METHOD FOR PRODUCING A STEEL STRIP WITH IMPROVED BONDING OF METALLIC HOT-DIP COATINGS

Abstract

A cold-rolled or hot-rolled steel strip having a metal coating, the steel strip having iron as the main constituent and, in addition to carbon, an Mn content of 4.1 to 8.0 wt. % and optionally one or more of the alloy elements Al, Si, Cr, B, Ti, V, Nb and/or Mo. The surface of the uncoated steel strip is cleaned, a layer of pure iron is applied to the cleaned surface, an oxygen-containing iron-based layer is applied to the layer of pure iron and contains more than five mass percent oxygen. The steel strip is then annealed and, to attain a surface consisting substantially of metallic iron, is subjected to a reduction treatment in a reducing furnace while being annealed. The steel strip is then coated with the metallic coating by hot dipping. Uniform and reproducible adhesion conditions are hereby achieved for the metallic coating on the steel strip surface.

Claims

1. Method for producing a cold-rolled or hot-rolled steel strip having a metallic coat, the steel strip comprises iron as a main constituent and, in addition to carbon, an Mn content of 4.1 to 8.0 wt. % and optionally one or more of the alloy elements Al, Si, Cr, B, Ti, V, Nb and/or Mo, wherein the surface of the uncoated steel strip is cleaned, a layer of pure iron with an average iron content of more than 96 wt. % is applied onto the cleaned surface, onto the layer of pure iron an oxygen-containing, iron-based layer is applied which contains more than 5 mass percent of oxygen, then the steel strip together with the oxygen-containing, iron-based layer is subjected to annealing treatment and is reduction-treated during the course of the annealing treatment in a reducing furnace atmosphere and the steel strip thus treated and subjected to annealing treatment is then hot-dip coated with the metallic coat.

2. Method as claimed in claim 1, characterised in that an average thickness of the pure iron layer is formed to be 0.05 to 0.5 μm and an average thickness of the oxygen-containing, iron-based layer is formed to be 0.1 to 0.6 μm.

3. Method as claimed in claim 2, characterised in that an average thickness of the pure iron layer is 0.1 to 0.4 μm and an average thickness of the oxygen-containing, iron-based layer is from 0.2 to 0.5 μm.

4. Method as claimed in at least one of claims 1 to 3, characterised in that the average thickness of the oxygen-containing, iron-based layer is greater than the average thickness of the pure iron layer.

5. Method as claimed in at least one of claims 1 to 4, characterised in that the oxygen-containing, iron-based layer with a proportion of oxygen of more than 5 to 40 wt. % is applied to the pure iron layer.

6. Method as claimed in claim 5, characterised in that the oxygen-containing, iron-based layer with a proportion of oxygen of more than 10 to 30 wt. %, advantageously more than 12 to 25 wt. %, is applied to the pure iron layer.

7. Method as claimed in at least one of claims 1 to 6, characterised in that the pure iron layer is deposited electrolytically or by deposition from the vapour phase and the oxygen-containing, iron-based layer is deposited electrolytically.

8. Method as claimed in at least one of claims 1 to 7, characterised in that the steel strip comprises the following composition in wt. %: C: 0.03% to 0.35%, Mn: 4.1% to 8.0%, Si: 0.008% to 2.5%, Al: 0.001% to 2.0%, optionally Cr: 0.01% to 0.7%, B: 0.001% to 0.08%, Ti: 0.005% to 0.3%, V: 0.005% to 0.3%, Nb: 0.005% to 0.2%, Mo: 0.005% to 0.7%, P:<_0.10%, S:<_0.010%, with the remainder being iron and unavoidable impurities.

