Patent Application
20130189539
The invention relates to a method for producing a steel strip composite and to a steel strip composite produced by said method.
Advanced high strength steels (AHSS) and ultra high strength steels (UHSS) are commonly used in the automotive industry due to their improved yield strength and ductility compared to other high strength steels (HSS). High strength steels are typically hardened by solid solution, precipitation or grain refining, whereas AHSS are hardened by phase transformation. AHSS and UHSS contain microstructures based on austenite, ferrite, bainite and martensite and include dual phase (DP) steel, transformation induced plasticity (TRIP) steel, TRIP assisted dual phase (TADP) steel and Twinning induced plasticity (TWIP).
To enable their use in the automotive industry AHSS/UHSS steels are hot-dip galvanised to afford corrosion protection to the underlying AHSS/UHSS substrate. In order to reach the desired strength levels and to control phase transformation, alloying elements such as silicon, manganese, chromium and aluminium are required, silicon is particularly favourable since it is relatively inexpensive.
It is known that the inclusion of the above alloying elements, particularly silicon in AHSS/UHSS, reduces zinc wetting and/or zinc adhesion during hot-dip galvanising; consequently a reduction in the galvanised surface quality to unacceptable levels is observed. Alternative galvanising methods such as electro-zinc galvanising could be used in lieu of hot-dip galvanising, but such methods tend to be more expensive and bring with them the risk of hydrogen ingress and associated embrittlement.
Therefore the problem arises that it is difficult to provide a steel strip having improved strength and ductility in combination with an acceptable up to excellent hot-dip galvanisability.
It is an object of this invention to provide a method for improving the hot-dip galvanisability of steels having a high alloy content.
It is a further object of this invention to provide a steel having improved strength and ductility in combination with an acceptable up to excellent hot dip galvanisability.
According to a first aspect of the invention there is provided a three-layer steel strip composite consisting of a steel strip having a first microstructure disposed between two steel strips having a second microstructure, wherein a metal or metal alloy coating is present on each steel strip having the second microstructure on a surface opposite to the surface contacting the steel strip having the first microstructure.
The steel strip having the first microstructure (core) exhibits high strength and ductility due to a high alloying element content in the core. In this respect the steel strip core preferably contains at least 2 wt % Mn and/or at least 0.5 wt % Si. However, the same alloying elements reduce the wetting and/or adhesion of the metal or metal alloy coating to the steel core substrate. As a consequence, the surface quality of such an applied coating would be of an unacceptable level. In contrast, the steel strip having the second microstructure (clad) is highly formable and comprises a low alloying element content that promotes wetting and/or adhesion of the metal or metal alloy coating to the clad.
The inventors have found that by providing a steel strip composite consisting of two steel strips having a low content of alloying elements and a steel strip having a high alloy content disposed therebetween, it was possible to provide a composite having improved strength and ductility together with improved coating performance. By improved coating performance, it should be understood that the formation of bare spots, cracks or flakes in or on the metallic coating are reduced or eliminated.
In a preferred embodiment of the invention the metal or metal alloy coating is zinc, aluminium or an alloy thereof. By coating each steel strip having the second microstructure with zinc, aluminium or an alloy thereof, the steel is afforded sacrificial corrosion protection since the zinc and aluminium, will oxidise in preference to iron in the steel.
In a preferred embodiment of the invention the metal alloy may further comprise magnesium to improve the corrosion resistance and the conductivity of the sacrificial corrosion layer. Other elements such as Si, Ti, Cu, Ni, Co and Cr may also be present in the metal alloy coating.
In a preferred embodiment of the invention each steel having the second microstructure comprises 1-10%, preferably 1-5% of the total thickness of the steel strip composite. Each strip having the second microstructure should not exceed a thickness that is greater than 10% of the total thickness of the composite otherwise the overall strength of the steel strip composite is reduced. However, the thickness of each strip having the second microstructure should not be less than 1% of the total thickness of the composite since this results in the formation of bare spots and/or flaking of the metallic coating. If each strip having the second microstructure has a thickness of 5% then the composite exhibits an improved galvanising response and an improvement in weldability relative to composites comprising less than 5% of the steel strip having the second microstructure.
In a preferred embodiment of the invention the thickness of the steel strip composite is between 0.5 and 10 mm, preferably between 0.5 and 4 mm and more preferably between 0.5 and 2.5 mm.
In a preferred embodiment of the invention the steel strip having the first microstructure is an advanced high strength steel or ultra high strength steel such as dual phase (DP) steel, transformation induced plasticity (TRIP) steel, TRIP assisted dual phase (TADP) steel, Twinning induced plasticity (TWIP) steel. A composite which comprises any one the above steels exhibits improved strength and ductility characteristics relative to other high strength steels. As a consequence, the down-gauging potential of AHSS and UHSS is improved; such properties are particularly attractive to the automotive sector where weight reduction is becoming an increasingly important issue.
