171692 discloses a method for coating steel sheet, where a nickel layer is coated on a steel sheet, and a nickel diffusion layer is formed within the steel sheet by heating the steel sheet in a non-oxidizing atmosphere, and a Zn-Ni alloy coating is applied on the steel sheet.
  • Ni-Fe diffusion layer stabilizes the surface condition of the steel sheet to suppress the beginning of corrosion and that once the corrosion of the base iron plate starts, however, the insufficient density of the corrosion products allows an easy permeation of water or oxygen which enhances the corrosion through the corrosion products, which can not inhibit the progress of corrosion.
  • JP-B-61-60914 discloses a technology relating to a high corrosion-resistance surface treated steel sheet.
  • a coating of a metal selected from the group of Zn, Ni, Sn, Cr, or alloy consisting mainly of these metals is applied to the steel sheet.
  • the coated steel sheet is heated in a non-oxidizing atmosphere to form a metallic diffusion layer in the steel.
  • a Zn-Ni alloy coating is applied on the metal surface.
  • the technology however, also gives less effect for improving corrosion resistance once the corrosion of base iron plate occurs because the components such as Zn, Ni, Sn, Cr, etc.
  • JP-A-63 312 960 relates to a method for manufacturing hot-dipped zinc alloy coating steel sheet having good workability, wherein prior to zinc coating a preplating step is performed, wherein a Ni-P, Co-P or Fe-P coating is applied in such an amount that the amount of P exceeds 50 mg/m 2 .
  • JP-A 4-6259 relates to a method for manufacturing hot-dip zinc alloy coating steel sheet having good workability where a preplating step providing a Fe, Fe-Ni, Fe-Mo or Ni-P coating layer on the steel sheet is performed.
  • a preplating step providing a Fe, Fe-Ni, Fe-Mo or Ni-P coating layer on the steel sheet is performed.
  • the alloying ratio in the preplating systems this is not particularly limited, and in the Ni-P system a higher P content is preferred.
  • the object of the present invention is to provide a method for producing zinc coated steel sheet having excellent corrosion resistance.
  • the present invention provides a method for producing zinc coated steel sheet, comprising the steps of:
  • the present invention also provides a method for producing zinc coated steel sheet, comprising the steps of:
  • the present invention further provides a method for producing zinc coated steel sheet, comprising the steps of:
  • Steel sheets applied in the present invention are hot-rolled steel sheets or the like, and their thickness is of 1.6 to 4.5mm.
  • the steel sheets of the present invention include steel strips.
  • the steel sheets undergo pickling and descaling.
  • On one or both sides of the steel sheets are coated with Ni-P alloy coating layer.
  • the Ni-P coating layer has a Ni-P alloy composition containing P of 8 to 15wt.%. The reason of limiting the P content is that a Ni-P alloy coating having the composition shows an amorphous-like structure.
  • Addition of less than 8wt.% P gives a crystalline Ni-P alloy coating layer and results in a non-uniform distribution of P. As a result, a stable corrosion resistance can not be obtained because the composition of diffused alloy layer formed during a heat treatment is not uniform and because the homogeneity and denseness of the rust formed during the initial stage of corrosion process are not sufficient.
  • Addition of above 15wt.% P induces a brittle Ni-P alloy coating and results in a poor adhesiveness of the coating layer. Consequently, an excessive addition of P tends to separate the coating layer before forming a hot dip galvanized layer. Therefore, the present invention specifies the content of P in the above described range. Preferable P content is in a range of from 10 to 13wt.%.
  • a steel sheet may be coated with a Ni-P alloy system coating layer which is a composite of Ni-P combined with at least one element selected from the group of W, Mo, Cr, and Cu in an amount of up to 15wt.%.
  • Ni and P The role of Ni and P is described above.
  • W, Mo, Cr, and Cu they play a role of inhibitor against the corrosion of steel and they also provide an effect to further improve the denseness and stability of the rust generated in the initial stage of corrosion process owing to the synergistic effect with Ni and P.
  • the present invention specifies the sum of them as 15wt.% or less. Increase of the content of W, Mo, Cr, and Cu improves the corrosion resistance.
  • the present invention specifies the content of the sum of W, Mo, Cr, and Cu to the range described above.
  • a preferable lower limit of the content to perform the effect of W, Mo, Cr, and Cu is 0.5wt.%.
  • a preferred range of coating weight of the Ni-P alloy coating layer is from 0.5 to 8 g/m 2 . If the coating weight is less than 0.5 g/m 2 , the effect for improving the corrosion resistance is not necessarily sufficient, and if the coating weight exceeds 8 g/m 2 , the performance improvement can not correspond to the cost increase, which is not efficient for practical point of view.
  • Ni-P alloy coating layer There are several proposed methods for forming Ni-P alloy coating layer.
  • electroplating or electroless coating (chemical coating) is preferable from the stand point of simple operation and uniformity of obtained film quality.
  • the coating can be applied after the pickling treatment at the exit of the picking. This treatment allows to form effectively a pre-coating film having a good adhesiveness without giving a further cleaning stage to the hot rolled steel sheet which was pickled and activated.
  • an Fe-Ni-P diffused alloy layer is formed by heating the steel sheet.
  • the thermal diffusion can be performed by using a hot dip galvanizing equipment.
  • a continuous hot dip galvanizing facility of Sendzimir type is provided with a heat treatment furnace operated in a non-oxidizing atmosphere aiming at the annealing and the surface activation of the steel sheets.
  • the Ni-P alloy coating layer undergoes an adequate heat treatment in the heat treatment furnace, where the coating layer reacts with the steel base plate to form an alloy layer by mutual diffusion of Fe, Ni, and P.
  • a preferable maximum sheet temperature of the heat treatment is from 500°C to 800°C.
  • the temperature below 500°C does not form a sufficient diffused alloy layer between the Ni-P alloy coating layer and the steel sheet surface, and gives less effect for improving the corrosion resistance because a stable initial stage rust can not be formed during the corrosion process.
  • the temperature above 800°C likely induces pickup of coating metal onto the rolls inside of the heat treatment furnace, and may cause surface flaws.
  • the holding time at the maximum sheet temperature is preferably from 1 to 30 sec., though it depends on the temperature level.
  • the holding time less than 1 sec. hardly forms the sufficient diffused alloy layer, and results in an insufficient improvement of corrosion resistance.
  • the holding time above 30 sec. tends to induce a brittle interface layer caused by an excessive diffusion alloying phenomenon, which may degrade the adhesiveness and workability of the coating layer.