9. Method as claimed in at least one of claims 1 to 8, characterised in that the annealing treatment is carried out in a radiant tube furnace as a continuous annealing furnace, at an annealing temperature of 550° C. to 880° C. and an average heating rate of 1 K/s to 100 K/s, with a reducing annealing atmosphere, consisting of 2 to 40% H.sub.2 and 98 to 60% N2 and a dew point in the annealing furnace between +15 and −70° C. and a holding time of the steel strip at an annealing temperature between 30 s and 650 s with optional subsequent cooling to a holding temperature between 200° C. and 600° C. for up to 500 s with subsequent optional inductive heating to a temperature above the melting bath temperature of the metallic coat at 400° C. to 750° C. and subsequently hot-dip coating of the steel strip with the metallic coat is carried out.

10. Method as claimed in at least one of claims 1 to 9, characterised in that the ratio of the partial pressures of steam and hydrogen during the annealing in the radiant tube furnace is in the range of 0.00077>pH.sub.2O/pH.sub.2>0.00021, advantageously 0.00254>pH.sub.2O/pH.sub.2>0.00021.

11. Method as claimed in at least one of claims 1 to 10, characterised in that the following are used as metallic coats: aluminium-silicon (AS, AlSi), zinc (Z), zinc-aluminium (ZA, galfan), zinc-iron (ZF, galvannealed), zinc-aluminium-magnesium (ZM, ZAM) or aluminium-zinc (AZ, galvalume).

12. Steel strip comprising, in addition to carbon, iron as a main constituent, an Mn content of 4.1 to 8.0 wt. % and optionally one or more of the alloy elements Al, Si, Cr, B, Ti, V, Nb and/or Mo with a metallic coat applied by means of hot-dipping, characterised in that, in the transition region between the metallic coat and the steel strip surface, a predominantly ferritic edge zone with more than 60 vol. % ferrite is formed, wherein the predominantly ferritic edge zone has a thickness of 0.15 to 1.1 gm and, as seen from the steel strip surface, consists of a pure iron layer with an average iron content of more than 96 wt. % and an oxygen-containing, iron-based layer containing more than 5 mass percent of oxygen thereon.

13. Steel strip as claimed in claim 12, characterised in that the predominantly ferritic edge zone has a thickness of between 0.3 and 0.9 μm.

14. Steel strip as claimed in at least one of claims 12 and 13, characterised by the following composition in wt. %: C: 0.03% to 0.35%, Mn: 4.1% to 8.0%, Si: 0.008% to 2.5%, Al: 0.001% to 2.0%, optionally Cr: 0.01% to 0.7%, B: 0.001% to 0.08%, Ti: 0.005% to 0.3%, V: 0.005% to 0.3%, Nb: 0.005% to 0.2%, Mo: 0.005% to 0.7%, P:<_0.10%, S:<_0.010%, with the remainder being iron and unavoidable impurities.

15. Steel strip as claimed in at least one of claims 12 to 14, characterised by a metallic coat consisting of aluminium-silicon (AS, AlSi), zinc (Z), zinc-aluminium (ZA), zinc-aluminium-iron (ZF/galvannealed), zinc-magnesium-aluminium (ZM, ZAM) or aluminium-zinc (AZ).

16. Steel strip as claimed in claim 15, characterised in that in the case of a metallic coat based on zinc, the zinc coat contains 0.1 to 1 wt. % Al.

17. Steel strip as claimed in claim 15, characterised in that in the case of a metallic coat based on zinc, the zinc coat contains 0.1 to 6 wt. % Al and 0.1 to 6 wt. % Mg.

18. Steel strip as claimed in claim 15, characterised in that in the case of a metallic coat based on zinc, the zinc coat contains 5 to 15 wt. % Fe.

19. Use of a steel strip produced according to at least one of claims 1 to 11 or of a steel strip according to at least one of claims 12 to 18 for the production of parts for motor vehicles.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0021] FIG. 1 shows a scanning electron microscopic image of the surface of a medium manganese steel before and after deposition of a pre-coating of pure iron and oxygen-containing, iron-based layer in accordance with an aspect of the invention; and

[0022] FIG. 2 shows the results of depth profile analysis by means of GDOES (glow discharge optical emission spectroscopy) on the medium manganese steel samples shown in FIG. 1 after annealing.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

[0023] The invention is embodied as a combination of a pure iron coating applied to the steel strip surface with an oxygen-containing iron coating deposited thereover with subsequent annealing and hot-dip finishing.

