EP2432910B2 - Method for hot-dip coating a flat steel product containing 2-35 wt% mn and flat steel product - Google Patents
Method for hot-dip coating a flat steel product containing 2-35 wt% mn and flat steel product Download PDFInfo
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- EP2432910B2 EP2432910B2 EP10717595.2A EP10717595A EP2432910B2 EP 2432910 B2 EP2432910 B2 EP 2432910B2 EP 10717595 A EP10717595 A EP 10717595A EP 2432910 B2 EP2432910 B2 EP 2432910B2
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- flat steel
- steel product
- annealing
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- flat
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- 229910000831 Steel Inorganic materials 0.000 title claims description 134
- 239000010959 steel Substances 0.000 title claims description 134
- 238000000034 method Methods 0.000 title claims description 36
- 238000003618 dip coating Methods 0.000 title claims description 18
- 239000010410 layer Substances 0.000 claims description 92
- 238000000137 annealing Methods 0.000 claims description 90
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 73
- 239000011701 zinc Substances 0.000 claims description 72
- 238000000576 coating method Methods 0.000 claims description 37
- 239000011248 coating agent Substances 0.000 claims description 36
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 32
- 229910052725 zinc Inorganic materials 0.000 claims description 32
- 239000000758 substrate Substances 0.000 claims description 28
- 229910052742 iron Inorganic materials 0.000 claims description 26
- 229910052748 manganese Inorganic materials 0.000 claims description 24
- 229910052782 aluminium Inorganic materials 0.000 claims description 20
- 239000012535 impurity Substances 0.000 claims description 17
- 229910052749 magnesium Inorganic materials 0.000 claims description 11
- 239000011253 protective coating Substances 0.000 claims description 11
- 238000005260 corrosion Methods 0.000 claims description 10
- 230000007797 corrosion Effects 0.000 claims description 10
- 229910052751 metal Inorganic materials 0.000 claims description 8
- 239000002184 metal Substances 0.000 claims description 8
- 229910052759 nickel Inorganic materials 0.000 claims description 8
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- 239000010960 cold rolled steel Substances 0.000 claims description 7
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910001297 Zn alloy Inorganic materials 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 6
- 230000001603 reducing effect Effects 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 230000001590 oxidative effect Effects 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 229920006395 saturated elastomer Polymers 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 229910045601 alloy Inorganic materials 0.000 claims description 4
- 239000000956 alloy Substances 0.000 claims description 4
- 238000007598 dipping method Methods 0.000 claims description 3
- 230000000694 effects Effects 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910052797 bismuth Inorganic materials 0.000 claims description 2
- 229910052793 cadmium Inorganic materials 0.000 claims description 2
- 229910052745 lead Inorganic materials 0.000 claims description 2
- 239000011241 protective layer Substances 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims 2
- 239000000470 constituent Substances 0.000 claims 1
- 238000011144 upstream manufacturing Methods 0.000 claims 1
- 239000011572 manganese Substances 0.000 description 73
- 239000011777 magnesium Substances 0.000 description 19
- 238000012360 testing method Methods 0.000 description 19
- 238000009736 wetting Methods 0.000 description 14
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 12
- 229910052739 hydrogen Inorganic materials 0.000 description 12
- 239000000523 sample Substances 0.000 description 11
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 9
- 239000000155 melt Substances 0.000 description 9
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 8
- 229910000617 Mangalloy Inorganic materials 0.000 description 5
- 239000001257 hydrogen Substances 0.000 description 5
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 4
- 230000004888 barrier function Effects 0.000 description 4
- 239000011651 chromium Substances 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 238000007654 immersion Methods 0.000 description 4
- 229910015136 FeMn Inorganic materials 0.000 description 3
- 239000002318 adhesion promoter Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 239000011247 coating layer Substances 0.000 description 3
- 238000010276 construction Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- 229910000794 TRIP steel Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 238000007757 hot melt coating Methods 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000012943 hotmelt Substances 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 238000011065 in-situ storage Methods 0.000 description 1
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000001228 spectrum Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0222—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating in a reactive atmosphere, e.g. oxidising or reducing atmosphere
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0224—Two or more thermal pretreatments
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/026—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
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
Definitions
- the invention relates to a method for hot-dip coating a flat steel product containing 6-35% by weight of Mn with zinc or a zinc alloy, and a flat steel product provided with a zinc or zinc alloy coating.
- Typical alloying elements are manganese, chromium, silicon, aluminum and others, which form stable, non-reducible oxides on the surface with conventional recrystallizing annealing. These oxides can prevent reactive wetting with a molten zinc.
- Steels with a high manganese content are particularly suitable for use in vehicle construction due to their favorable combination of properties, consisting of high strengths of up to 1,400 MPa on the one hand and extremely high elongations (uniform elongation up to 70% and elongation at break up to 90%) on the other , especially in the automotive industry.
- Steels with high Mn contents of 6% by weight to 30% by weight that are particularly suitable for this purpose are, for example, from DE 102 59 230 A1 , the DE 197 27 759 C2 or the DE 199 00 199 A1 known.
- Flat products made from the known steels exhibit isotropic deformation behavior with high strength and are also still ductile even at low temperatures.
- the reason for these poor adhesion properties was determined to be the thick oxide layer that develops during the annealing process that is essential for hot-dip coating.
- the sheet metal surfaces oxidized in this way can no longer be wetted with the coating metal with the required uniformity and completeness, so that the goal of comprehensive corrosion protection is not achieved.
- WO 2006/042931 A1 Another method for coating a high-manganese steel strip containing 0.35-1.05% by weight C, 16-25% by weight Mn, the remainder iron and unavoidable impurities is known from WO 2006/042931 A1 known.
- the steel strip composed in this way is first cold-rolled and then recrystallized annealed in an atmosphere which has a reducing effect on iron.
- the annealing parameters are selected in such a way that an intermediate layer is formed on both sides of the steel strip, which essentially consists entirely of amorphous (FeMn) oxide, and an additional outer layer is formed, which consists of crystalline Mn oxide, with the thickness of the both layers is at least 0.5 ⁇ m. Hot-dip coating then no longer takes place. Rather, the Mn oxide layer in combination with the (FeMn) oxide layer should offer adequate protection against corrosion.
- This specification is based on the knowledge that by suitably setting the annealing atmosphere, namely its hydrogen content in relation to its dew point, a surface quality of the steel strip to be coated is achieved during annealing that ensures optimal adhesion of the metallic protective coating subsequently applied by hot-dip coating .
- the annealing atmosphere set in this way has a reducing effect on both the iron and the manganese in the steel strip.
- the aim is to avoid the formation of an oxide layer that would impair the adhesion of the fused coating to the high-manganese steel substrate.
- the object of the invention was to provide a method that allows flat steel products containing high levels of Mn to be provided with a zinc coating that protects against corrosion and in which further improved adhesion of the coating on the steel substrate is ensured.
- a steel flat product was to be created in which the Zn coating formed from zinc or a zinc alloy adheres securely to the steel substrate even under high degrees of deformation.
- this object is achieved according to the invention in that the work steps specified in claim 1 are carried out during the hot-dip coating of a flat steel product having a high Mn content.
- a flat steel product in the form of a steel strip or sheet steel is first provided in a continuous process sequence for the hot-dip coating of a flat steel product containing 6-35% by weight of Mn.
- the coating procedure according to the invention is particularly suitable for steel strips that are highly alloyed in order to ensure high strength and good elongation properties.
- Steel strips which are provided with a metallic protective coating by hot-dip coating in the manner according to the invention contain (in % by weight) C: ⁇ 1.6%, Mn: 6-35%, Al: ⁇ 10%, Ni: ⁇ 10%, Cr: ⁇ 10%, Si: ⁇ 10%, Cu: ⁇ 3%, Nb: ⁇ 0.6%, Ti: ⁇ 0.3%, V: ⁇ 0.3%, P: ⁇ 0.1%, B: ⁇ 0.01%, Mo: ⁇ 0.3%, N: ⁇ 1.0%, balance iron and unavoidable impurities.
- the effects achieved by the invention are effective in the coating of high-alloy steel strips which contain manganese contents of at least 6% by weight. It is thus evident that a steel base material which (in % by weight) C: ⁇ 1.00%, Mn: 20.0 - 30.0%, Al: ⁇ 0.5%, Si: ⁇ 0.5% , B: ⁇ 0.01%, Ni: ⁇ 3.0%, Cr: ⁇ 10.0%, Cu: ⁇ 3.0%, N: ⁇ 0.6%, Nb: ⁇ 0.3%, Ti : ⁇ 0.3%, V: ⁇ 0.3%, P: ⁇ 0.1%, the remainder containing iron and unavoidable impurities, can be coated particularly well with a coating that protects against corrosion.
- a steel is used as the base material which (in % by weight) C: ⁇ 1.00%, Mn: 7.00 - 30.00%, Al: 1.00 - 10.00%, Si : > 2.50 - 8.00% (whereby the sum of Al content and Si content is > 3.50 - 12.00%), B: ⁇ 0.01%, Ni: ⁇ 8, 00%, Cu: ⁇ 3.00%, N: ⁇ 0.60%, Nb: ⁇ 0.30%, Ti: ⁇ 0.30%, V: ⁇ 0.30%, P: ⁇ 0.01% , balance iron and unavoidable impurities.
- both hot-rolled and cold-rolled steel strips can be coated in the manner according to the invention as flat steel products, with the method according to the invention being particularly effective in the processing of cold-rolled steel strip.
- the flat products made available in this way are annealed in a work step b).
- the glow temperature Tg is 600 - 1100 °C, while the annealing time, over which the steel flat product is kept at the annealing temperature, is 10 - 240 s.
- the annealing temperature Tg and annealing duration mentioned above has a reducing effect on iron oxide FeO present on the steel flat product and an oxidizing effect on the manganese contained in the steel substrate.
- the annealing atmosphere contains 0.01 - 85 vol 2 O/H 2 ratio applies: 8th ⁇ 10 ⁇ 15 ⁇ day 3,529 ⁇ H 2 O / H 2 ⁇ 0.957
- the H 2 O/H 2 ratio is to be set such that it is greater than 8 ⁇ 10 -15 *Tg 3.529 and at most 0.957, with Tg denoting the respective annealing temperature.
- the dew point of the atmosphere is in the range from -50°C to +60°C.
- the annealing atmosphere in this case typically contains 0.1-85% by volume of H 2 .
- a particularly economical mode of operation of the continuous furnace used for annealing according to the invention can be achieved by keeping the dew point of the atmosphere at -20.degree. C. to +20.degree.
- the Mn mixed oxide layer is defined as MnO ⁇ Fe metal . This means that metallic iron is present in this Mn mixed oxide layer and not oxidized iron, as is the case in the prior art.