In a preferred embodiment of the invention the advanced high strength steel or ultra high strength steel strip material contains in weight % 0.04-0.30% C, 1.0-3.5% Mn, 0-1.0% Si, 0-2.0% Al and 0-1.0% Cr. Other elements can be present, such as V, Nb, Ti and B, but usually in a small amount.
Preferably, the steel strip having the first microstructure is a TRIP steel containing in weight % 0.10-0.30% C, 1.0-3.5% Mn, 0.2-0.8% Si and 0.5-2.0% Al, preferably, 0.10-0.20% C, 1.0-2.0% Mn, 0.2-0.6% Si and 0.5-1.5 Al. Small amounts of other alloying elements can also be present. Preferably Si+Al does not exceed 1.5 wt % but in the absence of Al, Si may be added in the range of 1.0-2.0 wt %, preferably 1.0-1.5 wt %.
In the case of TRIP steels the first microstructure comprises a triple phase microstructure of ferrite, bainite and retained austenite. During plastic deformation the retained austenite is transformed into martensite, which results in the steel exhibiting enhanced strength and ductility.
Preferably the steel strip having the first microstructure is a TWIP steel containing in weight % between 10 and 40% manganese, preferably between 12 and 25% manganese and up to 10% aluminium. TWIP steels are typically difficult to galvanize. However, the provision of a steel strip having the second microstructure on both sides of the TWIP steel leads to an improved galvanising response of the TWIP steel.
In a preferred embodiment of the invention the steel strip having the first microstructure is a quenched and partitioned steel containing in weight % 0.15-0.4% C, 1.0-3.0% Mn, 1.0-2.5% Si, 0-0.5% Mo and 0-1.0% Cr, preferably, 0.15-0.22% C, 1.0-1.7% Mn, 1.0-1.7% Si, 0-0.25% Mo and 0-0.5% Cr, the remainder being iron and unavoidable impurities. Other alloying elements such as P, Ti, V, Ni, Nb, B and Ta can be present but only in small amounts The microstructure of the Q&P steel comprises martensite and carbon-enriched austenite, and in certain instances, equiaxed ferrite. The Q&P steel is heated to form austenite, either partially or fully, followed by quenching to a temperature between the martensite start temperature (Ms) and the martensite finish temperature (Mf), thereby creating a controlled amount of martensite and retained austenite. The Q&P steel is then subjected to a thermal treatment to partition carbon from the martensite into the austenite. By partitioning, the formation of carbides is suppressed and the austenite is stabilised rather than decomposed. The stabilisation of austenite results in the steel exhibiting improved ductility relative to traditional high strength steels.
In a preferred embodiment the steel strip having the first microstructure is a low density steel containing in weight % 0-0.2% C, 0-2.0% Si, 0-5.0% Mn, 2.0-17.0% Al, 0-3.0% Cr, 0-0.2% Ti and 0-0.2% Ce, preferably 0.005-0.2% C, 0-1.5% Si, 0-3.0% Mn, 2.0-9.0% Al, 0-2.1% Cr, 0-0.1% Ti and 0-0.15% Ce, the remainder being iron and unavoidable impurities. Low density steels comprise a ferritic microstructure or a ferritic and austenitic microstructure in the case of low density duplex steels comprising 10-30 wt % Mn and 5-10 wt % Al.
In a preferred embodiment of the invention the steel strip having the second microstructure is an interstitial-free (IF), extra low carbon (ELC), ultra low carbon (ULC) or low carbon (LC) steel, preferably containing in weight % 0-0.1% C, 0-1.0% Mn, 0-0.1% Si, 0-0.1 Al and 0-0.1 Cr, preferably 0.001-0.005% C, 0.05-1% Mn, 0-0.1% Si, 0-0.1 Al and 0-0.1 Cr the remainder being iron and unavoidable impurities. Other alloying elements such as Mo, P, Ti, V, Ni, Nb and Ta can be present but only in small amounts.
The above steel clad substrates all comprise a low content (≦1 wt %) of alloying elements and therefore the presence of the corresponding alloy-oxides is also low. By having a low content of alloy-oxides the wettability of the metal or metal alloy coating to the clad is increased to an extent where the surface quality of the applied coating is of an acceptable level.
In a preferred embodiment of the invention the steel strip having the first microstructure comprises austenite.
In a preferred embodiment of the invention the steel strip composite has yield strength of 400 MPa or above, making such composites suitable for automotive applications.
In a preferred embodiment of the invention the steel strip composite has a tensile strength of 800 MPa or above, making such composites suitable for automotive applications.
According to a second aspect of the invention there is provided a method for producing a three-layer steel strip composite, which comprises the steps of providing a steel plate having a first microstructure and two steel strips having a second microstructure; deoxidising and cleaning the steel plate and each steel strip and disposing the steel plate between the two steel strips to form a three-layer stack package; rolling the stack package to form the composite and providing a metallic coating on each steel strip having the second microstructure on a surface opposite to the surface contacting the steel strip having the first microstructure.