  • the preferred depth of the diffused alloy layer is from 0.1 to 20 ⁇ m to effectively function the adhesiveness and workability of the coating layer.
  • a Ni-P alloy coating layer undergoes heat treatment, two types of coating structure appear. The one is that a part of the Ni-P alloy coating layer forms a diffused alloy layer and forms the steel sheet / diffused alloy layer / Ni-P alloy coating layer structure. The other is that all the Ni-P alloy coating layer forms a diffused alloy layer to give the steel sheet / diffused alloy layer structure.
  • the present invention includes both cases.
  • the steel sheet After forming the diffused alloy layer, the steel sheet is fed to the hot dip galvanizing bath.
  • the coating weight of the hot dip galvanized coating is preferably of 20 to 120 g/m 2 . Too small coating weight can not give a good corrosion resistance, and excessive coating weight degrades the workability of coating layer.
  • Hot dip galvanizing bath may be the one containing a slight amount of Al, which has widely been used. For an application needed a better paintability, a formed hot dip galvanized coating to a specified coating weight may successively be heated to alloy the coating layer. Alloying rate is calculated as follows; Fe and a part of components in the Ni-P alloy layer are divided by the hot dip galvanized coating layer. The alloying rate is expressed by wt.%.
  • the preferred alloying rate is in a range of from 7 to 15wt.%.
  • the alloying rate below 7wt.% is difficult to obtain the effect for improving paintability, and the alloying rate above 15wt.% tends to degrade the workability of coating layer.
  • the zinc coated steel sheet of the present invention obtained by the procedure described above gives better corrosion resistance than a zinc coated steel sheet prepared by a conventional method.
  • a diffused alloy layer consisting mainly of Fe-Ni-P is formed at the interface between the base steel sheet and the coating layer and that the formed intermediate layer contributes to the improvement of corrosion resistance.
  • the intermediate diffused alloy layer forms a uniform and dense iron rust during the initial stage of corrosion process, which suppresses the cathode reaction.
  • Ni-P alloy coating Three types of steel sheet as the base plate for coating underwent Ni-P alloy coating to form Ni-P alloy coating layer on the surface thereof.
  • the Ni-P alloy coating is referred to as the "pre-coating".
  • the pre-coated steel sheets were subjected to heat treatment to form the diffused alloy layer of Fe-Ni-P system on the surface thereof. After the heat treatment, hot dip galvanizing was applied to the steel sheets.
  • Table 1 shows the thickness and composition of the steel sheets employed.
  • the steel sheet C is a corrosion resistant steel sheet containing Cr and Mo.
  • Table 2 shows the pre-coating condition.
  • the composition of the coating solution is represented by the unit of gram per liter.
  • the pre-coating of No. 8, 9, 10, and 15 were prepared by electroless coating.
  • the coating solution contained pH buffer agent or stabilizer such as boric acid and sodium citrate.
  • the coating weight was adjusted by changing the current density and the coating time.
  • Table 3 shows the condition of pre-coating, heat treatment, and hot dip galvanizing, along with the evaluation on corrosion resistance for the obtained coated steel sheets.
  • Example 1 was conducted using small test pieces in a laboratory coating simulator. The test pieces No. 1 through 12, 16 through 18, and 21 through 39 in Table 3 were the examples of the present invention.
  • test pieces No. 13 through 15, 19, 20, and 40 through 46 were the comparative examples differ from the scope of the present invention.
  • Test pieces No. 13 and 45 were the case where no Ni-P alloy coating was applied.
  • Test pieces No. 14, 15, 40, and 41 were the case where the pre-coating weight was outside of the range of the present invention.
  • the test pieces No. 19, 20, 43, and 44 were the case where the P content was outside of the range of this invention.
  • the test piece No. 46 was the case of Zn-Ni alloy coating.
  • the condition of hot dip galvanizing was the following.
  • Table 3 shows that the present invention effectively produces a zinc coated steel sheet having a good corrosion resistance.
  • the addition of small amount of corrosion-resistance-improving component to the interface of coating layer and steel sheet surface significantly improves the corrosion resistance without excessively adding that kind of additive to the whole body of steel sheet.
  • the mode of the present invention offers a considerable advantage to the steel sheet production cost, and the mode also provides a better corrosion-resistant steel sheet than conventional corrosion-resistant steel sheet (high Cr, and Mo addition) coated with Zn layer, which is proved by the test pieces No. 45 and 46.
  • the presumable cause of latter advantage is that the interface diffusion layer formed by the "pre-coating" is superior to the coating of conventional methods in terms of forming a stable and dense rust during the initial stage of corrosion process.
  • the mode of the present invention provided better workability of coating layer than conventional methods.
  • the reason of the good workability of coating layer is presumably the effect of Ni by the method of the present invention to enhance the uniform reaction between the steel and zinc to form an alloy layer having a good adhesiveness.
  • the present invention it is possible to reduce the coating weight of zinc coating or alloyed zinc coating while maintaining the corrosion resistance.
  • the advantage further improves the workability of coating layer and the weldability (for example, anti-blow hole characteristic in arc welding). From a long term point of view, the reduction of zinc amount in scrap offers an effective recycling of resources.
  • the present invention provides a method for effectively producing zinc coated steel sheet having a good corrosion resistance without applying large amount of corrosion-resistance-improving component to the steel sheet and offers a considerable merit to the production cost of steel sheets.
  • the present invention reduces the coating weight of zinc coating layer or alloyed zinc coating layer, and the reduction of zinc amount in scrap is effective also in the recycling of resources.
  • the present invention improves the workability and weldability (for example, anti-blow hole characteristic in arc welding) of coating layer.
  • a Ni-P alloy coating layer containing P of 8 to 15wt.% is formed on a cold-rolled steel sheet.
  • the Ni-P alloy coating containing P of 8 to 15wt.% shows an amorphous-like structure.
  • a steel sheet having that type of coating layer is subjected to heat treatment, a uniformly diffused alloy layer which is more uniform than general crystalline coating film is formed within a short period. Since the diffusion layer contains P, the iron corrosion products formed after the initiation of corrosion at the base plate iron gives an extremely dense structure. As a result, a corrosion resistance which could not be obtained by conventional technology is attained.
  • the P content of less than 8wt.% gives a crystalline Ni-P alloy coating layer and results in a non-uniform distribution of P.
  • an excellent corrosion resistance can not be obtained because the composition of diffused alloy layer formed in a heat treatment is not uniform and because the contribution to the densification of the rust generated in the base steel plate is not sufficient.