- an Mn mixed oxide layer is set in a targeted manner via at least one annealing stage, in that the annealing (step b)) is carried out under an atmosphere that reduces FeO and an atmosphere that oxidizes Mn.
- the layer of Mn mixed oxides produced according to the invention on the steel substrate forms an adhesion base to which the subsequently applied zinc layer surprisingly adheres particularly securely.
- the Mn mixed oxide layer is largely retained during the hot-dip coating process, so that it also ensures the permanent cohesion of the Zn coating and steel substrate in the finished product.
- the flat steel product which has been cooled to the bath inlet temperature, is then passed through an iron-saturated, 420 - 520 °C hot Zn molten bath within an immersion time of 0.1 - 10 seconds, in particular 0.1 - 5 s, which consists of the main component zinc and zinc unavoidable impurities and 0.05-8% by weight Al and/up to 8% by weight Mg, in particular 0.05-5% by weight Al and up to 5% by weight Mg.
- the molten bath optionally Si ⁇ 2%, Pb ⁇ 0.1%, Ti ⁇ 0.2%, Ni ⁇ 1%, Cu ⁇ 1%, Co ⁇ 0.3%, Mn ⁇ 0.5%, Cr ⁇ 0.2%, Sr ⁇ 0.5%, Fe ⁇ 3%, B ⁇ 0.1%, Bi ⁇ 0.1%, Cd ⁇ 0.1% present in order to determine certain properties of the coating in a manner known per se set.
- the flat steel product obtained in this way which is hot-dip coated with a Zn protective coating to protect against corrosion, is finally cooled, it being possible for the thickness of the coating to be adjusted in a manner known per se before cooling.
- the Zn coating according to the invention necessarily contains Al contents of 0.05-8% by weight and additional contents of up to 8% by weight Mg, with the upper limit of the contents of both elements being typically limited to a maximum of 5% by weight in practice. % is limited.
- a flat steel product according to the invention with an Mn content of 6-35% by weight and a Zn protective coating that protects against corrosion is accordingly characterized in that the Zn protective coating has a Mn mixed oxide layer that essentially covers and adheres to the flat steel product, in which metallic Iron is present, and has a Zn layer that shields the flat steel product and the Mn mixed oxide layer adhering to it from the environment.
- the Zn protective coating comprises an Fe(Mn) 2 Al 5 layer arranged between the Mn mixed oxide layer and the Zn layer. This occurs when there is a sufficient quantity of aluminum of 0.05 - 5% by weight Al in the molten bath.
- the Fe (Mn) 2 Al 5 layer forms a barrier layer through which the reduction of the Mn mixed oxide layer melt dipping is reliably prevented.
- the barrier layer can transform into FeZn phases, with the Mn oxide layer nevertheless being retained.
- the MnO layer and the Fe(Mn) 2 Al 5 layer of a coating produced and configured according to the invention thus ensure, even after hot-dip coating, that the outer Zn layer adheres firmly to the steel substrate with high degrees of deformation.
- the presence of a Mn mixed oxide layer on the surface of the steel substrate according to the invention not only has a positive effect if the Fe(Mn) 2 Al 5 layer is also formed, but also if magnesium is used as an alternative or in addition to aluminum in the molten bath is present in effective levels. Even when a ZnMg coating layer is produced on the steel substrate, the MnO layer produced according to the invention ensures particularly good and uniform wetting of the steel flat product with optimum adhesion and minimized risk of cracking or flaking even with high degrees of deformation.
- a particularly practical embodiment of the invention results in this connection when the following applies to the ratio of the Al content %Al and the Mg content %Mg: %Al/%Mg ⁇ 1.
- the Al content is therefore of the melt bath is always smaller than its Mg content.
- Magnesium is characterized by a higher reduction potential to MnO than aluminum. Therefore, when higher Mg contents are present in the melted layer, there is a forced dissolution of the MnO structure of the mixed oxide layer.
- the mixed oxide is dissolved to a greater extent, more metallic iron “Fe metal " from the "depth” of the mixed oxide layer is effectively available at the mixed oxide layer/zinc bath reaction front, so that the covering Fe(Mn) 2 Al 5 boundary layer is particularly effective as an adhesion promoter can train. Accordingly, the MnO reduction by dissolved magnesium in situ contributes with a particularly high degree of effectiveness to the boundary layer formation that is aimed at according to the invention and ensures particularly good adhesion of the Zn coating.
- the annealing step (work step b)) carried out in preparation for the hot-dip coating in the context of the process according to the invention can be carried out in one or more stages. If the annealing is carried out in one stage, different hydrogen contents are possible in the annealing atmosphere depending on the dew point. If the dew point is in the range from -50 °C to +20 °C, the annealing atmosphere can contain at least 0.01% by volume H 2 , but less than 3% by volume H 2 . If, on the other hand, a dew point of at least +20 °C up to and including + 60 °C is set, the hydrogen content should be in the range of 3% to 85% so that the atmosphere has a reducing effect on iron. Taking into account the other parameters to be taken into account during the implementation of the annealing step according to the invention, the reducing effect on the FeO that may be present and the oxidizing effect on the Mn present in the steel substrate are thus reliably achieved.
- an additional annealing step can be carried out before the annealing step (work step b) of claim 1) carried out according to the invention, in which the flat steel product is heated to an annealing temperature of 200 - 1100 °C is maintained for an annealing period of 0.1-60 s under an atmosphere oxidative for both Fe and Mn, containing 0.0001-5 vol.% H 2 and optionally 200-5500 vol.ppm O 2 and a has a dew point in the range of -60 °C to +60 °C.
- the annealing step according to the invention is then carried out at a dew point in the range from -50 °C to +20 °C in an atmosphere containing 0.01-85% hydrogen, taking into account the other parameters to be taken into account when carrying out the annealing step according to the invention, before the steel flat product into the melt bath.
- Optimum adhesion properties of the Zn coating are achieved with a coating produced according to the invention when the thickness of the Mn mixed oxide layer obtained after annealing (step b)) is 40-400 nm, in particular up to 200 nm.
- a cold-rolled steel strip has been produced in a known manner from a high-manganese steel having the composition given in Table 1.
- Table 1 C Mn P si v Al Cr Ti Nb 0.634 22.2 0.02 0.18 0.2 0.01 0.08 0.001 0.001 Rest iron and unavoidable impurities, data in % by weight
- a first sample of the cold-rolled steel strip was then annealed in a single-stage annealing process.
- the steel strip sample was heated at a heating rate of 10 K/s to an annealing temperature Tg of 800° C., at which the sample was then held for 30 seconds.
- the annealing took place under an annealing atmosphere which consisted of 5% by volume H 2 and 95% by volume N 2 and whose dew point was +25°C.
- the annealed steel strip was then cooled at a cooling rate of 20 K/s to a bath inlet temperature of 480° C., at which point it was initially subjected to an overaging treatment for 20 seconds.
- the overaging treatment took place under the unchanged annealing atmosphere.
- the steel strip was then fed into a 460 °C hot, Fe-saturated molten zinc bath which, in addition to Zn, unavoidable impurities and Fe, also contained 0.23% by weight Al. After an immersion time of 2 seconds, the steel strip, which is now hot-dip coated, was removed from the molten bath and cooled to room temperature.
- the steel strip was first heated to 600 °C at a heating rate of 10 K/s and held at this annealing temperature for 10 seconds.
- the annealing atmosphere contained 2000 ppm O 2 and the remainder N 2 .
- Her dew point was -30 °C.
- the steel strip was heated in a second annealing step to an annealing temperature Tg of 800 °C, at which it was held for 30 seconds under an annealing atmosphere containing 5 vol -30 °C.
- the steel strip was then cooled to 480° C. under the annealing atmosphere at a cooling temperature of approx. 20 K/s and subjected to an overaging treatment for 20 seconds.
- the steel strip was then fed with a bath inlet temperature of 480 °C into a 460 °C hot melt bath saturated with Fe, which in turn contained 0.23% by weight Al and other elements in ineffective traces of impurities and the remainder zinc.
- the finished hot-dip coated flat steel product was then removed from the melt bath and cooled to room temperature.
- Mn mixed oxide layer M 20-400 nm, while the thickness of the Fe(Mn) 2 Al 5 intermediate layer F is 10-200 nm.
- the total thickness of the coating layers M and F is accordingly 20 - 600 nm.
- the zinc layer Zn is significantly thicker at 3 - 20 ⁇ m.
- the influence of the dew point of the respective annealing atmosphere on the coating result was examined.
- the samples were each subjected to an annealing process in which they were also heated to an annealing temperature Tg of 800 °C at a heating rate of 10 K/s.
- Tg annealing temperature
- the sample was then held at this annealing temperature for 60 seconds.
- the annealing took place in each case under an annealing atmosphere that consisted of 5% by volume H 2 and 95% by volume N 2 , the respective dew point of the annealing atmosphere being varied between ⁇ 55° C. and +45° C.
- the annealed steel strip was cooled at a cooling rate of 20 K/s to a bath inlet temperature of 480° C., as in the test series described above, at which point it was initially subjected to an overaging treatment for 20 seconds.
- the overaging treatment took place under the unchanged annealing atmosphere.
- the steel strip was then fed into a 460 °C hot, Fe-saturated molten zinc bath which, in addition to Zn, unavoidable impurities and Fe, also contained a combination of 0.4% by weight Al and 1.0 wt% Mg or alone 0.14 wt%, 0.17 wt% or 0.23 wt% Al.
- the steel strip, which is now hot-dip coated was removed from the molten bath and cooled to room temperature.
- the thickness of the Mn mixed oxide layer M' is 20-400 nm, while the thickness of the Fe(Mn) 2 Al 5 intermediate layer F' is 10-200 nm.
- the total thickness of the coating layers M' and F' is accordingly 20 - 600 nm.
- the zinc layer ZnMg is significantly thicker at 3 - 20 ⁇ m.
- the comparative samples C1-C6 were also heat-treated in the manner described above for the samples according to the invention before they were hot-dip coated in the melt bath.
- the molten bath contained 0.4% by weight Al and 1% by weight Mg in each case.
- the degree of wetting and the zinc adhesion were also examined on samples C1-C6 coated in this way.
- the test parameters and results of these tests are listed in Table 6. It turns out that due to the lower manganese content of steels VS1 and VS2, no MnO structure forms in the mixed oxidation layer on the surface of the steel substrate. As a result, no covering Fe(Mn) 2 layer is formed as an adhesion promoter.
Description
Die Erfindung betrifft ein Verfahren zum Schmelztauchbeschichten eines 6 - 35 Gew.-% Mn enthaltenden Stahlflachprodukts mit Zink oder einer Zinklegierung sowie ein mit einem Zink- oder Zinklegierungsüberzug versehenes Stahlflachprodukt.The invention relates to a method for hot-dip coating a flat steel product containing 6-35% by weight of Mn with zinc or a zinc alloy, and a flat steel product provided with a zinc or zinc alloy coating.