[0024] In terms of the present invention, a pure iron layer is understood to be a layer with an average iron content of more than 96 wt. %. The oxygen-containing, iron-based layer is understood to be a layer with an iron content in wt. % of at least 50%, which contains oxygen of more than 5 wt. % in the form of oxides and/or hydroxides.

[0025] The oxides and/or hydroxides can be present in the oxygen-containing, iron-based layer both in the form of crystalline, amorphous compounds and/or as mixtures of crystalline, e.g. magnetite (Fe.sub.3O.sub.4), and amorphous compounds. In addition, the oxygen-containing, iron-based layer is understood to be both a homogeneous stoichiometric iron-oxide layer e.g. a magnetite layer (Fe.sub.3O.sub.4), and also a metallic iron layer which contains oxidic and/or hydroxidic inclusions (dispersion layer). Therefore, the distribution of the amorphous and/or crystalline compounds is also not limited. Therefore the layer is characterised in that it contains oxygen-containing, reducible iron species.

[0026] In trials it has proved to be the case that without a pre-coating of pure iron, during the annealing treatment prior to the hot-dip coating, a solid deposition of oxides of the alloy elements takes place at the transition from the steel substrate to the oxygen-containing, iron-based layer, which weakens the whole system and can lead to adhesion failure. With the pre-coating of pure iron, the oxides of the alloy elements are deposited in a less locally concentrated manner and adhesion failure no longer occurs. The deposition of the pure iron layer can preferably take place electrolytically or by deposition from the vapour phase (e.g. by means of PVD or CVD).

[0027] In the case of the preferred electrolytic deposition of the pure iron layer, typically sulphatic or chloridic electrolytes and combinations thereof are used, the pH value of which is less than or equal to 5.5. In the case of higher pH values, iron(II) species precipitate as hydroxides. Iron with a purity in wt. % of greater than 99.5 is preferably used as the anode material. Electrolyte cells with separated anode and cathode chambers can also be used, whereby the use of oxygen-generating or insoluble anodes is rendered possible. In order to reduce the cell resistance a conductive salt can optionally be added to the electrolyte. The use of further additives, such as e.g. surfactants to improve wetting and/or defoaming is also possible.

[0028] The electrolytic deposition takes place at current densities which produce a deposition thickness which is homogeneous over the strip length irrespective of the respective strip speed. Furthermore, the current density is dependent upon the anode construction length in the running direction of the strip. Typical values are between 1 and 150 A/dm.sup.2 per strip side. Below 1 A/dm.sup.2 excessively long processing lengths are required and consequently the process cannot be operated economically. In the case of current densities above 150 A/dm.sup.2 a homogeneous deposition is rendered significantly more difficult owing to burning-on or dendrite formation. The duration of the electrolytic deposition is dependent on the processing length, the current density, the current yield and the desired layer contact and is typically between 1 s and 30 s per side. Exemplified compositions of aqueous electrolytes and deposition conditions are shown in Table 1.

TABLE-US-00001 TABLE 1 Electrolyte system Composition Conditions Sulphate FeSO.sub.4•7H.sub.2O: 220 g/l pH 2.2; 35° C. NaSO.sub.4: 90 g/l Chloride FeCl.sub.2•4H.sub.2O: 280 g/l pH 1.4; 48° C. KCl: 210 g/l Sulphate chloride FeSO.sub.4•7H.sub.2O: 400 g/l pH 1.6; 85° C. FeCl.sub.2•4H.sub.2O: 400 g/l CaCl.sub.2: 180 g/l Sulphamate Fe(SO.sub.3NH.sub.2).sub.2: 220 g/l pH 3.2; 60° C. NH.sub.4(SO.sub.3NH.sub.2): 30 g/l Fluoroborate Fe(BF.sub.4).sub.2: 240 g/l pH 2.1; 58° C. NaCl: 8 g/l