  • Addition of above 15wt.% P induces a brittle Ni-P alloy coating and results in a poor adhesiveness of the coating layer. Consequently, an excessive addition of P tends to separate the coating layer during heat treatment and other processing. Therefore, the present invention specifies the content of P in the coating layer of the steel sheet in a range of 8 to 15wt.%. More preferable P content is in a range of 10 to 13wt.%.
  • a steel sheet may be coated with a Ni-P alloy coating layer which is a composite of Ni-P combined with at least one element selected from the group of W, Mo, and Cu in an amount of 15wt.% or less after the cold-rolling stage.
  • W, Mo, and Cu they play a role of inhibitor against the corrosion of steel and they also provide an effect to further improve the denseness and stability of the rust generated in the initial stage of corrosion process owing to the synergistic effect with Ni and P.
  • Preferable content of W, Mo, and Cu is the sum of them at 15wt.% or less. Increase of the content of W, Mo, and Cu improves the corrosion resistance.
  • the present invention specifies the content of the sum of W, Mo, and Cu as 15wt.% as the total amount of these elements.
  • a preferable lower limit of content to perform the effect of W, Mo, and Cu is 0.5wt.%.
  • the range of coating weight of the Ni-P alloy coating layer is not specified, but a preferred range is from 0.1 to 8 g/m 2 . If the coating weight is too small, the effect for improving the corrosion resistance is not sufficient. If the coating weight is excessive, the performance improvement can not correspond to the cost increase, which is not efficient for practical point of view. Furthermore, the latter case needs to slow the line speed to increase the coating weight, which degrades the production efficiency.
  • Ni-P alloy coating layer There are several proposed methods for forming Ni-P alloy coating layer. However, electroplating or electroless coating (chemical coating) is preferable from the stand point of simple operation and uniformity of obtained film quality.
  • a steel sheet coated with Ni-P coating layer is a cold-rolled material, and the usefulness of the present invention is effectively achieved when a very low carbon steel having especially good mechanical characteristics is employed.
  • the very low carbon steel has the C content of solid solution as low as several tens of ppm (normally in a range of from 30 to 50ppm) and has very high purity of the steel sheet, so the corrosion resistance of that type of steel tends to be inferior to ordinary low carbon steels. Nevertheless, the method of the present invention compensates the disadvantage of base steel and provides a steel sheet having both the good mechanical characteristics and the high corrosion resistance.
  • the steel sheet coated with Ni-P alloy coating layer undergoes a heat treatment in a non-oxidizing atmosphere to form a diffused alloy layer consisting mainly of Fe-Ni-P at the interface between the base steel plate and the coating layer.
  • Preferable non-oxidizing atmosphere is argon atmosphere, nitrogen atmosphere, or a reducing atmosphere containing a specified amount of hydrogen gas and balance of inert gas.
  • the heat treatment for diffusion may be carried out in an ordinary annealing facility after cold rolling. At that heat treatment, a normal annealing may be conducted to perform the heat treatment at a time.
  • a preferred maximum temperature of the heat treatment is of 500 to 850°C.
  • the heat treatment at below 500°C can not form a sufficient diffusion layer between the Ni-P alloy coating layer and the steel sheet surface, and the insufficient dense rust formation during the corrosion process results in a small effect for improving corrosion resistance.
  • the heat treatment at above 850°C tends to induce a pickup of coating metal to the surface of rolls in the heat treatment furnace, which may cause the surface flaw on the steel sheets.
  • a preferred range of holding time at the maximum temperature of the steel sheet is 1 to 120 sec., though the holding time depends on the temperature. Too short holding time does not give the improving effect of corrosion resistance because sufficient diffusion layer can not be formed. An excessive holding time induces an excessive diffusion alloying, which results in a brittle interface layer to degrade the adhesiveness and workability of the coating layer.
  • an overaging may be applied for several minutes at an approximate temperature range of from 300 to 400°C.
  • a preferable depth of appropriate diffusion layer formed by the heat treatment is in a range of from 0.1 to 20 ⁇ m.
  • an effective mode is the Zn electroplating having Zn as the matrix and containing at least one metal or oxide selected from the group of Ni, Fe, Co, Cr, Mn, Ti, Mo, Si, and Al in a form of alloy or of dispersed particles. That type of coating is inert for coating corrosion so that it contributes to the corrosion resistance during the coating corrosion process.
  • the synergistic effect of the components in the Zn matrix and the components existing in the diffusion layer, such as Ni, P, etc. gives an effect on the rust stabilization and densification in the base iron plate.
  • Cr in the coating film performs a synergistic effect with the components such as P in the diffusion treatment layer even after the disappearance of the coating, and the Zn-Cr coating is effective for stabilizing and densifying the rust in the base iron plate. Accordingly, the Zn-Cr coating gives particularly high corrosion resistance among the above discussed coatings.
  • a preferable zinc coating weight of zing electroplating is in a range of from 1 to 30 g/m 2 . Too small coating weight can not give a sufficient corrosion resistance, and excessive coating weight degrades the workability of coating layer and increases the production cost.
  • sulfuric acid bath and chloride bath may be employed for a zinc electroplating bath.
  • the coating films produced by these electroplating baths are Zn film, Zn-Ni film, Zn-Cr film, Zn-Fe film, Zn-Cr-Ni film, Zn-Cr-Mo film, etc.
  • a preferable content of alloy or dispersed particles existing in the zinc electroplating layer is 1wt.% or more as the total amount for the effective functioning of the effect, and 70wt.% or less because an excessive components other than Zn degrades the adhesiveness of the film.
  • a chromate treatment may be applied on the zinc electroplating layer, and further an organic composite resin coating may be applied.
  • the chromate film may contain organic compound such as acrylic resin, oxide colloid such as silica colloid and alumina colloid, acid such as molybdenum oxide, salt, or other corrosion-resistance-improving component.
  • the organic resin film which coats the chromate film may use epoxy resin as the base resin.
  • the organic resin film preferably further contains a rust preventive additive such as silica and chromate at an approximate range of from 10 to 60wt.%.
  • the cold-rolled steel sheets After coated with Ni-P layer, the cold-rolled steel sheets underwent heat treatment in a non-oxidizing atmosphere.
  • the Ni-P coating or the like is hereinafter referred to as "pre-coating".
  • the heat-treated steel sheets were subjected to preliminary treatment and coating to prepare test pieces. For comparison, test pieces which were treated by annealing and coating without applying Ni-P coating were also prepared.