Im modernen Automobilbau wird verstärkt auf hoch und höchstfeste Stähle zurückgegriffen. Typische Legierungselemente sind Mangan, Chrom, Silicium, Aluminium u.a., die bei konventioneller rekristallisierender Glühbehandlung stabile nicht reduzierbare Oxide an der Oberfläche bilden. Diese Oxide können die reaktive Benetzung mit einer Zinkschmelze hindern.In modern automobile construction, use is increasingly being made of high-strength and ultra-high-strength steels. Typical alloying elements are manganese, chromium, silicon, aluminum and others, which form stable, non-reducible oxides on the surface with conventional recrystallizing annealing. These oxides can prevent reactive wetting with a molten zinc.
Stähle mit hohen Mangan-Gehalten eignen sich aufgrund ihrer günstigen Eigenschaftskombination aus hohen Festigkeiten von bis zu 1.400 MPa einerseits und extrem hohen Dehnungen (Gleichmaßdehnungen bis zu 70 % und Bruchdehnungen bis zu 90 %) andererseits grundsätzlich im besonderen Maße für die Verwendung im Bereich des Fahrzeugbaus, insbesondere im Automobilbau. Für diesen Einsatzzweck speziell geeignete Stähle mit hohen Mn-Gehalten von 6 Gew.-% bis 30 Gew.-% sind beispielsweise aus der
Diesen Vorteilen steht jedoch gegenüber, dass hochmanganhaltige Stähle zu Lochfraß neigen und nur schwer zu passivieren sind. Diese im Vergleich zu niedriger legierten Stählen bei Einwirken erhöhter Chloridionen-Konzentrationen große Neigung zu lokal zwar begrenzter, jedoch intensiver Korrosion macht die Verwendung von zur Werkstoffgruppe der hochlegierten Stahlbleche gehörenden Stählen gerade im Karosseriebau schwierig. Zudem neigen hochmanganhaltige Stähle zu Flächenkorrosion, wodurch das Spektrum ihrer Verwendung ebenfalls einschränkt wird.However, these advantages are offset by the fact that high-manganese steels tend to pit and are difficult to passivate. In comparison to low-alloy steels, this great tendency towards locally limited but intensive corrosion when exposed to increased chloride ion concentrations makes it difficult to use steels belonging to the material group of high-alloy steel sheets, especially in body construction. In addition, steels with a high manganese content tend to surface corrosion, which also limits the spectrum of their use.
Daher ist vorgeschlagen worden, auch Stahlflachprodukte, die aus hochmanganhaltigen Stählen erzeugt sind, in an sich bekannter Weise mit einem metallischen Überzug zu versehen, der den Stahl vor korrosivem Angriff schützt. Praktische Versuche, Stahlbänder mit hohen Mangangehalten durch ein kostengünstig durchführbares Schmelztauchbeschichten mit einer metallischen Schutzschicht zu versehen, brachten neben grundsätzlichen Problemen bei der Benetzung mit der Zn-Schmelze insbesondere im Hinblick auf die bei einer Kaltverformung von dem Überzug geforderten Haftung auf dem Stahlsubstrat unbefriedigende Ergebnisse.It has therefore been proposed to also provide flat steel products made from high-manganese steels with a metallic coating in a manner known per se, which protects the steel from corrosive attack. Practical attempts to provide steel strips with high manganese contents with a metallic protective layer by means of a cost-effective hot-dip coating process have produced unsatisfactory results, in addition to fundamental problems with wetting with the Zn melt, particularly with regard to the adhesion to the steel substrate required of the coating during cold deformation.
Als Grund für diese schlechten Haftungseigenschaften wurde die starke Oxidschicht ermittelt, die sich bei der für das Schmelztauchbeschichten unverzichtbaren Glühung einstellt. Die derart oxidierten Blechoberflächen lassen sich nicht mehr mit der erforderlichen Gleichmäßigkeit und Vollständigkeit mit dem Überzugsmetall benetzen, so dass das Ziel eines flächendeckenden Korrosionsschutzes nicht erreicht wird.The reason for these poor adhesion properties was determined to be the thick oxide layer that develops during the annealing process that is essential for hot-dip coating. The sheet metal surfaces oxidized in this way can no longer be wetted with the coating metal with the required uniformity and completeness, so that the goal of comprehensive corrosion protection is not achieved.
Die aus dem Bereich von hochlegierten, jedoch niedrigere Mn-Gehalte aufweisenden Stählen bekannten Möglichkeiten der Verbesserung der Benetzbarkeit durch Aufbringen einer Zwischenschicht aus Fe oder Ni führten bei Stahlblechen mit mindestens 6 Gew.-% Mangan nicht zu dem gewünschten Erfolg.The possibilities of improving wettability by applying an intermediate layer of Fe or Ni, which are known from the area of high-alloy steels with lower Mn contents, did not lead to the desired success in steel sheets with at least 6% by weight manganese.
In der
Ein anderes Verfahren zum Beschichten eines hochmanganhaltigen, 0,35 - 1,05 Gew.-% C, 16 - 25 Gew.-% Mn, Rest Eisen sowie unvermeidbare Verunreinigungen enthaltendes Stahlband ist aus der
Auf einem ähnlichen Prinzip basiert das in der
Praktische Untersuchungen haben gezeigt, dass auch derart aufwändig vorbeschichtete Stahlbänder in der Praxis nicht die für eine Kaltverformung geforderte Haftung auf dem Stahlsubstrat aufweisen. Darüber hinaus erweist sich das aus der
Schließlich ist aus der
Praktische Untersuchungen haben gezeigt, dass gemäß dem voranstehend erläuterten bekannten Verfahren vorbereitete Stahlflachprodukte zwar ein gutes Benetzungsverhalten und eine für viele Anwendungen ausreichende Haftung des Zn-Überzuges aufweisen. Jedoch ergab sich bei der Verformung von entsprechend beschichteten Stahlflachprodukten zu Bauteilen, dass es bei hohen Verformungsgraden nach wie vor zu Ablösungen und Rissbildungen des Überzugs kommt.Practical investigations have shown that flat steel products prepared according to the known method explained above have good wetting behavior and adhesion of the Zn coating which is sufficient for many applications. However, when flat steel products with a corresponding coating were deformed into components, it was found that the coating still came off and cracked at high degrees of deformation.
Ferner können die aus dem Stand der Technik bekannten Verfahren, insbesondere bei Anwendung von hohen Prozesstemperaturen, die mechanischen Eigenschaften im Stahlflachprodukt negativ beeinflussen. Des Weiteren ist mit den bestehenden Prozessen kein ökonomischern, den ökologischen Anforderungen gerecht werdender Betrieb möglich.Furthermore, the methods known from the prior art, particularly when high process temperatures are used, can adversely affect the mechanical properties in the flat steel product. Furthermore, no more economical operation that meets ecological requirements is possible with the existing processes.
Vor diesem Hintergrund bestand die Aufgabe der Erfindung darin, ein Verfahren anzugeben, das es erlaubt, hohe Gehalte an Mn aufweisende Stahlflachprodukte mit einem vor Korrosion schützenden Zinküberzug zu versehen, bei dem eine weiter verbesserte Haftung des Überzugs auf dem Stahlsubstrat gewährleistet ist. Darüber hinaus sollte ein Stahlflachprodukt geschaffen werden, bei dem auch unter hohen Verformungsgraden der jeweils aus Zink oder eine Zinklegierung gebildete Zn-Überzug sicher auf dem Stahlsubstrat haftet.Against this background, the object of the invention was to provide a method that allows flat steel products containing high levels of Mn to be provided with a zinc coating that protects against corrosion and in which further improved adhesion of the coating on the steel substrate is ensured. In addition, a steel flat product was to be created in which the Zn coating formed from zinc or a zinc alloy adheres securely to the steel substrate even under high degrees of deformation.
In Bezug auf das Verfahren ist diese Aufgabe erfindungsgemäß dadurch gelöst, dass beim Schmelztauchbeschichten eines hohe Mn-Gehalte aufweisenden Stahlflachproduktes die in Anspruch 1 angegebenen Arbeitsschritte absolviert werden.With regard to the method, this object is achieved according to the invention in that the work steps specified in claim 1 are carried out during the hot-dip coating of a flat steel product having a high Mn content.
In Bezug auf das Produkt ist die voranstehend angegebene Aufgabe zudem durch ein Stahlflachprodukt gelöst worden, das erfindungsgemäß die in Anspruch 7 angegebenen Merkmale besitzt.With regard to the product, the object specified above has also been achieved by a flat steel product which, according to the invention, has the features specified in claim 7 .
Gemäß der Erfindung wird zum Schmelztauchbeschichten eines 6 - 35 Gew.-% Mn enthaltenden Stahlflachprodukts in einem kontinuierlichen Verfahrensablauf zunächst ein Stahlflachprodukt in Form eines Stahlbands oder Stahlblechs zur Verfügung gestellt.According to the invention, a flat steel product in the form of a steel strip or sheet steel is first provided in a continuous process sequence for the hot-dip coating of a flat steel product containing 6-35% by weight of Mn.
Die erfindungsgemäße Vorgehensweise bei der Beschichtung ist insbesondere für solche Stahlbänder geeignet, die hoch legiert sind, um hohe Festigkeiten und gute Dehnungseigenschaften zu gewährleisten.The coating procedure according to the invention is particularly suitable for steel strips that are highly alloyed in order to ensure high strength and good elongation properties.
Stahlbänder, die in erfindungsgemäßer Weise durch Schmelztauchbeschichten mit einem metallischen Schutzüberzug versehen werden, enthalten (in Gew.-%) C: ≤ 1,6 %, Mn: 6 - 35 %, Al: ≤ 10 %, Ni: ≤ 10 %, Cr: ≤ 10 %, Si: ≤ 10 %, Cu: ≤ 3 %, Nb: ≤ 0,6 %, Ti: ≤ 0,3 %, V: ≤ 0,3 %, P: ≤ 0,1 %,
B: ≤ 0,01 %, Mo: ≤ 0,3 %, N: ≤ 1,0 %, Rest Eisen und unvermeidbare Verunreinigungen.Steel strips which are provided with a metallic protective coating by hot-dip coating in the manner according to the invention contain (in % by weight) C: ≦1.6%, Mn: 6-35%, Al: ≦10%, Ni: ≦10%, Cr: ≤ 10%, Si: ≤ 10%, Cu: ≤ 3%, Nb: ≤ 0.6%, Ti: ≤ 0.3%, V: ≤ 0.3%, P: ≤ 0.1%,
B: ≤ 0.01%, Mo: ≤ 0.3%, N: ≤ 1.0%, balance iron and unavoidable impurities.