[0029] In one exemplified embodiment, the deposition of the pure iron layer takes place with an electrolyte temperature of 60° C. with a current density of 30 A/dm.sup.2 using an iron anode with a purity in wt. % of greater than 99.5 in an aqueous sulphuric acid electrolyte of the following composition: 60 g/l iron(II), 20 g/l sodium, pH 1.8.

[0030] The preferred deposition of the oxygen-containing, iron-based layer takes place electrolytically from an Fe(II)-containing and/or Fe(III)-containing electrolyte. For this purpose, sulphatic or chloridic electrolytes and combinations thereof are typically used, the pH value of which is generally less than or equal to 5.5.

[0031] However, the use of a basic electrolyte with a pH value>10 is also possible when using a suitable complexing agent such as e.g. triethanolamine (TEA). The electrolytic deposition takes place at current densities which produce a deposition thickness which is homogeneous over the strip length irrespective of the respective strip speed. Furthermore, the current density is dependent upon the anode construction length in the running direction of the strip. Typical values are between 1 and 150 A/dm.sup.2 per strip side. Below 1 A/dm.sup.2 excessively long processing lengths are required and consequently the process cannot be operated economically. In the case of current densities above 150 A/dm.sup.2 a homogeneous deposition is rendered significantly more difficult owing to burning-on or dendrite formation. The deposition time is dependent on the processing length, the current density, the current yield and the desired layer contact and is typically between 1 s and 30 s per side. Exemplified compositions of aqueous electrolytes and deposition conditions are shown in Table 2.

TABLE-US-00002 TABLE 2 Complexing agent Composition Conditions Citrate FeSO.sub.4•7H.sub.2O: 350 g/l pH 2.3; 45° C. Fe.sub.2(SO.sub.4).sub.3: 10 g/l Na.sub.2SO.sub.4: 110 g/l Sodium citrate: 20 g/l Triethanolamine Fe.sub.2(SO.sub.4).sub.3: 170 g/l pH 13; 80° C. NaOH: 12 g/l C.sub.6H.sub.15NO.sub.3: 15 g/l

[0032] In order to generate oxygen-containing, iron-based layers, a complexing agent for the iron ions is also required in addition to said Fe(II) and Fe(III) ions in the acid electrolyte. This is typically a compound with one or more carbonyl functionalities such as citric acid, acetic acid or even nitriloacetic acid (NTA) or ethanolamine.

[0033] Iron with a purity in wt. % of greater than 99.5 is preferably used as the anode material. Electrolyte cells with separated anode and cathode chambers can also be used, whereby the use of oxygen-generating or insoluble anodes is rendered possible. In order to reduce the cell resistance a conductive salt can optionally be added to the electrolyte. The use of further additives, such as e.g. surfactants to improve wetting or defoaming is also possible.

[0034] In one exemplified embodiment, the deposition of the oxygen-containing iron layer takes place at 60° C. with a current density of 30 A/dm.sup.2 using an iron anode with a purity in wt. % of greater than 99.5 in an aqueous sulphuric acid electrolyte with the following composition: 60 g/l iron(II), 3 g/l iron(III), 25 g/l sodium, 11 g/l citrate pH 1.8.