  • Table 4 shows the thickness and composition of the cold-rolled steel sheets tested.
  • the steel sheets No. A and B in Table 1 are the low carbon steel of the Example of the present invention, and No. C is the very low carbon steel of the Example of the present invention.
  • the steel sheets No. D, E, and F are the high Cr steel, the high P steel, and the high Mo steel used in the Comparative Examples, respectively.
  • Table 5 shows the condition of pre-coating.
  • the composition of coating solution is expressed by the unit of gram per liter.
  • the conditions No. 1 through No. 10 are the pre-coating condition used in the Examples, and No. 11 through No. 20 are the pre-coating condition used in Comparative Examples. No. 8, 9, 10, and 15 are the condition of electroless coating.
  • the coating solution contained pH buffer agent such as boric acid and sodium citrate or stabilizer.
  • the Coating weight was adjusted by changing the current density and the coating time.
  • Table 6 shows the condition of zinc electroplating.
  • the coating solution contained a conductive assistant such as sodium sulfate, a pH buffer agent-such as sodium citrate, a brightening agent, and a deposition assistant, at need.
  • the coating weight was adjusted by changing the current density and the coating time.
  • Tables 7(A) through (C) show the evaluation of various types of performance. The method and the criterion of evaluation were the same as in Example 1.
  • Tables 8(A) and (B) show the evaluation of various types of performance in Comparative Examples.
  • the corrosion resistance of the products of the present invention is superior to the conventional corrosion-resistant steel sheets (high P, with addition of Cr and Mo) coated with Zn layer (Comparative Examples 22, 23, 24, and 25). Also for the kinds and compositions of pre-coating, the product of the present invention is better than those of Comparative Examples 6 through 18. The reason of the superiority is presumably the excellent performance of the interface diffusion layer formed by the "pre-coating" in terms of formation of a stable and dense rust during initial stage of corrosion process compared with the conventional processes.
  • the present invention effectively produces a zinc coated steel sheet having a good corrosion resistance with less coating weight.
  • the present invention significantly improves the corrosion resistance by adding a small amount of corrosion-resistance-improving component to the interface between the coating layer and the steel sheet surface without adding a large amount of that type of component to the whole body of the steel sheet.
  • the method offers a considerable merit to the production cost of the steel sheet, and the resulted corrosion resistance is better than that of conventional corrosion-resistant steel sheets (high P, with addition of Cr and Mo) coated with Zn layer.
  • the corrosion resistance of the obtained steel sheets by the method of the present invention is better than the conventional steels.
  • Table 4 (wt.%) Plate thickness C Si Mn P S Al Cu Cr Mo Ti A 0.08mm 0.06 0.02 0.5 0.03 0.002 0.03 - - - - B 0.08mm 0.05 0.04 1.2 0.05 0.002 0.05 - - - C 0.08mm 0.002 0.01 0.2 0.08 0.003 0.06 - - - 0.11 D 0.08mm 0.02 0.01 0.2 0.03 0.012 0.04 0.03 0.8 - - E 0.08mm 0.01 0.01 0.2 0.1 0.012 0.04 0.1 - - - F 0.08mm 0.05 0.01 0.3 0.02 0.012 0.04 0.01 1.0 0.3 -
  • the steel sheets used in the present invention are hot-rolled steel sheets and the like including steel strips, and have their approximate thickness of 1.6 to 4.5mm.
  • the usefulness of the present invention effectively appears by employing a very low carbon steel sheet having good mechanical characteristics.
  • a very low carbon steel shows a very low content of solid solution C at a level of several tens of ppm and has a very high purity, so the corrosion resistance of that type of steel tends to be inferior to ordinary low carbon steels.
  • the method of the present invention compensates the disadvantage of base plate and provides a steel sheet having both the good mechanical characteristics and the high corrosion resistance.
  • a Ni-P alloy coating layer containing P of 8 to 15wt.% is formed on a cold-rolled steel sheet. This is called the "pre-coating layer".
  • the Ni-P alloy coating containing P 8 to 15wt.% shows an amorphous-like structure.
  • a uniform diffused alloy layer which is more uniform than general crystalline coating film is formed within a short period.
  • the P content less than 8wt.% gives a crystalline Ni-P alloy coating layer and results in a non-uniform distribution of P.
  • the content of P in the coating layer formed on the steel sheet of the present invention is specified in a range of from 8 to 15wt.%. More preferable P content is in a range of from 10 to 13wt.%.
  • a steel sheet may be coated with a Ni-P alloy coating layer which is a composite of Ni-P combined with at least one element selected from the group of W, Mo, Cr, and Cu in an amount of 15wt.% or less after the pickling stage.
  • W, Mo, Cr, and Cu they play a role of inhibitor against the corrosion of steel and they also provide an effect to further improve the denseness and stability of the rust generated in the initial stage of corrosion process owing to the synergistic effect with Ni and P.
  • Preferable content of W, Mo, Cr, and Cu is the sum of them at 15wt.% or less. Increase of the content of W, Mo, Cr, and Cu improves the corrosion resistance.
  • a preferable content of the sum of W, Mo, Cr, and Cu is specified as 15wt.% or less as the total amount of these elements.
  • a preferable lower limit of content to perform the effect of W, Mo, Cr, and Cu is 0.5wt.%.
  • the range of coating weight of the Ni-P alloy coating layer is not specified, but a preferred range is from 0.5 to 8 g/m 2 . If the coating weight is too small, the effect for improving the corrosion resistance is not sufficient, and if the coating weight is excessive, the performance improvement can not correspond to the cost increase, which is not efficient for practical point of view.
  • the coating can be applied at the exit of the pickling stage following the pickling treatment. This treatment allows to form effectively a pre-coating film having a good adhesiveness without giving a further cleaning stage to the hot-rolled steel sheet which was pickled and activated.
  • the steel sheet coated with Ni-P alloy layer undergoes cold rolling.
  • the cold rolling condition such as reduction ratio is not specifically defined.
  • the reason why the pre-coating is given before the cold rolling is that the treatment line-up has advantages that cleaning before the pre-coating and the pickling as the activation before coating are not required.
  • the hot-rolled steel sheet is subjected to heat treatment in a non-oxidizing atmosphere to form a diffused alloy layer consisting mainly of Fe-Ni-P at the interface between the base steel sheet surface and the coating layer.
  • the heat treatment for diffusion may be performed in an ordinary annealing facility following the cold-rolling process. At that treatment, a normal softening annealing may be applied to conduct the heat treatment at a time.