Erfindungsgemäss wirken sich die durch die Erfindung erzielten Effekte bei der Beschichtung von hochlegierten Stahlbändern aus die Mangan-Gehalte von mindestens 6 Gew.-% enthalten. So zeigt sich, dass ein Stahlgrundmaterial, welches (in Gew.-%) C: ≤ 1,00 %, Mn: 20,0 - 30,0 %, Al: ≤ 0,5 %, Si: ≤ 0,5 %, B: ≤ 0,01 %, Ni: ≤ 3,0 %, Cr: ≤ 10,0 %, Cu: ≤ 3,0 %, N: < 0,6 %, Nb: < 0,3 %, Ti: < 0,3 %, V: < 0,3 %, P: < 0,1 %, Rest Eisen und unvermeidbare Verunreinigungen enthält, sich besonders gut mit einem vor Korrosion schützenden Überzug beschichten lässt.According to the invention, the effects achieved by the invention are effective in the coating of high-alloy steel strips which contain manganese contents of at least 6% by weight. It is thus evident that a steel base material which (in % by weight) C: ≤ 1.00%, Mn: 20.0 - 30.0%, Al: ≤ 0.5%, Si: ≤ 0.5% , B: ≤ 0.01%, Ni: ≤ 3.0%, Cr: ≤ 10.0%, Cu: ≤ 3.0%, N: < 0.6%, Nb: < 0.3%, Ti : < 0.3%, V: < 0.3%, P: < 0.1%, the remainder containing iron and unavoidable impurities, can be coated particularly well with a coating that protects against corrosion.
Gleiches gilt, wenn ein Stahl als Grundmaterial eingesetzt wird, der (in Gew.-%) C: ≤ 1,00 %, Mn: 7,00 - 30,00 %, Al: 1,00 - 10,00 %, Si: > 2,50 - 8,00 % (wobei gilt, dass die Summe aus Al-Gehalt und Si-Gehalt > 3,50 - 12,00 % ist), B: < 0,01 %, Ni: < 8,00 %, Cu: < 3,00 %, N: < 0,60 %, Nb: < 0,30 %, Ti: < 0,30 %, V: < 0,30 %, P: < 0,01 %, Rest Eisen und unvermeidbare Verunreinigungen enthält.The same applies if a steel is used as the base material which (in % by weight) C: ≤ 1.00%, Mn: 7.00 - 30.00%, Al: 1.00 - 10.00%, Si : > 2.50 - 8.00% (whereby the sum of Al content and Si content is > 3.50 - 12.00%), B: < 0.01%, Ni: < 8, 00%, Cu: <3.00%, N: <0.60%, Nb: <0.30%, Ti: <0.30%, V: <0.30%, P: <0.01% , balance iron and unavoidable impurities.
Wie bei der üblichen Schmelztauchbeschichtung können als Stahlflachprodukte sowohl warmgewalzte als auch kaltgewalzte Stahlbänder in erfindungsgemäßer Weise beschichtet werden, wobei sich das erfindungsgemäße Verfahren insbesondere bei der Verarbeitung von kaltgewalztem Stahlband bewährt.As with conventional hot-dip coating, both hot-rolled and cold-rolled steel strips can be coated in the manner according to the invention as flat steel products, with the method according to the invention being particularly effective in the processing of cold-rolled steel strip.
Die so zur Verfügung gestellten Flachprodukte werden in einem Arbeitschritt b) geglüht. Die Glühtemperatur Tg beträgt dabei 600 - 1100 °C, während die Glühdauer, über die das Stahlflachprodukt auf der Glühtemperatur gehalten wird, 10 - 240 s beträgt.The flat products made available in this way are annealed in a work step b). The glow temperature Tg is 600 - 1100 °C, while the annealing time, over which the steel flat product is kept at the annealing temperature, is 10 - 240 s.
Für die Erfindung entscheidend ist, dass der bei der voranstehend genannten Glühtemperatur Tg und Glühdauer unter einer in Bezug auf Eisenoxid FeO, das auf dem Stahlflachprodukt vorhanden ist, reduzierend und in Bezug auf das im Stahlsubstrat enthaltene Mangan oxidierend wirkt. Dazu enthält die Glühatmosphäre 0,01 - 85 Vol.-% H2, H2O und als Rest N2 sowie technisch bedingt unvermeidbare Verunreinigungen und weist einen zwischen -50 °C und +60 °C liegenden Taupunkt auf, wobei für das H2O/H2-Verhältnis gilt:
Erfindungsgemäß ist also das Verhältnis H2O/H2 so einzustellen, dass es einerseits größer als 8x10-15*Tg3,529 und andererseits höchstens gleich 0,957 ist, wobei mit Tg die jeweilige Glühtemperatur bezeichnet ist.According to the invention, the H 2 O/H 2 ratio is to be set such that it is greater than 8×10 -15 *Tg 3.529 and at most 0.957, with Tg denoting the respective annealing temperature.
Bei praxistypischen Anwendungen, die insbesondere darauf abzielen, auf dem jeweiligen Stahlsubstrat in erfindungsgemäßer Weise ein Mg-haltigen Zinklegierungsüberzug in einem einstufigen Glühverfahren zu erzeugen, liegt der Taupunkt der Atmosphäre im Bereich von - 50 °C bis + 60 °C. Gleichzeitig enthält die Glühatmosphäre in diesem Fall typischerweise 0,1 - 85 Vol.-% H2. Eine besonders wirtschaftliche Betriebsweise des zum Glühen erfindungsgemäß genutzten Durchlaufofens kann dadurch erreicht werden, dass der Taupunkt der Atmosphäre bei - 20 °C bis +20 °C gehalten wird.In typical applications, which aim in particular to produce a Mg-containing zinc alloy coating on the respective steel substrate in a one-stage annealing process according to the invention, the dew point of the atmosphere is in the range from -50°C to +60°C. At the same time, the annealing atmosphere in this case typically contains 0.1-85% by volume of H 2 . A particularly economical mode of operation of the continuous furnace used for annealing according to the invention can be achieved by keeping the dew point of the atmosphere at -20.degree. C. to +20.degree.
Im Ergebnis wird so durch eine vor dem Schmelztauchbeschichten durchgeführte Glühung auf dem Stahlflachprodukt eine 20 - 400 nm dicke, das Stahlflachprodukt mindestens abschnittsweise bedeckende Mn-Mischoxidschicht erzeugt, wobei es im Hinblick auf die Haftung des Zn-Überzuges auf dem Stahlsubstrat besonders günstig ist, wenn die Mn-Mischoxidschicht die Oberfläche des Stahlflachproduktes nach dem Glühen im Wesentlichen vollständig bedeckt. Die Mn-Mischoxidschicht ist dabei im Sinne der Erfindung als MnO·Femetall definiert. D.h., in dieser Mn-Mischoxidschicht liegt metallisches Eisen vor und nicht, wie beim Stand der Technik, oxidiertes Eisen.As a result, a 20 - 400 nm thick Mn mixed oxide layer covering at least sections of the flat steel product is produced by annealing on the flat steel product before hot-dip coating. With regard to the adhesion of the Zn coating on the steel substrate, it is particularly favorable if the Mn mixed oxide layer essentially completely covers the surface of the flat steel product after annealing. In the context of the invention, the Mn mixed oxide layer is defined as MnO·Fe metal . This means that metallic iron is present in this Mn mixed oxide layer and not oxidized iron, as is the case in the prior art.
Erfindungsgemäß wird also über mindestens eine Glühstufe gezielt eine Mn-Mischoxidschicht eingestellt, indem die Glühung (Arbeitsschritt b)) unter einer für FeO reduzierenden und einer für Mn oxidierenden Atmosphäre durchgeführt wird.According to the invention, an Mn mixed oxide layer is set in a targeted manner via at least one annealing stage, in that the annealing (step b)) is carried out under an atmosphere that reduces FeO and an atmosphere that oxidizes Mn.
Überraschend hat sich gezeigt, dass auf diese Weise ein Stahlflachprodukt erhalten wird, das eine gute Benetzung bei der anschließend durchgeführten Schmelztauchbeschichtung sicherstellt. Ebenso bildet die auf dem Stahlsubstrat erfindungsgemäß erzeugte Schicht aus Mn-Mischoxiden einen Haftgrund, auf dem die anschließend aufgebrachte Zinkschicht überraschender Weise besonders sicher haftet. Im Gegensatz zum in der
Anschließend wird das auf die Badeintrittstemperatur abgekühlte Stahlflachprodukt innerhalb einer Tauchzeit von 0,1 - 10 Sekunden, insbesondere 0,1 - 5 s, durch ein an Eisen gesättigtes, 420 - 520 °C heißes Zn-Schmelzenbad geleitet, das aus dem Hauptbestandteil Zink und unvermeidbaren Verunreinigungen sowie 0,05 - 8 Gew.-% Al und/ bis zu 8 Gew.-% Mg, insbesondere 0,05 - 5 Gew.-% Al und bis zu 5 % Gew.-% Mg, besteht. Zusätzlich sind in dem Schmelzenbad optional Si < 2 %, Pb < 0,1 %, Ti < 0,2 %, Ni < 1 %, Cu < 1 %, Co < 0,3 %, Mn < 0,5 %, Cr < 0,2 %, Sr < 0,5 %, Fe < 3 %, B < 0,1 %, Bi < 0,1 %, Cd < 0,1 % vorhanden, um in an sich bekannter Weise bestimmte Eigenschaften des Überzugs einzustellen.The flat steel product, which has been cooled to the bath inlet temperature, is then passed through an iron-saturated, 420 - 520 °C hot Zn molten bath within an immersion time of 0.1 - 10 seconds, in particular 0.1 - 5 s, which consists of the main component zinc and zinc unavoidable impurities and 0.05-8% by weight Al and/up to 8% by weight Mg, in particular 0.05-5% by weight Al and up to 5% by weight Mg. In addition, in the molten bath optionally Si < 2%, Pb < 0.1%, Ti < 0.2%, Ni < 1%, Cu < 1%, Co < 0.3%, Mn < 0.5%, Cr < 0.2%, Sr < 0.5%, Fe < 3%, B < 0.1%, Bi < 0.1%, Cd < 0.1% present in order to determine certain properties of the coating in a manner known per se set.
Das so erhaltene, mit einem vor Korrosion schützenden Zn-Schutzüberzug schmelztauchbeschichtete Stahlflachprodukt wird schließlich abgekühlt, wobei vor dem Abkühlen noch in an sich bekannter Weise die Dicke des Überzugs eingestellt werden kann.The flat steel product obtained in this way, which is hot-dip coated with a Zn protective coating to protect against corrosion, is finally cooled, it being possible for the thickness of the coating to be adjusted in a manner known per se before cooling.