[0035] In a preferred large-scale implementation, the surface of the steel strip is activated prior to the deposition with the pure iron layer preferably by cleaning in a usually alkaline aqueous medium and a subsequent optional deoxidation in an acid aqueous medium. A sulphuric acid bath with an acid content of 20 to 70 g/l at temperatures of 30 to 70° C. is preferably used for the deoxidation. The subsequent coating with the oxygen-containing, iron-based layer onto the previously deposited pure iron layer is preferably effected wet-in-wet or after drying of the steel strip surface. After the deposition of the oxygen-containing, iron-based layer the steel strip surface is preferably dried in order to prevent undefined ingress of water into the annealing furnace atmosphere. In order to prevent impurities on the steel strip surface and/or carry-over between the different process media, a rinse can optionally be used after each process step. The deposition of the layers can thus take place within one or a plurality of electrolyte cells disposed one after another, the construction of which is preferably horizontal or vertical.

[0036] Trials have shown that as a result of the pre-coating with pure iron, the oxygen-containing, iron-based layer is deposited in a particularly finely crystalline form and leads to better adhesion of the hot-dip coat than when the oxygen-containing, iron-based layer is applied directly to the steel surface. Of course, the pre-coating with pure iron clearly significantly improves the nucleation conditions for the subsequent oxygen-containing, iron-based layer, whereby the nucleation rate is increased and the crystallite size therefore decreases compared to a single layer system.

[0037] In advantageous developments of the invention, provision is made for the pure iron layer to be formed with an average thickness of 0.05 to 0.5 μm and the oxygen-containing, iron-based layer with an average thickness of 0.1 to 0.6 μm. It has proved to be advantageous for improved adhesion conditions of the hot-dip coat if the pure iron layer has an average thickness of 0.1 to 0.4 μm and the oxygen-containing, iron-based layer an average thickness of 0.2 to 0.5 μm. In addition it is advantageous for the adhesion of the hot-dip coat if the average thickness of the oxygen-containing, iron-based layer is greater than the average thickness of the pure iron layer.

[0038] In a further embodiment of the invention, the oxygen-containing, iron-based layer has an oxygen proportion of more than 5 to 40 wt. %, advantageously more than 10 to 30 wt. %. In a particularly advantageous embodiment of the invention, this layer has an oxygen content of more than 12 to 25 wt. %. In trials it has proved to be the case that the more oxygen is incorporated into the iron layer the more strongly the disadvantageous external oxidation of alloy elements on the surface can be suppressed since this oxygen is used by the alloy elements for internal oxidation during the annealing prior to the hot-dip coating. However, the quantity of the oxygen incorporated into the oxygen-containing, iron-based layer is dependent to a considerable degree on the deposition conditions. Owing to technical and economic boundary conditions, the expedient maximum value for the oxygen content is 40 wt. %.

[0039] The pure iron layer itself can be applied in accordance with the invention either electrolytically or by deposition from the vapour phase, while the oxygen-containing, iron-based layer is advantageously deposited electrolytically. A layer with an average iron content of more than 96 wt. % is understood as a pure iron layer.

[0040] The steel substrate for a steel strip produced in accordance with the invention with a metallic hot-dip coat can have the following composition in wt. %:

C: 0.03% to 0.35%,

Mn: 4.1% to 8.0%,

Si: 0.008% to 2.5%,

Al: 0.001% to 2.0%,

[0041] optionally

[0042] Cr: 0.01% to 0.7%,

B: 0.001% to 0.08%,

Ti: 0.005% to 0.3%,

V: 0.005% to 0.3%,

Nb: 0.005% to 0.2%,

[0043] Mo: 0.005% to 0.7%,

P<_0.10%,

S 0.010%,

[0044] with the remainder being iron and unavoidable impurities.