  • a preferable maximum temperature of the steel sheet during the heat treatment is from 500°C to 850°C. The temperature below 500°C does not form a sufficient diffused layer between the "pre-coating layer" and the steel sheet surface, and gives less effect for improving the corrosion resistance because a stable initial stage rust can not be formed during the corrosion process.
  • the holding time at the maximum sheet temperature is preferably in a range of from 1 to 120 sec., though it depends on the temperature level.
  • the holding time of less than 1 sec. hardly forms the sufficient diffused layer, and results in an insufficient improvement of corrosion resistance.
  • the holding time above 120 sec. tends to induce a brittle interface layer caused by an excessive diffusion alloying phenomenon, which may degrade the adhesiveness and workability of the coating layer.
  • An overaging at an approximate temperature of 300 to 400°C for several minutes may be applied during the heat treatment.
  • the preferred depth of the diffused layer formed by the heat treatment is in a range of from 0.1 to 20 ⁇ m.
  • Ni-P alloy coating layer undergoes heat treatment
  • two types of coating structure appear. The one is that a part of the Ni-P alloy coating layer forms a diffused alloy layer and forms the steel sheet / diffused alloy layer / Ni-P alloy coating layer structure.
  • the other is that all the Ni-P alloy coating layer forms a diffused alloy layer to give the steel sheet / diffused alloy layer structure.
  • the present invention includes both cases. According to the present invention, a temper rolling is conducted after the heat treatment for diffusion under an appropriate condition, at need.
  • the steel sheet undergone such a treatment is subjected to an electroplating in the electroplating line.
  • An effective mode of the electroplating is the Zn electroplating having Zn as the matrix and containing at least one metal or oxide selected from the group of Ni, Fe, Co, Cr, Mn, Ti, Mo, Si, and Al in a form of alloy or of dispersed particles. That type of coating is inert for coating corrosion so that it contributes to the corrosion resistance during the coating corrosion process.
  • the synergistic effect of the components in the Zn matrix and the components existing in the diffusion layer, such as Ni, P, etc. gives an effect on the rust stabilization and densification of the rust in the base iron plate.
  • the Zn-Cr coating gives particularly high corrosion resistance among the above discussed coatings.
  • a preferable zinc coating weight of zinc electroplating or zinc coating is in a range of from 10 to 50 g/m 2 . Too small coating weight can not give a sufficient corrosion resistance, and excessive coating weight degrades the workability of coating layer and increases the production cost.
  • a zinc electroplating bath widely used sulfuric acid bath and chloride bath may be employed.
  • a chromate treatment may be applied on the zinc electroplating layer, and further an organic composite resin coating may be applied.
  • the chromate treatment either one of reaction type, electrolysis type, and application type is applicable.
  • the chromate film may contain organic compound such as acrylic resin, oxide colloid such as silica colloid and alumina colloid, acid such as molybdenum oxide, salt, or other anti-rusting improve agent.
  • organic resin film which coats the chromate film may use epoxy resin as the base resin.
  • the organic resin film preferably further contains a rust preventive additive such as silica and chromate at an approximate range of from 10 to 60wt.%.
  • the zinc electroplating steel sheet prepared by the procedure described above has the diffused alloy layer consisting mainly of Fe-Ni-P formed by the mutual diffusion of the pre-coating layer of the surface of base steel sheet and the base steel sheet, and has the zinc coating or the zinc electroplating layer above the pre-coating layer.
  • the zinc electroplating steel sheet of the present invention has an extremely high corrosion resistance compared with the zinc coated steel sheets obtained by conventional processes. The superiority presumably comes from the contribution of the diffused alloy layer consisting mainly of Fe-Ni-P existing at the interface between the zinc coating layer and the base steel sheet, as well as the high corrosion resistance of the zinc coating layer.
  • the inventors assume a process where, during the progress of corrosion of the coated film to corrode the base steel sheet, the intermediate diffused alloy layer forms a uniform and dense Fe rust, which rust then suppresses the cathode reaction in the corrosion process.
  • the case of forming a zinc coating layer gives a better corrosion resistance than conventional products, though it gives somewhat lower corrosion resistance compared with the case of forming a zinc electroplating layer which is described above.
  • the zinc coating is relatively active, it is effective for the cases where a high corrosion resistance is requested under a condition which needs a sacrifice corrosion protection: for example, the steel sheet exposes by a defected painting or at an edge thereof.
  • the highly active property of that type of product initiates the corrosion of the diffusion-treated layer on the base steel sheet compared with the zinc coating described above.
  • the components such as Ni and P existing in the diffusion-treated layer contribute to the stabilization of Fe rust, so the progress of the corrosion reaches a saturation level.
  • the application of zinc coating provides a steel sheet having high corrosion resistance over the whole corrosion process because the zinc coating layer plays an effective role during the initial stage of corrosion and the diffusion-treated layer plays an effective role during the latter half period of the corrosion process.
  • Hot-rolled steel sheets underwent pre-coating treatment to form Ni-P alloy coating layer.
  • the hot-rolled steel sheets coated with the Ni-P alloy layer were subjected to cold rolling at a reduction ratio of 75%.
  • the cold-rolled steel sheets were subjected to heat treatment in a non-oxidizing atmosphere to form a diffused alloy layer consisting mainly of Fe-Ni-P at the interface between the base steel sheet and the coating layer.
  • the steel sheets were then treated by ordinary preliminary treatment before coating, followed by the zinc electroplating to form the zinc electroplating layer.
  • the test pieces of the present invention were prepared.
  • the test pieces were prepared in a similar procedure of cold rolling, annealing, and coating except for pre-coating. Those test pieces were evaluated by the same method employed in Example 1.
  • Table 9 shows the thickness and composition of the hot-rolled steel sheets tested.
  • the materials No. A and B of Table 9 are the low carbon steel of the Example of the present invention
  • the material No. C is the very low carbon steel of the Example of the present invention
  • the materials No. D, E, and F are the high Cr steel, the high P steel, and the high Mo steel of the Comparative Examples.
  • Table 10 shows the condition of pre-coating.
  • the composition of the coating solution is expressed by the unit of gram per liter.
  • the conditions No. 1 through 10 are the pre-coating condition for the Examples of the present invention, and the conditions No. 11 through 16 are the pre-coating condition for the Comparative Examples.
  • the conditions No. 8, 9, 10, and 15 are for the electroless coating.