Der erfindungsgemäße Zn-Überzug enthält notwendig Al-Gehalte von 0,05 - 8 Gew.-% und zusätzlich Gehalte an bis zu 8 Gew.-% Mg, wobei die Obergrenze der Gehalte beider Elemente in der Praxis typischerweise auf maximal 5 Gew.-% beschränkt ist.The Zn coating according to the invention necessarily contains Al contents of 0.05-8% by weight and additional contents of up to 8% by weight Mg, with the upper limit of the contents of both elements being typically limited to a maximum of 5% by weight in practice. % is limited.
Ein erfindungsgemäßes Stahlflachprodukt mit einem Mn-Gehalt von 6 - 35 Gew.-% und einem vor Korrosion schützenden Zn-Schutzüberzug ist dementsprechend dadurch gekennzeichnet, dass der Zn-Schutzüberzug eine auf dem Stahlflachprodukt im Wesentlichen deckende und haftende Mn-Mischoxidschicht, in der metallisches Eisen vorliegt, und eine das Stahlflachprodukt und die auf ihm haftende Mn-Mischoxidschicht gegenüber der Umgebung abschirmende Zn-Schicht aufweist.A flat steel product according to the invention with an Mn content of 6-35% by weight and a Zn protective coating that protects against corrosion is accordingly characterized in that the Zn protective coating has a Mn mixed oxide layer that essentially covers and adheres to the flat steel product, in which metallic Iron is present, and has a Zn layer that shields the flat steel product and the Mn mixed oxide layer adhering to it from the environment.
Eine besonders gute Haftung der Zinkschicht auf dem Stahlsubstrat ergibt sich dann, wenn der Zn-Schutzüberzug eine zwischen der Mn-Mischoxidschicht und der Zn-Schicht angeordnete Fe(Mn)2Al5-Schicht umfasst. Diese entsteht dann, wenn in dem Schmelzenbad eine ausreichende Menge an Aluminium von 0,05 - 5 Gew.-% Al vorhanden ist. Die Fe(Mn)2Al5-Schicht bildet dabei eine Sperrschicht, durch die die Reduktion der Mn-Mischoxidschicht beim Schmelztauchen sicher verhindert wird. In Abhängigkeit vom insbesondere zwischen 0,05 - 0,15 Gew.-% liegenden Al-Gehalt kann sich die Sperrschicht in FeZn-Phasen umwandeln, wobei die Mn-Oxidschicht dennoch erhalten bleibt.A particularly good adhesion of the zinc layer on the steel substrate results when the Zn protective coating comprises an Fe(Mn) 2 Al 5 layer arranged between the Mn mixed oxide layer and the Zn layer. This occurs when there is a sufficient quantity of aluminum of 0.05 - 5% by weight Al in the molten bath. The Fe (Mn) 2 Al 5 layer forms a barrier layer through which the reduction of the Mn mixed oxide layer melt dipping is reliably prevented. Depending on the Al content, which is in particular between 0.05 and 0.15% by weight, the barrier layer can transform into FeZn phases, with the Mn oxide layer nevertheless being retained.
Die MnO-Schicht und die Fe(Mn)2Al5-Schicht eines erfindungsgemäß erzeugten und beschaffenen Überzugs stellen somit auch nach dem Schmelztauchbeschichten noch sicher, dass die außen liegende Zn-Schicht unter hohen Verformungsgraden fest auf dem Stahlsubstrat haftet.The MnO layer and the Fe(Mn) 2 Al 5 layer of a coating produced and configured according to the invention thus ensure, even after hot-dip coating, that the outer Zn layer adheres firmly to the steel substrate with high degrees of deformation.
Jedoch wirkt sich die erfindungsgemäße Anwesenheit einer Mn-Mischoxidschicht auf der Oberfläche des Stahlsubstrats nicht nur dann positiv aus, wenn sich zusätzlich die Fe(Mn)2Al5-Schicht bildet, sondern auch dann, wenn in dem Schmelzenbad Magnesium alternativ oder ergänzend zu Aluminium in wirksamen Gehalten vorhanden ist. Auch bei Erzeugung einer ZnMg-Überzugsschicht auf dem Stahlsubstrat stellt die erfindungsgemäß erzeugte MnO-Schicht eine besonders gute und gleichmäßige Benetzung des Stahlflachproduktes bei gleichzeitig optimaler Haftung und minimiertem Risiko einer Rissbildung oder Abplatzung auch bei hohen Umformgraden sicher.However, the presence of a Mn mixed oxide layer on the surface of the steel substrate according to the invention not only has a positive effect if the Fe(Mn) 2 Al 5 layer is also formed, but also if magnesium is used as an alternative or in addition to aluminum in the molten bath is present in effective levels. Even when a ZnMg coating layer is produced on the steel substrate, the MnO layer produced according to the invention ensures particularly good and uniform wetting of the steel flat product with optimum adhesion and minimized risk of cracking or flaking even with high degrees of deformation.
Eine besonders praxisgerechte Ausgestaltung der Erfindung ergibt sich in diesem Zusammenhang, wenn für das Verhältnis des Al-Gehalts %Al und des Mg-Gehalts %Mg gilt: %Al/%Mg < 1. Bei dieser Ausgestaltung der Erfindung ist also der Al-Gehalt des Schmelzenbades stets kleiner als dessen Mg-Gehalt. Dies hat den Vorteil, dass die erfindungsgemäß angestrebte Grenzschichtbildung auch ohne eine besondere Glühschrittfolge im Rahmen des erfindungsgemäßen Verfahrens zu einer Erhöhung des metallischen Eisens in der Mischoxidschicht führt. Magnesium zeichnet sich dabei durch ein höheres Reduktionspotential auf MnO als Aluminium aus. Deshalb erfolgt bei Anwesenheit von höheren Mg-Gehalten in der Schmelzschicht eine forcierte Auflösung des MnO-Gerüsts der Mischoxidschicht. Da das Mischoxid starker aufgelöst wird, steht effektiv mehr metallisches Eisen "Femetall" aus der "Tiefe" der Mischoxidschicht an der Reaktionsfront Mischoxidschicht/Zinkbad zur Verfügung, so dass sich die deckende Fe(Mn)2Al5-Grenzschicht als Haftvermittler besonders effektiv ausbilden kann. Dementsprechend trägt die MnO-Reduktion durch gelöstes Magensium in-situ mit besonders hoher Wirksamkeit zur erfindungsgemäß angestrebten, die besonders gute Haftung des Zn-Überzuges gewährleistenden Grenzschichtbildung bei.A particularly practical embodiment of the invention results in this connection when the following applies to the ratio of the Al content %Al and the Mg content %Mg: %Al/%Mg<1. In this embodiment of the invention, the Al content is therefore of the melt bath is always smaller than its Mg content. This has the advantage that the boundary layer formation aimed at according to the invention leads to an increase in the metallic iron in the mixed oxide layer even without a special sequence of annealing steps in the context of the method according to the invention. Magnesium is characterized by a higher reduction potential to MnO than aluminum. Therefore, when higher Mg contents are present in the melted layer, there is a forced dissolution of the MnO structure of the mixed oxide layer. Since the mixed oxide is dissolved to a greater extent, more metallic iron "Fe metal " from the "depth" of the mixed oxide layer is effectively available at the mixed oxide layer/zinc bath reaction front, so that the covering Fe(Mn) 2 Al 5 boundary layer is particularly effective as an adhesion promoter can train. Accordingly, the MnO reduction by dissolved magnesium in situ contributes with a particularly high degree of effectiveness to the boundary layer formation that is aimed at according to the invention and ensures particularly good adhesion of the Zn coating.
Der zur Vorbereitung des Schmelztauchbeschichtens im Rahmen des erfindungsgemäßen Verfahrens durchgeführte Glühschritt (Arbeitsschritt b)) kann ein- oder mehrstufig durchgeführt werden. Im Fall, dass die Glühung einstufig durchgeführt wird, sind in Abhängigkeit vom Taupunkt verschiedene Wasserstoffgehalte in der Glühatmosphäre möglich. Liegt der Taupunkt im Bereich von -50 °C bis +20 °C kann die Glühatmosphäre mindestens 0,01 Vol.-% H2, jedoch weniger als 3 Vol.-% H2 enthalten. Wird dagegen ein Taupunkt von mindestens +20 °C bis einschließlich + 60 °C eingestellt, sollte der Wasserstoffgehalt im Bereich von 3 % bis 85 % liegen, damit die Atmosphäre reduzierend für Eisen wirkt. Unter Berücksichtigung der anderen während der Durchführung des erfindungsgemäßen Glühschritts zu berücksichtigenden Parameter wird so die reduzierende Wirkung in Bezug auf das gegebenenfalls vorhandene FeO und die oxidierende Wirkung in Bezug auf das im Stahlsubstrat vorhandene Mn sicher erreicht.The annealing step (work step b)) carried out in preparation for the hot-dip coating in the context of the process according to the invention can be carried out in one or more stages. If the annealing is carried out in one stage, different hydrogen contents are possible in the annealing atmosphere depending on the dew point. If the dew point is in the range from -50 °C to +20 °C, the annealing atmosphere can contain at least 0.01% by volume H 2 , but less than 3% by volume H 2 . If, on the other hand, a dew point of at least +20 °C up to and including + 60 °C is set, the hydrogen content should be in the range of 3% to 85% so that the atmosphere has a reducing effect on iron. Taking into account the other parameters to be taken into account during the implementation of the annealing step according to the invention, the reducing effect on the FeO that may be present and the oxidizing effect on the Mn present in the steel substrate are thus reliably achieved.
Soll dagegen das Stahlflachprodukt vor dem Eintritt in das Schmelzenbad in zwei Stufen geglüht werden, so kann dazu dem erfindungsgemäß durchgeführten Glühschritt (Arbeitsschritt b) von Anspruch 1) ein zusätzlicher Glühschritt vorgeschaltet werden, bei dem das Stahlflachprodukt bei einer Glühtemperatur von 200 - 1100 °C für eine Glühdauer von 0,1 - 60 s unter einer für sowohl Fe als auch für Mn oxidativen Atmosphäre gehalten wird, die 0,0001 - 5 Vol.-% H2 sowie optional 200 - 5500 Vol.-ppm O2 enthält und einen im Bereich von -60 °C bis +60 °C liegenden Taupunkt besitzt. Anschließend wird dann der erfindungsgemäße Glühschritt bei einem Taupunkt im Bereich von -50 °C bis +20 °C in einer 0,01 - 85 % Wasserstoff enthaltenden Atmosphäre unter Berücksichtigung der anderen während der Durchführung des erfindungsgemäßen Glühschritts zu berücksichtigenden Parameter durchgeführt, bevor das Stahlflachprodukt in das Schmelzenbad geleitet wird.If, on the other hand, the flat steel product is to be annealed in two stages before entering the molten bath, an additional annealing step can be carried out before the annealing step (work step b) of claim 1) carried out according to the invention, in which the flat steel product is heated to an annealing temperature of 200 - 1100 °C is maintained for an annealing period of 0.1-60 s under an atmosphere oxidative for both Fe and Mn, containing 0.0001-5 vol.% H 2 and optionally 200-5500 vol.ppm O 2 and a has a dew point in the range of -60 °C to +60 °C. The annealing step according to the invention is then carried out at a dew point in the range from -50 °C to +20 °C in an atmosphere containing 0.01-85% hydrogen, taking into account the other parameters to be taken into account when carrying out the annealing step according to the invention, before the steel flat product into the melt bath.