[0045] The method in accordance with the invention also comprises an annealing treatment of the steel strip, provided with a pure iron layer and an oxygen-containing, iron-based layer applied thereto, in a continuous annealing furnace. This furnace can be a combination of a furnace part with open combustion (DFF, direct fired furnace/NOF, non-oxidising furnace) and a radiant tube furnace (RTF) disposed downstream thereof or can even take place in an all radiant tube furnace. The steel strip is annealed at an annealing temperature of 550° C. to 880° C. and an average heating rate of 1 K/s to 100 K/s, and a holding time of the steel strip at the annealing temperature between 30 s and 650 s. In the radiant tube furnace a reducing annealing atmosphere consisting of 2% to 40% H2 and 98 to 60% N2 and a dew point between +15° C. and −70° C. is used. Then the strip is cooled to a temperature above the melting bath temperature of the coat and subsequently coated with the metallic coat. Optionally, after the annealing treatment and before the coating with the metallic coat, the strip can be cooled to a so-called overaging temperature between 200° C. and 600° C. and held at this temperature for up to 500 s. If an overaging temperature below the melting bath temperature of the coat is selected in order e.g. to influence the microstructure and the resulting technological characteristic values of the steel, the strip can be reheated, e.g. by inductive heating, prior to entry into the melting bath, to a temperature above the melting bath temperature between 400° C. and 750° C. in order not to extract heat from the melting bath by reason of the cold steel strip.

[0046] The use of the pre-coatings in accordance with the invention renders an additional introduction of steam in order to increase the dew point, as in the previously known methods, unnecessary. For the annealing atmosphere in the furnace it has therefore proved sufficient for the ratio of the partial pressures of the steam and hydrogen during the annealing in the radiant tube furnace to be in the range of 0.00077>pH.sub.2O/pH.sub.2>0.00021, advantageously between 0.00254>pH.sub.2O/pH.sub.2>0.00021.

[0047] An exemplified advantageous implementation of the method for the production of a steel strip in accordance with the invention with improved adhesion of a hot-dip galvanisation makes provision that a hot-rolled steel strip (hot strip) is first acid-cleaned then cold-rolled and then galvanised in a hot-dip galvanising line. Within the hot-dip galvanising line the strip passes through a pre-cleaning section, after the pre-cleaning the strip passes further through a strip activation (acid-cleaning/deoxidation) and subsequently 6 electrolyte cells. In the first 3 cells, an iron layer is deposited, in the following 3 cells an oxygen-containing, iron-based layer. The coated strip then passes through a rinse and drying. The strip then passes into the furnace section of the galvanising line, is annealed and galvanised.

[0048] Metallic coats for the steel strip annealed in this manner can be e.g. aluminium-silicon (AS, AlSi), zinc (Z), zinc-aluminium (ZA, galfan), zinc-aluminium-iron (ZF, galvannealed), zinc-magnesium-aluminium (ZM, ZAM) or aluminium-zinc (AZ, galvalume). In one embodiment the metallic coat is based on zinc and the zinc coat contains 0.1 to 1 wt. % Al or 0.1 to 6 wt. % Al and 0.1 to 6 wt. % Mg or 5 to 15 wt. % Fe.

[0049] A steel strip in accordance with the invention is further characterised in that in the transition region between the metallic coat and the steel strip surface a predominantly ferritic edge zone with more than 60 vol. % ferrite is formed which advantageously has a thickness of 0.15 to 1.1 μm and particularly advantageously a thickness between 0.3 and 0.9 μm. The thickness of this edge zone results directly from the deposited pre-coatings, which, even after annealing and hot-dip coating, has microstructure characteristics deviating from the steel substrate and therefore the desired positive effects.

[0050] FIGS. 1 and 2 illustrate the results of trials by way of example. FIG. 1 shows a scanning electron microscopic image of the surface of a medium manganese steel before and after deposition of a pre-coating of pure iron and oxygen-containing, iron-based layer in accordance with the invention. The medium manganese steel comprises 6 mass percent Mn and 2 mass percent Si+Al. The images show the surface before and after deposition of the pre-coating of pure iron and oxygen-containing, iron-based layer in accordance with the invention.