  • the coating solution contained a pH buffer agent such as boric acid and sodium citrate or a stabilizer. The coating weight was adjusted by changing the current density and the coating time.
  • Table 11 lists the condition of zinc electroplating.
  • the coating solution contained a conductive assistant such as sodium sulfate, a pH buffer agent such as sodium citrate, a brightening agent, and a deposition assistant, at need.
  • the coating weight was adjusted by changing the current density and the coating time.
  • Table 12 (A) to (E) show the evaluation of each kind of performance based on the same criterion applied in Example 1.
  • Table 13 shows the evaluation of each kind of performance in Comparative Examples.
  • a zinc coated steel sheet having a good corrosion resistance with less coating weight is effectively produced.
  • the method of the present invention significantly improves the corrosion resistance by adding a small amount of corrosion-resistance-improving component to the interface between the coating layer and the steel sheet without adding a large amount of that type of component to the whole area of the steel sheet.
  • the method gives a substantial merit to the production cost of the steel sheets.
  • these Examples show that the steel sheets prepared by the method of the present invention has better corrosion resistance than the conventional anti-corrosive steel sheets (high P, with addition of Cr and Mo) coated with Zn layer (Comparative Examples 13, 14, 15, and 16).
  • the presumable cause of the advantage is that the interface diffusion layer formed by the "pre-coating," Ni-P alloy coating, is superior to the coating of conventional methods in terms of forming a stable and dense rust during the initial stage of corrosion process.
  • the mode of the present invention provided better workability of coating layer than conventional methods.
  • the reason of the good workability of coating layer is presumably the effect of Ni to enhance the uniform reaction between copper and zinc to form an alloy layer having a good adhesiveness.
  • the diffused alloy layer appeared at the interface between the zinc coating layer and the base steel sheet forms a uniform and dense Fe rust.
  • the steel sheet of the present invention provides a high corrosion resistance with less coating weight without limitation of the component content in the base steel sheet even under a severe environmental condition which an automobile rust preventive steel sheet encounters.

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Claims (61)

  1. Verfahren zur Herstellung eines zinkbeschichteten Stahlblechs, umfassend die Schritte aus:
    a) Herstellen eines warmgewalzten Stahlblechs;
    b) Bilden einer Ni-P-Legierungsüberzugsschicht, die P in einer Menge von 8 bis 15 Gew.-% enthält und die gegebenenfalls zusätzlich wenigstens ein Element, ausgewählt aus W, Mo, Cr und Cu, in einer Gesamtmenge von bis zu 15 Gew.-% enthält, mit einem Überzugsgewicht von 0,1 bis 8 g/m2 auf wenigstens einer Oberfläche des warmgewalzten Stahlblechs;
    c) Vergüten des mit der Legierungsüberzusschicht beschichteten warmgewalzten Stahlblechs in einer nicht-oxidierenen Atmosphäre bei einer maximalen Temperatur von 500 bis 850°C und einer Haltezeit von 1 bis 120 s, um eine diffundierte Fe-Ni-P-Legierungsschicht an der Grenzfläche des Stahlblechs und der Legierungsüberzugsschicht zu bilden; und
    d) Versehen der diffundierten Legierungsschicht mit einem Zink- oder Zinklegierungsüberzug mit einem Überzugsgewicht von 20 bis 120 g/m2 durch Feuerverzinkung des mit der diffundierten Legierungsschicht beschichteten Stahlblechs.
  2. Verfahren gemäß Anspruch 1, worin die Ni-P-Legierungsüberzugsschicht 10 bis 13 Gew.-% P enthält.
  3. Verfahren gemäß Anspruch 1, worin der Schritt der Bildung der Legierungsüberzugsschicht die Bildung einer Ni-P-Legierungsüberzugsschicht umfaßt, welche 8 bis 15 Gew.-% P und wenigstens ein Element, ausgewählt aus W, Mo, Cr und Cu, in einer Menge von 15 Gew.-% enthält.
  4. Verfahren gemäß Anspruch 3, worin die Legierungsüberzugsschicht Ni, P und Cr enthält.
  5. Verfahren gemäß Anspruch 3, worin die Legierungsüberzugsschicht Ni, P und Mo enthält.
  6. Verfahren gemäß Anspruch 3, worin die Legierungsüberzugsschicht Ni, P, Cr und Mo enthält.
  7. Verfahren gemäß Ansprüchen 3 bis 6, worin die Legierungsüberzugsschicht Ni, P und W enthält.
  8. Verfahren gemäß Ansprüchen 3 bis 7, worin die Legierungsüberzugsschicht Ni, P und Cu enthält.
  9. Verfahren gemäß einem der Ansprüche 1 bis 8, worin die Ni-P-Legierungsüberzugsschicht ein Überzugsgewicht von 0,5 bis 8 g/m2 hat.
  10. Verfahren gemäß einem der Ansprüche 1 bis 9, worin die Ni-P-Legierungsüberzugsschicht durch Galvanisieren gebildet wird.
  11. Verfahren gemäß einem der Ansprüche 1 bis 9, worin die Ni-P-Legierungsüberzugsschicht durch stromloses Überziehen gebildet wird.
  12. Verfahren gemäß einem der vorhergehenden Ansprüche, worin die Vergütung bei einer maximalen Temperatur von 500 bis 800°C und einer Haltezeit von 1 bis 30 s durchgeführt wird.
  13. Verfahren gemäß einem der vorhergehenden Ansprüche, worin die diffundierte Legierungsschicht eine Tiefe von 0,1 bis 20 µm hat.
  14. Verfahren gemäß einem der vorhergehenden Ansprüche, worin die feuerverzinkte Überzugsschicht ein Überzugsgewicht von 20 bis 120 g/m2 hat.
  15. Verfahren gemäß einem der vorhergehenden Ansprüche, welches zusätzlich den Schritt des Erwärmens des mit der feuerverzinkten Schicht beschichteten Stahlblechs zum Legieren der Überzugsschicht umfaßt.