Optimale Haftungseigenschaften des Zn-Überzuges werden bei einem erfindungsgemäß erzeugten Überzug erreicht, wenn die Dicke der nach dem Glühen (Arbeitsschritt b)) erhaltenen Mn-Mischoxidschicht 40 - 400 nm, insbesondere bis zu 200 nm, beträgt.Optimum adhesion properties of the Zn coating are achieved with a coating produced according to the invention when the thickness of the Mn mixed oxide layer obtained after annealing (step b)) is 40-400 nm, in particular up to 200 nm.
Ebenso trägt es zur Optimierung des Verformungsverhaltens eines erfindungsgemäß erzeugten Stahlflachproduktes bei, wenn das mit der Mn-Mischoxidschicht versehene Stahlflachprodukt vor dem Eintritt in das Schmelzenbad einer Überalterungsbehandlung unterzogen wird.It also contributes to optimizing the deformation behavior of a flat steel product produced according to the invention if the flat steel product provided with the Mn mixed oxide layer is subjected to an overaging treatment before it enters the molten bath.
Nachfolgend wird die Erfindung von Ausführungsbeispielen näher erläutert. Es zeigen:
- Fig. 1
- ein mit einem Al-haltigen Zn-Überzug versehenes Stahlflachprodukt in einer schematischen Schnittdarstellung;
- Fig. 2
- einen Schrägschliff einer Probe eines mit einem Zn-Überzugs versehenen Stahlflachprodukts;
- Fig. 3
- ein mit einem ZnMg-Überzug versehenes Stahlflachprodukt in einer schematischen Schnittdarstellung;
- Fig. 4
- einen Schrägschliff einer Probe eines mit einem ZnMg-Überzugs versehenen Stahlflachprodukts.
- 1
- a flat steel product provided with an Al-containing Zn coating in a schematic sectional view;
- 2
- a bevel section of a sample of a Zn-coated steel flat product;
- 3
- a flat steel product provided with a ZnMg coating in a schematic sectional view;
- 4
- a bevel section of a sample of a ZnMg-coated steel flat product.
Aus einem hoch manganhaltigen Stahl mit der in Tabelle 1 angegebenen Zusammensetzung ist in bekannter Weise ein kaltgewalztes Stahlband erzeugt worden.
Eine erste Probe des kaltgewalzten Stahlbands ist daraufhin in einem einstufig durchgeführten Glühprozess geglüht worden.A first sample of the cold-rolled steel strip was then annealed in a single-stage annealing process.
Dazu ist die Stahlband-Probe mit einer Erwärmungsrate von 10 K/s auf eine Glühtemperatur Tg von 800 °C aufgeheizt worden, bei der die Probe dann für 30 Sekunden gehalten worden ist. Die Glühung erfolgte dabei unter einer Glühatmosphäre, die zu 5 Vol.-% H2 und zu 95 Vol.-% aus N2 bestand und deren Taupunkt bei +25 °C lag. Anschließend ist das geglühte Stahlband mit einer Abkühlrate von 20 K/s auf eine Badeintrittstemperatur von 480 °C abgekühlt worden, bei der es zunächst für 20 Sekunden einer Überalterungsbehandlung unterzogen worden ist. Die Überalterungsbehandlung fand dabei unter der unveränderten Glühatmosphäre statt. Ohne die Glühatmosphäre zu verlassen, ist das Stahlband daraufhin in ein 460 °C heißes, an Fe gesättigtes Zink-Schmelzenbad geleitet worden, das neben Zn, unvermeidbaren Verunreinigungen und Fe zusätzlich 0,23 Gew.-% Al enthielt. Nach einer Tauchzeit von 2 Sekunden ist das nun schmelztauchbeschichtete Stahlband aus dem Schmelzbad herausgeleitet und auf Raumtemperatur abgekühlt worden.For this purpose, the steel strip sample was heated at a heating rate of 10 K/s to an annealing temperature Tg of 800° C., at which the sample was then held for 30 seconds. The annealing took place under an annealing atmosphere which consisted of 5% by volume H 2 and 95% by volume N 2 and whose dew point was +25°C. The annealed steel strip was then cooled at a cooling rate of 20 K/s to a bath inlet temperature of 480° C., at which point it was initially subjected to an overaging treatment for 20 seconds. The overaging treatment took place under the unchanged annealing atmosphere. Without leaving the annealing atmosphere, the steel strip was then fed into a 460 °C hot, Fe-saturated molten zinc bath which, in addition to Zn, unavoidable impurities and Fe, also contained 0.23% by weight Al. After an immersion time of 2 seconds, the steel strip, which is now hot-dip coated, was removed from the molten bath and cooled to room temperature.
In einem zweiten Versuch ist eine zweite Probe des gemäß Tabelle 1 zusammengesetzten kaltgewalzten Stahlbands in einem ebenfalls kontinuierlich durchlaufenen Verfahrensablauf in einem zweistufigen Prozess geglüht und anschließend schmelztauchbeschichtet worden.In a second test, a second sample of the cold-rolled steel strip composed according to Table 1 was annealed in a two-stage process in a process sequence that also ran continuously and was then hot-dip coated.
Dazu ist das Stahlband zunächst mit einer Heizrate von 10 K/s auf 600 °C erwärmt und bei dieser Glühtemperatur für 10 Sekunden gehalten worden. Die Glühatmosphäre enthielt dabei 2000 ppm O2 und als Rest N2. Ihr Taupunkt lag bei -30 °C.For this purpose, the steel strip was first heated to 600 °C at a heating rate of 10 K/s and held at this annealing temperature for 10 seconds. The annealing atmosphere contained 2000 ppm O 2 and the remainder N 2 . Her dew point was -30 °C.
In unmittelbarem Anschluss daran ist das Stahlband in einem zweiten Glühschritt auf eine 800 °C betragende Glühtemperatur Tg erwärmt worden, bei der es für 30 Sekunden unter einer 5 Vol.-% H2, Rest N2 enthaltenden Glühatmosphäre gehalten worden ist, deren Taupunkt bei -30 °C lag. Darauf ist das Stahlband nach wie vor unter der Glühatmosphäre mit einer ca. 20 K/s betragenden Abkühltemperatur auf 480 °C abgekühlt und für 20 Sekunden einer Überalterungsbehandlung unterzogen worden. Im Anschluss daran ist das Stahlband mit einer Badeintrittstemperatur von 480 °C in ein 460 °C heißes, an Fe gesättigtes Schmelzenbad geleitet worden, das wiederum 0,23 Gew.-% Al sowie andere Elemente in unwirksamen Verunreinigungsspuren und als Rest Zink enthielt. Nach einer Tauchzeit von 2 Sekunden ist das fertig schmelztauchbeschichtete Stahlflachprodukt dann aus dem Schmelzenbad herausgeleitet und auf Raumtemperatur abgekühlt worden.Immediately afterwards, the steel strip was heated in a second annealing step to an annealing temperature Tg of 800 °C, at which it was held for 30 seconds under an annealing atmosphere containing 5 vol -30 °C. The steel strip was then cooled to 480° C. under the annealing atmosphere at a cooling temperature of approx. 20 K/s and subjected to an overaging treatment for 20 seconds. The steel strip was then fed with a bath inlet temperature of 480 °C into a 460 °C hot melt bath saturated with Fe, which in turn contained 0.23% by weight Al and other elements in ineffective traces of impurities and the remainder zinc. After an immersion time of 2 seconds, the finished hot-dip coated flat steel product was then removed from the melt bath and cooled to room temperature.
In
In
Zur Überprüfung des Erfolgs der erfindungsgemäßen Verfahrensweise sind zwanzig zusätzliche Versuche 1 - 20 durchgeführt worden, bei denen das Schmelzenbad neben Zn und unvermeidbaren Verunreinigungen jeweils 0,23 Gew.-% Al enthielt. An den so erhaltenen Proben sind jeweils der Benetzungsgrad und die Zinkhaftung visuell untersucht worden. Als Prüfprinzip ist der Kerbschlagtest gemäß SEP 1931 angewendet worden. Die Versuchsparameter und Ergebnisse dieser Versuche sind in Tabelle 2 angegeben.To check the success of the procedure according to the invention, twenty additional tests 1-20 were carried out in which the molten bath contained 0.23% by weight Al in addition to Zn and unavoidable impurities. The degree of wetting and the zinc adhesion were examined visually on the samples obtained in this way. The notched-bar impact test according to SEP 1931 was used as the test principle. The test parameters and results of these tests are given in Table 2.
Darüber hinaus sind weitere sechzehn Versuche 21 - 36 durchgeführt worden, bei denen das Schmelzenbad neben Zn und unvermeidbaren Verunreinigungen 0,11 Gew.-% Al enthielt. Gegenüber der im oben erläuterten Versuch aufgezeigten, als Fe(Mn)2Al5-Schicht ausgebildeten Sperrschicht stellte sich bei diesem niedrigeren Al-Gehalt des Schmelzenbads eine FeMnZn-Sperrschicht ein. An den so erhaltenen Proben sind ebenfalls jeweils der Benetzungsgrad und die Zinkhaftung untersucht worden. Die Versuchsparameter und Ergebnisse dieser Versuche sind in Tabelle 3 angegeben.In addition, a further sixteen tests 21 - 36 were carried out, in which the molten bath contained 0.11% by weight Al in addition to Zn and unavoidable impurities. Compared to the barrier layer shown in the experiment explained above, which was designed as an Fe(Mn) 2 Al 5 layer, an FeMnZn barrier layer formed with this lower Al content of the melt bath. The degree of wetting and the zinc adhesion were also examined on the samples obtained in this way. The test parameters and results of these tests are given in Table 3.