By following the above method it is possible to provide steel strip composite having improved strength and ductility in combination with improved coating performance. The contact surfaces of the steel plate having the first microstructure and the steel strip having second microstructure are deoxidised and cleaned by brushing, grinding and/or pickling before the steel strips are stacked to form the stack package. By cleaning before stacking, inter-metallic particles which could cause brittleness are substantially absent.
In a preferred embodiment of the invention the composite is formed by hot-rolling, cold rolling or by hot-rolling followed by cold rolling. When the composite is formed by hot-rolling, the three-layer stack package is heated and hot-rolled between 1250° C. and 800° C.; the temperature after the final hot-rolling pass should be above the austenitic (Ac) temperature. The composite thus produced has a thickness of approximately 4 mm. The composite is then subjected to a controlled cooling to a coiling temperature in order to control phase transformations in the steel. The composite is coiled and left to cool to room temperature before being cold-rolled to reduce the thickness of the composite still further. Preferably the cold rolled steel composite has a thickness of 1.5 mm. The composite is then subjected to a continuous annealing cycle and subsequently provided with a metallic coating on each steel strip having the second microstructure on a surface opposite the surface contacting the steel strip having the first microstructure. When the composite is formed by cold rolling, at least one cold rolling pass with a reduction of 25-50%, preferably 30-50% and more preferably 35-45% is required. Steel strip composites, whether formed by hot-rolling, by cold-rolling or by hot-rolling followed by cold-rolling exhibit full metallic bonding between the atoms of the strip having the first microstructure and the strip having the second microstructure.
In a preferred embodiment of the invention the stack package is circumferentially welded before the step of rolling. By welding the steel strip having the first microstructure and the steel strip having the second microstructure together, oxygen is prevented from entering into contact with interface therebetween, which would otherwise result in the oxide formation and growth at the interface.
In a preferred embodiment of the invention the metallic coating is provided by hot-dip galvanising or by electro-galvanising.
The invention will now be elucidated by way of example making reference to the accompanying figures.
According to an example a Q&P steel (2) is provided in the form of a cast block, hot-rolled at a temperature of 1250° C. and break down rolled from 100 mm to a flat 32 mm plate. Two strips of low carbon steel (3) having a strip thickness of 4 mm are cut to a width of approximately 1 mm less than that of the Q&P plate. The contact surfaces of each substrate are brushed and milled before each side of the Q&P plate is provided with a low carbon steel strip, resulting in a 3-layer stack package. The different layers of the stack package are welded together by rectangular arc welding.
The welded 3-layer stack package is then heated to a temperature of 1250° C. for 30 minutes before being hot-rolled in six passes 27-17.8-12-8-6-4mm, the final pass being performed at a temperature of 880° C., thereby forming a steel strip composite (1). The composite is cooled at a rate of 30° C./s from 840° C. to 600° C. using a table simulation and cooled to room temperature using a warm coil simulation. The composite is then pickled and cold-rolled to 1.5 mm in 0.5 mm passes.
After cold-rolling the composite is annealed and galvanised according to the annealing and galvanising cycle of
In Table 1 below, the chemical compositions (wt % unless specified) of Q&P steel and low carbon steel in accordance with the invention are given.
The chemical composition of advanced and ultra high strength steels such as TWIP and TRIP steels, and low density and low density duplex steels are also given in Table 1. The aforementioned steels contain a high alloying element content and are therefore suitable core materials that can be used in place of the Q&P steel in the steel strip composite.
In Table 2 the mechanical properties of a Q&P steel and a composite wherein a Q&P steel is disposed between two strips of low carbon steel are given.
The Erichsen cupping test was carried out in accordance with ISO 20482-2003. The Erichsen cup height of the composite is approximately 20% greater than the Q&P steel which was used as a reference. Moreover, the perpendicular bending angle and strain before failure of the composite were 57% and 47% respectively, which is better than the results obtained for the Q&P reference. These improved mechanical properties have been attributed to the improved resistance to crack initiation at the low carbon steel surface.
Visual inspection of the Q&P reference and the steel strip composite after hot-dip galvanising revealed that no zinc wetting was observed on the Q&P reference. However, very good wetting was observed for the composite and no bare spots could be seen.
Zinc adhesion was tested using a standard ½ bending test. Due to the unacceptable zinc wetting on the Q&P reference, the Q&P reference was not tested. After deformation of the composite, the zinc layer exhibited only a few small cracks which is standard. Following the bending test it was not possible to peel the zinc off from the composite which is again indicative of very good zinc adhesion.
Results relating to the hot-dip galvanising response can be seen in
| Number | Date | Country | Kind |
|---|---|---|---|
| 10013487.3 | Oct 2010 | EP | regional |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/EP11/05065 | 10/11/2011 | WO | 00 | 4/4/2013 |