  16. Verfahren zur Herstellung eines zinkbeschichteten Stahlblechs, umfassend die Schritte aus:
    a) Herstellen eines kaltgewalzten Stahlblechs;
    b) Bilden einer Ni-P-Legierungsüberzugsschicht, die P in einer Menge von 8 bis 15 Gew.-% enthält und die gegebenenfalls zusätzlich wenigstens ein Element, ausgewählt aus W, Mo und Cu, in einer Gesamtmenge von bis zu 15 Gew.-% enthält, mit einem Überzugsgewicht von 0,1 bis 8 g/m2 auf wenigstens einer Oberfläche des kaltgewalzten Stahlblechs;
    c) Vergüten des mit der Legierungsüberzugsschicht beschichteten kaltgewalzten Stahlblechs in einer nicht-oxidierenden Atmosphäre bei einer maximalen Temperatur von 500 bis 850°C und einer Haltezeit von 1 bis 120 s, um eine diffundierte Fe-Ni-P-Legierungsschicht an der Grenzfläche des kaltgewalzten Stahlblechs und der Legierungsüberzugsschicht zu bilden; und
    d) Versehen der diffundierten Legierungsschicht mit einem Zink- oder Zinklegierungsüberzug mit einem Überzugsgewicht von 1 bis 30 g/m2 durch galvanisches Verzinken des mit der diffundierten Legierungsschicht beschichteten Stahlblechs.
  17. Verfahren gemäß Anspruch 16, worin der Schritt der Bildung der Legierungsüberzugsschicht die Bildung einer Ni-P-Legierungsüberzugsschicht umfaßt, welche 8 bis 15 Gew.-% und wenigstens ein Element, ausgewählt aus W, Mo und Cu, in einer Menge von bis zu 15 Gew.-% enthält.
  18. Verfahren gemäß Anspruch 17, worin die Legierungsüberzugsschicht Ni, P und Cu enthält.
  19. Verfahren gemäß Ansprüchen 17 oder 18, worin die Legierungsüberzugsschicht Ni, P und Mo enthält.
  20. Verfahren gemäß Ansprüchen 17, 18 oder 19, worin die Legierungsüberzugsschicht Ni, P und W enthält.
  21. Verfahren gemäß einem der Ansprüche 16 bis 20, worin die galvanische Zinküberzugsschicht Zn als Matrix hat und wenigstens ein Metall, ausgewählt aus Ni, Fe, Co, Cr, Mn, Ti, Mo, Si und Al, in Form einer Legierung enthält.
  22. Verfahren gemäß Anspruch 21, worin die galvanische Zinküberzugsschicht Zn und Ni enthält.
  23. Verfahren gemäß Ansprüchen 21 oder 22, worin die galvanische Zinküberzugsschicht Zn und Fe enthält.
  24. Verfahren gemäß Ansprüchen 21, 22 oder 23, worin die galvanische Zinküberzugsschicht Zn und Cr enthält.
  25. Verfahren gemäß Ansprüchen 21, 22, 23 oder 24, worin die galvanische Zinküberzugsschicht Zn und Mn enthält.
  26. Verfahren gemäß Anspruch 16, worin die galvanische Zinküberzugsschicht Zn als Matrix hat und wenigstens ein Oxid der Elemente, ausgewählt aus Ni, Fe, Co, Cr, Mn, Ti, Mo, Si und Al, in Form von dispergierten Partikeln enthält.
  27. Verfahren gemäß Anspruch 26, worin die galvanische Zinküberzugsschicht Zn und Cr-oxid enthält.
  28. Verfahren gemäß Ansprüchen 26 oder 27, worin die galvanische Zinküberzugsschicht Zn und Si-oxid enthält.
  29. Verfahren gemäß Ansprüchen 26, 27 oder 28, worin die galvanische Zinküberzugsschicht Zn und Ti-oxid enthält.
  30. Verfahren gemäß einem der Ansprüche 16 bis 29, worin die Ni-P-Legierungsüberzugsschicht 10 bis 13 Gew.-% P enthält.
  31. Verfahren gemäß einem der Ansprüche 16 bis 30, worin die Ni-P-Legierungsüberzugsschicht ein Überzugsgewicht von 0,1 bis 8 g/m2 hat.
  32. Verfahren gemäß einem der Ansprüche 16 bis 31, worin die Ni-P-Legierungsüberzugsschicht durch Galvanisieren gebildet wird.
  33. Verfahren gemäß einem der Ansprüche 16 bis 31, worin die Ni-P-Legierungsüberzugsschicht durch stromloses Überziehen gebildet wird.
  34. Verfahren gemäß einem der Ansprüche 16 bis 33, worin die Vergütung bei einer maximalen Temperatur von 500 bis 800°C und einer Haltezeit von 1 bis 120 s durchgeführt wird.
  35. Verfahren gemäß einem der Ansprüche 16 bis 34, worin die diffundierte Legierungsschicht eine Tiefe von 0,1 bis 20 µm hat.
  36. Verfahren gemäß einem der Ansprüche 16 bis 35, worin die galvanische Zinküberzugsschicht ein Überzugsgewicht von 1 bis 30 g/m2 hat.
  37. Verfahren zur Herstellung eines zinkbeschichteten Stahlblechs, umfassend die Schritte aus:
    a) Herstellen eines warmgewalzten Stahlblechs;
    b) Bilden einer Ni-P-Legierungsüberzugsschicht, die P in einer Menge von 8 bis 15 Gew.-% enthält und die gegebenenfalls zusätzlich wenigstens ein Element, ausgewählt W, Mo, Cr und Cu, in einer Gesamtmenge von bis zu 15 Gew.-% enthält, mit einem Überzugsgewicht von 0,1 bis 8 g/m2 auf wenigstens einer Oberfläche des warmgewalzten Stahlblechs;
    c) Kaltwalzen des mit der Legierungsüberzugsschicht beschichteten kaltgewalzten Stahlblechs;
    d) Vergüten des kaltgewalzten Stahlblechs in einer nicht-oxidierenden Atmosphäre bei einer maximalen Temperatur von 500 bis 850°C und einer Haltezeit von 1 bis 120 s, um eine diffundierte Fe-Ni-P-Legierungsschicht an der Grenzfläche des warmgewalzten Stahlblechs und der Legierungsüberzugsschicht zu bilden; und
    e) Versehen der diffundierten Legierungsschicht mit einem Zink- oder Zinklegierungsüberzug mit einem Überzugsgewicht von 10 bis 50 g/m2 durch galvanisches Verzinken des mit der diffundierten Legierungsschicht beschichteten kaltgewalzten Stahlblechs.
  38. Verfahren gemäß Anspruch 37, worin die Ni-P-Legierungsüberzugsschicht 10 bis 13 Gew.-% P enthält.
  39. Verfahren gemäß Anspruch 37, worin der Schritt der Bildung der Legierungsüberzugsschicht die Bildung einer Ni-P-Legierungsüberzugsschicht umfaßt, welche 8 bis 15 Gew.-% P und wenigstens ein Element, ausgewählt aus W, Mo, Cr und Cu, in einer Menge von 15 Gew.-% oder weniger enthält.