Auf Grundlage weiterer Proben des aus dem gemäß Tabelle 1 zusammengesetzten Stahl kaltgewalzten hochmanganghaltigen Stahlbands ist der Einfluss des Taupunkts der jeweiligen Glühatmosphäre auf das Beschichtungsergebnis untersucht worden. Die Proben sind dazu jeweils einem Glühprozess unterzogen worden, bei dem sie ebenfalls mit einer Erwärmungsrate von 10 K/s auf eine Glühtemperatur Tg von 800 °C aufgeheizt worden sind. Auf dieser Glühtemperatur sind die Probe dann für 60 Sekunden gehalten worden ist. Die Glühung erfolgte jeweils unter einer Glühatmosphäre, die jeweils zu 5 Vol.-% H2 und zu 95 Vol.-% aus N2 bestand, wobei der jeweilige Taupunkt der Glühatmosphäre zwischen -55 °C und +45 °C variiert worden ist.On the basis of further samples of the high-manganese steel strip cold-rolled from the steel composed according to Table 1, the influence of the dew point of the respective annealing atmosphere on the coating result was examined. For this purpose, the samples were each subjected to an annealing process in which they were also heated to an annealing temperature Tg of 800 °C at a heating rate of 10 K/s. The sample was then held at this annealing temperature for 60 seconds. The annealing took place in each case under an annealing atmosphere that consisted of 5% by volume H 2 and 95% by volume N 2 , the respective dew point of the annealing atmosphere being varied between −55° C. and +45° C.
Nach der Wärmebehandlung ist das geglühte Stahlband wie bei der voranstehend beschriebenen Versuchsserie mit einer Abkühlrate von 20 K/s auf eine Badeintrittstemperatur von 480 °C abgekühlt worden, bei der es zunächst für 20 Sekunden einer Überalterungsbehandlung unterzogen worden ist. Die Überalterungsbehandlung fand dabei unter der unveränderten Glühatmosphäre statt. Ohne die Glühatmosphäre zu verlassen, ist das Stahlband daraufhin in ein 460 °C heißes, an Fe gesättigtes Zink-Schmelzenbad geleitet worden, das neben Zn, unvermeidbaren Verunreinigungen und Fe zusätzlich jeweils in Kombination 0,4 Gew.-% Al und 1,0 Gew.-% Mg oder alleine 0,14 Gew.-%, 0,17 Gew.-% oder 0,23 Gew.-% Al enthielt. Nach einer Tauchzeit von 2 Sekunden ist das nun schmelztauchbeschichtete Stahlband aus dem Schmelzbad herausgeleitet und auf Raumtemperatur abgekühlt worden.After the heat treatment, the annealed steel strip was cooled at a cooling rate of 20 K/s to a bath inlet temperature of 480° C., as in the test series described above, at which point it was initially subjected to an overaging treatment for 20 seconds. The overaging treatment took place under the unchanged annealing atmosphere. Without leaving the annealing atmosphere, the steel strip was then fed into a 460 °C hot, Fe-saturated molten zinc bath which, in addition to Zn, unavoidable impurities and Fe, also contained a combination of 0.4% by weight Al and 1.0 wt% Mg or alone 0.14 wt%, 0.17 wt% or 0.23 wt% Al. After an immersion time of 2 seconds, the steel strip, which is now hot-dip coated, was removed from the molten bath and cooled to room temperature.
In
In
Neben der bereits erwähnten Variation der Taupunkte der Glühatmosphäre sind bei zur Überprüfung des Erfolgs der erfindungsgemäßen Verfahrensweise durchgeführten einundzwanzig Versuchen 37 - 57 die Al- und Mg-Gehalte des Schmelzenbades variiert worden. An den so erhaltenen Proben sind jeweils der Benetzungsgrad und die Zinkhaftung visuell untersucht worden. Als Prüfprinzip ist auch hier der Kerbschlagtest gemäß SEP 1931 angewendet worden. Die Versuchsparameter und Ergebnisse dieser Versuche sind in Tabelle 4 angegeben.In addition to the already mentioned variation of the dew points of the annealing atmosphere, the Al and Mg contents of the melt bath were varied in twenty-one tests 37-57 carried out to check the success of the procedure according to the invention. The degree of wetting and the zinc adhesion were examined visually on the samples obtained in this way. The notched-bar impact test according to SEP 1931 was also used here as the test principle. The test parameters and results of these tests are given in Table 4.
Es zeigt sich, dass bei kombinierter Anwesenheit von Al und Mg und einer Einstellung des Taupunkts auf den Bereich von -50 °C bis +60 °C auch im einstufig erfolgenden Glühprozess zuverlässig auf hochmanganhaltigen Stahlsubstraten zinkbasierte Überzüge erzeugen lassen.It has been shown that with the combined presence of Al and Mg and an adjustment of the dew point to the range from -50 °C to +60 °C, zinc-based coatings can also be reliably produced on high-manganese steel substrates in a single-stage annealing process.
Zum Vergleich sind aus einem kaltgewalzten Stahlband, das aus einem Al-TRIP-Stahl VS1 bestand, und einem Stahlband, das aus einem ebenfalls kaltgewalzten Si-TRIP-Stahl VS2 bestand, weitere jeweils drei Proben V1-V3 und V4 - V6 gewonnen worden. Die Zusammensetzung der Stähle VS1 und VS2 sind in Tabelle 5 angegeben.
Auch die Vergleichsproben V1-V6 sind in der für die erfindungsgemäßen Proben voranstehend beschriebenen Weise wärmebehandelt worden, bevor sie im Schmelzenbad schmelztauchbeschichtet worden sind. Das Schmelzenbad enthielt dabei neben Zn und unvermeidbaren Verunreinigungen jeweils 0,4 Gew.-% Al und 1 Gew.-% Mg. An den so beschichteten Proben V1 - V6 sind ebenfalls jeweils der Benetzungsgrad und die Zinkhaftung untersucht worden. Die Versuchsparameter und Ergebnisse dieser Versuche sind in Tabelle 6 aufgelistet. Es zeigt sich, dass aufgrund der niedrigeren Mangan-Gehalte der Stähle VS1 und VS2 sich keine MnO-Struktur in der Mischoxidationsschicht an der Oberfläche des Stahlsubstrats bildet. Infolgedessen bildet sich auch keine deckende Fe(Mn)2-Schicht als Haftvermittler. Als Resultat kommt es im Schmelzenbad zu keiner ausreichenden MnO-Reduktion durch gelöstes Magnesium, so dass bei den Vergleichsproben auch keine ausreichende Benetzung und dementsprechend auch keine ausreichende Haftung der Beschichtung erzielt werden kann.
Claims (11)
- Method for hot-dip coating a flat steel product, consisting of (in % wt.) C: ≤1.6 %, Mn: 6 - 35 %, Al: ≤ 10 %, Ni: ≤ 10 %, Cr: ≤10 %, Si: ≤ 10 %, Cu: ≤ 3 %, Nb: ≤ 0.6 %, Ti: ≤ 0.3 %, V: ≤ 0.3 %, P: ≤ 0.1 %, B: ≤ 0.01 %, Mo: ≤ 0.3 %, N: ≤ 1.0 % and the remainder iron and unavoidable impurities, with zinc or a zinc alloy, comprising the following production steps:a) providing the flat steel product;b) annealing the flat steel product- at an annealing temperature Tg of 600 - 1100 °C,- for an annealing duration of 10 - 240 s under an annealing atmosphere having a reducing effect in relation to the FeO present on the flat steel product and having an oxidising effect in relation to the Mn contained in the steel substrate, this annealing atmosphere containing 0.01 - 85 % vol. H2, H2O and N2 and technically induced unavoidable impurities as the remainder and having a dew point which is between -50 °C and +60 °C, wherein for the H2O/H2 ratio the following applies:- so that a 20 - 400 nm thick Mn mixed oxide layer is formed on the steel flat product, covering the steel flat product at least in sections;c) cooling the annealed flat steel product down to a bath entry temperature;d) passing the flat steel product, cooled down to the bath entry temperature, through a 420 - 520 °C hot Zn molten bath saturated with iron within a dipping time of 0.1 - 10 s, so that the flat steel product is hot-dip coated with a Zn protective coating which protects against corrosion, wherein the Zn molten bath consists of the main constituent zinc and unavoidable impurities, as well as 0.05 - 8 % wt. Al and up to 8 % wt. Mg, as well as optionally Si < 2 %, Pb < 0.1 %, Ti < 0.2 %, Ni < 1 %, Cu < 1 %, Co < 0.3 %, Mn < 0.5 %, Cr < 0.2 %, Sr < 0.5 %, Fe < 3 %, B < 0.1 %, Bi < 0.1 %, Cd < 0.1 %;e) cooling the flat steel product flowing out of the molten bath and provided with the Zn coating.
- Method according to Claim 1, characterised in that the flat steel product is provided as a cold-rolled steel strip.
- Method according to either of Claims 1 and 2, characterised in that upstream of the annealing (production step b)) an annealing step is inserted in which the flat steel product is held at an annealing temperature of 200 - 1100 °C for an annealing duration of 0.1 - 60 s under an atmosphere which is oxidative for Fe and Mn, contains 0.0001 - 5 % vol. H2 and optionally 200 - 5500 vol. ppm O2 and has a dew point in the range from -60 °C to +60 °C.
- Method according to any one of the preceding claims, characterised in that the dipping time in the Zn molten bath is 0.1 - 5 s.
- Method according to Claim 1, characterised in that the Al content is in each case less than the Mg content of the molten bath.
- Method according to any one of the preceding claims, characterised in that the temperature of the flat steel product when it enters the molten bath is 360 - 710 °C.
- Flat steel product having a steel substrate, which consists of (in % wt.) C: ≤ 1.6 %, Mn: 6 - 35 %, Al: ≤ 10 %, Ni: ≤ 10 %, Cr: ≤10 %, Si: ≤ 10 %, Cu: ≤ 3 %, Nb: ≤ 0.6 %, Ti: ≤ 0.3 %, V: ≤ 0.3 %, P: ≤ 0.1 %, B: ≤ 0.01 %, Mo: ≤ 0.3 %, N: ≤ 1.0 % and the remainder iron and unavoidable impurities, and a Zn protective coating which protects against corrosion and is formed from zinc or a zinc alloy, characterised in that the Zn protective coating has a Mn mixed oxide layer consisting of MnO Femetal, which essentially covers the flat steel product and adheres to the flat steel product, and has a Zn layer shielding the flat steel product and the MnO Femetal layer adhering to it from the environment.
- Flat steel product according to Claim 7, characterised in that the Zn protective coating comprises an Fe(Mn)2Al5 layer arranged between the MnO Femetal layer and the Zn layer.
- Flat steel product according to either of Claims 7 or 8, characterised in that the Zn protective coating comprises an FeMnZn layer which lies between the MnO Femetal layer and the Zn layer.
- Flat steel product according to any one of Claims 7 to 9, characterised in that the Zn protective layer is formed as a ZnMg alloy coating.
- Flat steel product according to any one of Claims 7 to 10, characterised in that it is produced according to the method according to any one of Claims 1 to 6.