[0051] FIG. 2 shows the results of depth profile analyses by means of GDOES (glow discharge optical emission spectroscopy) on the medium manganese steel samples shown in FIG. 1 after annealing at 700° C. for 120 seconds in a nitrogen atmosphere with 5% hydrogen (H.sub.2) and 95% nitrogen dioxide (N.sub.2) with a furnace dew point of −50° C. The surfaces of the samples with the pre-treatment in accordance with the invention display significantly lower contents of the elements which are disadvantageous for hot-dip coating: oxygen, manganese, silicon and aluminium.

[0052] The following table 3 shows the results of galvanising trials which were carried out on a hot-dip galvanising simulator with sample sheets of medium manganese steel (6 mass percent Mn and 2 mass percent Si+Al). The deposition of the pre-coatings was carried out electrolytically with a current density of 75 A/dm.sup.2 per side. The trials were carried out in two different heat treatments (800° C. for 200 seconds and 700° C. for 120 seconds). Samples with complete zinc wetting and good adhesion could be achieved only by means of a pre-coating of pure iron and pre-coating of an oxygen-containing, iron-based layer disposed thereover.

[0053] The coat adhesion is checked in two different test geometries in order to ensure the adhesion when the steels are used for different purposes. The coat adhesion was tested during the deformation process by means of a ball impact test according to SEP1931. In this test, a semi-spherical stamp is struck with high impact energy against a sample sheet. A cup-shaped impression is made in the sample sheet by the impact force. This process is carried out—possibly a number of times—until an incipient crack is produced in the sample sheet. The surface is then checked visually for detachment and scaling of the zinc-based coat in the region of the cup. The result is evaluated with scores from 1-4 (scores 1+2 pass, scores 3+4 fail).

[0054] The coat adhesion in the case of a crash is checked by means of a glue bead test. For this purpose, a glue bead test is applied in a defined geometry, preferably 10 mm wide and 5 mm deep of a 1K epoxy resin structure adhesive to the sample sheet. The adhesive is then cured according to the data sheet and the sample is then quickly bent by 90° within a maximum of 2 s. During this process the glue bead breaks under the severe stress and abruptly pulls on the coat which is already stressed by the bending action.

[0055] The samples are then visually assessed for zinc detachment.

TABLE-US-00003 TABLE 3 Galvanisation (Zn + 0.2% Al) Oxygen-containing, Zinc adhesion In Pure iron layer iron-based layer (Ball impact accordance Deposition Deposition Annealing (5% H.sub.2-N.sub.2) Wet test according with the No. time/s Thickness/μm time/s Thickness/μm Temp./° C. Time/s DP/° C. surface/% to SEP1931) invention 1 — — — — 800 200 −30 5 — NO 2 — — — — 800 200 −50 5 — NO 3 2 0.3 5 0.75 800 200 −50 100 Score 1 YES 4 2 0.3 3 0.45 800 200 −50 100 Score 2 YES 5 — — — — 700 120 −30 90 Score 3 NO 6 — — — — 700 120 −50 80 Score 4 NO 7 2 0.3 3 0.45 700 120 −50 100 Score 1 YES 8 2 0.3 — — 700 120 −50 80 Score 3 NO 9 — — 3 0.75 700 120 −50 100 Score 3 NO

[0056] Advantages of the invention include the following: (i) reproducible good adhesion of the metallic coat to the steel substrate; (ii) improvement of the galvanising capability of steels with high manganese contents between 4.1 and 8 mass percent; and (iii) improvement in the visual surface quality of the hot-dip coat. Moreover, to date it has often only been possible to galvanise steels with very high alloy element contents on a large scale by means of electrolytic galvanisation and they have tended to suffer from hydrogen embrittlement owing to the hydrogen introduced during this process; this risk does not arise with the hot-dip coating in accordance with the invention. It is the case that in the electrolytic deposition in accordance with the invention, hydrogen can also be formed as a by-product on the cathode and is initially present in atomically adsorbed form on the surface and can be absorbed by the steel substrate later in the process. However, during the subsequent annealing process, the conditions for the effusion of the incorporated hydrogen are present.