  40. Verfahren gemäß Anspruch 39, worin die Legierungsüberzugsschicht Ni, P und Cr enthält.
  41. Verfahren gemäß Ansprüchen 39 oder 40, worin die Legierungsüberzugsschicht Ni, P und Mo enthält.
  42. Verfahren gemäß Anspruch 39, worin die Legierungsüberzugsschicht Ni, P, Cr und Mo enthält.
  43. Verfahren gemäß Ansprüchen 39 bis 42, worin die Legierungsüberzugsschicht Ni, P und W enthält.
  44. Verfahren gemäß Ansprüchen 39 bis 43, worin die Legierungsüberzugsschicht Ni, P und Cu enthält.
  45. Verfahren gemäß einem der Ansprüche 37 bis 44, worin die Ni-P-Legierungsüberzugsschicht ein Überzugsgewicht von 0,5 bis 8 g/m2 hat.
  46. Verfahren gemäß einem der Ansprüche 37 bis 45, worin die Ni-P-Legierungsüberzugsschicht durch Galvanisieren gebildet wird.
  47. Verfahren gemäß einem der Ansprüche 37 bis 45, worin die Ni-P-Legierungsüberzugsschicht durch stromloses Überziehen gebildet wird.
  48. Verfahren gemäß einem der Ansprüche 37 bis 47, worin die Vergütung bei einer maximalen Temperatur von 500 bis 850°C und einer Haltezeit von 1 bis 120 s durchgeführt wird.
  49. Verfahren gemäß einem der Ansprüche 37 bis 48, worin die diffundierte Legierungsschicht eine Tiefe von 0,1 bis 20 µm hat.
  50. Verfahren gemäß einem der Ansprüche 37 bis 49, worin die Zinküberzugsschicht eine galvanische Zinküberzugsschicht ist und die Zinküberzugsschicht Zn als Matrix hat und wenigstens ein Metall, ausgewählt aus Ni, Fe, Co, Cr, Mn, Ti, Mo, Si und Al, in Form einer Legierung enthält.
  51. Verfahren gemäß Anspruch 50, worin die galvanische Zinküberzugsschicht Zn und Ni enthält.
  52. Verfahren gemäß Ansprüchen 50 oder 51, worin die galvanische Zinküberzugsschicht Zn und Fe enthält.
  53. Verfahren gemäß Ansprüchen 50 bis 52, worin die galvanische Zinküberzugsschicht Zn und Cr enthält.
  54. Verfahren gemäß Ansprüchen 50 bis 53, worin die galvanische Zinküberzugsschicht Zn und Mn enthält.
  55. Verfahren gemäß Anspruch 37, worin die Zinküberzugsschicht eine galvanische Zinküberzugsschicht ist und die Zinküberzugsschicht Zn als Matrix hat und wenigstens ein Oxid des Elements, ausgewählt aus Ni, Fe, Co, Cr, Mn, Ti, Mo, Si und Al, in Form von dispergierten Partikeln enthält.
  56. Verfahren gemäß Anspruch 55, worin die galvanische Zinküberzugsschicht Zn und Cr-oxid enthält.
  57. Verfahren gemäß Ansprüchen 55 oder 56, worin die galvanische Zinküberzugsschicht Zn und Si-oxid enthält.
  58. Verfahren gemäß Ansprüchen 55 bis 57, worin die galvanische Zinküberzugsschicht Zn und Ti-oxid enthält.
  59. Verfahren gemäß einem der Ansprüche 37 bis 58, worin die Zinküberzugsschicht ein Überzugsgewicht von 10 bis 50 g/m2 hat.
  60. Zink-beschichtetes Stahlblech, herstellbar durch ein Verfahren gemäß einem der Ansprüche 1 bis 59.
  61. Verwendung eines Zink-beschichteten Stahlblechs gemäß Anspruch 60 in der Herstellung von Kraftfahrzeugen.
EP94109981A 1993-06-29 1994-06-28 Verfahren zum Herstellen eines verzinkten Bleches Expired - Lifetime EP0632140B1 (de)

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Application Number Priority Date Filing Date Title
JP158503/93 1993-06-29
JP5158503A JPH0711409A (ja) 1993-06-29 1993-06-29 亜鉛めっき鋼板の製造方法
JP5218565A JPH0770788A (ja) 1993-06-29 1993-09-02 防錆鋼板の製造方法
JP218565/93 1993-09-02
JP311937/93 1993-12-13
JP5311937A JPH0770763A (ja) 1993-06-29 1993-12-13 防錆鋼板の製造方法

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US6756134B2 (en) * 2002-09-23 2004-06-29 United Technologies Corporation Zinc-diffused alloy coating for corrosion/heat protection
US7413769B2 (en) * 2005-07-01 2008-08-19 Mcdevitt Erin T Process for applying a metallic coating, an intermediate coated product, and a finish coated product
EP3241929A1 (de) * 2016-05-04 2017-11-08 Haas Food Equipment GmbH Beschichtung von funktionsteilen aus metall
KR102201135B1 (ko) * 2019-02-27 2021-01-12 주식회사 수영프리텍 내부식성 및 수명 향상을 위한 금속 체결구의 표면 도금방법
CN110318015B (zh) * 2019-08-16 2020-09-29 东北大学 一种在扁平钢材上获得彩色镀层的热镀锌方法

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FR2554831B1 (fr) * 1983-11-15 1993-08-13 Thomson Csf Procede de depot d'un revetement protecteur sur des pieces metalliques
JPS61124580A (ja) * 1984-11-22 1986-06-12 Nippon Steel Corp 太陽熱吸収板の製造法
JPS6396294A (ja) * 1986-10-13 1988-04-27 Nippon Steel Corp 溶接性、耐食性に優れた缶用鋼板の製造方法
JPS63312960A (ja) * 1987-06-17 1988-12-21 Nippon Steel Corp 加工性の良い溶融亜鉛合金めっき鋼板の製造法
JPH0651903B2 (ja) * 1990-01-30 1994-07-06 新日本製鐵株式会社 摺動抵抗の高い亜鉛又は亜鉛系合金溶融めっき鋼板の製造方法
JPH0713286B2 (ja) * 1990-04-25 1995-02-15 新日本製鐵株式会社 加工性に優れた溶融合金化亜鉛めっき鋼板

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KR950000915A (ko) 1995-01-03

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