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PCT/EP2010/055334 WO2010122097A1 (en) | 2009-04-23 | 2010-04-22 | Method for hot-dip coating a flat steel product containing 2-35 wt% mn and flat steel product |
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EP10717595.2A Active EP2432910B2 (en) | 2009-04-23 | 2010-04-22 | Method for hot-dip coating a flat steel product containing 2-35 wt% mn and flat steel product |
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US (1) | US9611527B2 (en) |
EP (1) | EP2432910B2 (en) |
JP (1) | JP5834002B2 (en) |
KR (1) | KR101679006B1 (en) |
CN (1) | CN102421928B (en) |
AU (2) | AU2010240903A1 (en) |
BR (1) | BRPI1016179B1 (en) |
CA (1) | CA2759369C (en) |
DE (1) | DE102009018577B3 (en) |
ES (1) | ES2717878T3 (en) |
PL (1) | PL2432910T3 (en) |
TR (1) | TR201906585T4 (en) |
WO (1) | WO2010122097A1 (en) |
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Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE2522485A1 (en) † | 1974-05-24 | 1975-12-04 | Armco Steel Corp | PROCESS FOR IMPROVING THE WETTABILITY OF THE SURFACE OF A LOW-ALLOY STEEL STRIP AND SHEET METAL BY A MOLTEN COVERING METAL |
BE1011131A6 (en) † | 1997-04-28 | 1999-05-04 | Centre Rech Metallurgique | Method of coating a steel strip by hot-dip galvanising |
WO2006002843A1 (en) † | 2004-06-29 | 2006-01-12 | Corus Staal Bv | Steel sheet with hot dip galvanized zinc alloy coating and process to produce it |
DE102004059566B3 (en) † | 2004-12-09 | 2006-08-03 | Thyssenkrupp Steel Ag | Process for hot dip coating a strip of high strength steel |
JP2007211279A (en) † | 2006-02-08 | 2007-08-23 | Nippon Steel Corp | Ultrahigh strength steel sheet having excellent hydrogen brittleness resistance, method for producing the same, method for producing ultrahigh strength hot dip galvanized steel sheet and method for producing ultrahigh strength hot dip alloyed galvanized steel sheet |
WO2007109865A1 (en) † | 2006-03-29 | 2007-10-04 | Centre De Recherches Metallurgiques Asbl-Centrum Voor Research In De Metallurgie Vzw | Method for continuously annealing and preparing strip of high-strength steel for the purpose of hot-dip galvanizing it |
CN100368580C (en) † | 2003-04-10 | 2008-02-13 | 新日本制铁株式会社 | High strength hot dip galvanized steel sheet, and its production method |
WO2008022980A2 (en) † | 2006-08-22 | 2008-02-28 | Thyssenkrupp Steel Ag | Process for coating a hot- or cold-rolled steel strip containing 6 - 30% by weight of mn with a metallic protective layer |
JP2008156734A (en) † | 2006-12-26 | 2008-07-10 | Jfe Steel Kk | High-strength hot-dip galvanized steel sheet and its manufacturing method |
WO2008102009A1 (en) † | 2007-02-23 | 2008-08-28 | Corus Staal Bv | Cold rolled and continuously annealed high strength steel strip and method for producing said steel |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH07316764A (en) | 1994-05-31 | 1995-12-05 | Sumitomo Metal Ind Ltd | Production of galvannealed steel sheet |
DE19727759C2 (en) | 1997-07-01 | 2000-05-18 | Max Planck Inst Eisenforschung | Use of a lightweight steel |
DE19900199A1 (en) | 1999-01-06 | 2000-07-13 | Ralf Uebachs | High strength light constructional steel for pre-stressed concrete reinforcements or automobile body components has high manganese and aluminum contents |
JP2003193213A (en) | 2001-12-21 | 2003-07-09 | Kobe Steel Ltd | Hot dip galvanized steel sheet and galvannealed steel sheet |
DE10259230B4 (en) | 2002-12-17 | 2005-04-14 | Thyssenkrupp Stahl Ag | Method for producing a steel product |
FR2876711B1 (en) | 2004-10-20 | 2006-12-08 | Usinor Sa | HOT-TEMPERATURE COATING PROCESS IN ZINC BATH OF CARBON-MANGANESE STEEL BANDS |
FR2876708B1 (en) | 2004-10-20 | 2006-12-08 | Usinor Sa | PROCESS FOR MANUFACTURING COLD-ROLLED CARBON-MANGANESE AUSTENITIC STEEL TILES WITH HIGH CORROSION RESISTANT MECHANICAL CHARACTERISTICS AND SHEETS THUS PRODUCED |
DE102005008410B3 (en) | 2005-02-24 | 2006-02-16 | Thyssenkrupp Stahl Ag | Coating steel bands comprises heating bands and applying liquid metal coating |
-
2009
- 2009-04-23 DE DE102009018577A patent/DE102009018577B3/en active Active
-
2010
- 2010-04-22 AU AU2010240903A patent/AU2010240903A1/en not_active Abandoned
- 2010-04-22 ES ES10717595T patent/ES2717878T3/en active Active
- 2010-04-22 TR TR2019/06585T patent/TR201906585T4/en unknown
- 2010-04-22 EP EP10717595.2A patent/EP2432910B2/en active Active
- 2010-04-22 WO PCT/EP2010/055334 patent/WO2010122097A1/en active Application Filing
- 2010-04-22 PL PL10717595T patent/PL2432910T3/en unknown
- 2010-04-22 CN CN201080018273.9A patent/CN102421928B/en active Active
- 2010-04-22 KR KR1020117027436A patent/KR101679006B1/en active IP Right Grant
- 2010-04-22 US US13/265,573 patent/US9611527B2/en active Active
- 2010-04-22 CA CA2759369A patent/CA2759369C/en not_active Expired - Fee Related
- 2010-04-22 BR BRPI1016179A patent/BRPI1016179B1/en active IP Right Grant
- 2010-04-22 JP JP2012506496A patent/JP5834002B2/en not_active Expired - Fee Related
-
2016
- 2016-01-01 AU AU2016200172A patent/AU2016200172B2/en not_active Ceased
Patent Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE2522485A1 (en) † | 1974-05-24 | 1975-12-04 | Armco Steel Corp | PROCESS FOR IMPROVING THE WETTABILITY OF THE SURFACE OF A LOW-ALLOY STEEL STRIP AND SHEET METAL BY A MOLTEN COVERING METAL |
BE1011131A6 (en) † | 1997-04-28 | 1999-05-04 | Centre Rech Metallurgique | Method of coating a steel strip by hot-dip galvanising |
CN100368580C (en) † | 2003-04-10 | 2008-02-13 | 新日本制铁株式会社 | High strength hot dip galvanized steel sheet, and its production method |
WO2006002843A1 (en) † | 2004-06-29 | 2006-01-12 | Corus Staal Bv | Steel sheet with hot dip galvanized zinc alloy coating and process to produce it |
DE102004059566B3 (en) † | 2004-12-09 | 2006-08-03 | Thyssenkrupp Steel Ag | Process for hot dip coating a strip of high strength steel |
JP2007211279A (en) † | 2006-02-08 | 2007-08-23 | Nippon Steel Corp | Ultrahigh strength steel sheet having excellent hydrogen brittleness resistance, method for producing the same, method for producing ultrahigh strength hot dip galvanized steel sheet and method for producing ultrahigh strength hot dip alloyed galvanized steel sheet |
WO2007109865A1 (en) † | 2006-03-29 | 2007-10-04 | Centre De Recherches Metallurgiques Asbl-Centrum Voor Research In De Metallurgie Vzw | Method for continuously annealing and preparing strip of high-strength steel for the purpose of hot-dip galvanizing it |
WO2008022980A2 (en) † | 2006-08-22 | 2008-02-28 | Thyssenkrupp Steel Ag | Process for coating a hot- or cold-rolled steel strip containing 6 - 30% by weight of mn with a metallic protective layer |
JP2008156734A (en) † | 2006-12-26 | 2008-07-10 | Jfe Steel Kk | High-strength hot-dip galvanized steel sheet and its manufacturing method |
WO2008102009A1 (en) † | 2007-02-23 | 2008-08-28 | Corus Staal Bv | Cold rolled and continuously annealed high strength steel strip and method for producing said steel |
Non-Patent Citations (5)
Title |
---|
FOURMENTIN ET AL.: "MICROSTRUCTURE AND PROPERTIES OF RAPIDLY HEAT TREATED AND GALVANIZED DUAL PHASE STEEL", 7TH INTERNATIONAL CONFERENCE ON ZINC AND ZINC ALLOY COATED STEEL SHEET GALVATECH`07, 2007, pages 380 - 385 † |
GAO ET AL.: "GALVANIZING TRIP STEEL USING THE DIRECT REDUCTION PROCESS", 7TH INTERNATIONAL CONFERENCE ON ZINC AND ZINC ALLOY COATED STEEL SHEET GALVATECH`07, 2007, pages 472 - 477 † |
HUIN D; FLAUDER P; J-B LEBLOND: "Numerical Simulation of Internal Oxidation of Steels during Annealing Treatments", OXIDATION OF METALS,, vol. 64, no. 1-2, August 2005 (2005-08-01), pages 131 - 167 † |
KIM ET AL.: "Galvanizability of Advanced High-Strength Steels 1180TRIP and 1180CP", GALVANIZERS ASSOCIATION 100TH ANNUAL MEETING, 27 October 2008 (2008-10-27), Baltimore, Maryland, USA, pages 1 - 14 † |
XUE BIN YU, XIN YAN JIN, QUAN CHENG ZHANG: "Top dross and bath behavior from galvannealing to galvanizing transition", 7TH INTERNATIONAL CONFERENCE ON ZINC AND ZINC ALLOY COATED STEEL SHEET GALVATECH`07, 18 November 2007 (2007-11-18) - 22 November 2007 (2007-11-22), Osaka, Japan, pages 129 - 134 † |
Also Published As
Publication number | Publication date |
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WO2010122097A1 (en) | 2010-10-28 |
JP2012524839A (en) | 2012-10-18 |
ES2717878T3 (en) | 2019-06-26 |
PL2432910T3 (en) | 2019-07-31 |
CN102421928B (en) | 2015-10-21 |
AU2016200172B2 (en) | 2017-08-03 |
EP2432910B1 (en) | 2019-02-13 |
TR201906585T4 (en) | 2019-05-21 |
AU2010240903A1 (en) | 2011-11-10 |
CN102421928A (en) | 2012-04-18 |
US20120125491A1 (en) | 2012-05-24 |
CA2759369A1 (en) | 2010-10-28 |
KR101679006B1 (en) | 2016-11-24 |
KR20120025476A (en) | 2012-03-15 |
JP5834002B2 (en) | 2015-12-16 |
BRPI1016179B1 (en) | 2020-04-07 |
US9611527B2 (en) | 2017-04-04 |
EP2432910A1 (en) | 2012-03-28 |
CA2759369C (en) | 2017-02-07 |
AU2016200172A1 (en) | 2016-01-28 |
BRPI1016179A2 (en) | 2016-04-19 |
DE102009018577B3 (en) | 2010-07-29 |
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