Patent Application
20240102138
The present invention relates to coated steel sheets and to high strength press hardened steel parts having good bendability properties.
High strength press-hardened parts can be used as structural elements in automotive vehicles for anti-intrusion or energy absorption functions.
In such type of applications, it is desirable to produce steel parts that combine high mechanical strength, high impact resistance and good corrosion resistance. Moreover, one of major challenges in the automotive industry is to decrease the weight of vehicles in order to improve their fuel efficiency in view of global environmental conservation, without neglecting safety requirements.
This weight reduction can be achieved in particular thanks to the use of steel parts with a martensitic or bainitic/martensitic microstructure.
The publication WO2016104881 relates to a hot press forming part used as a structural part of a vehicle or the like, requiring impact resistance characteristics, and more particularly, having a tensile strength of 1300 MPa or greater and a method for manufacturing the same by heating a steel material to a temperature at which an austenite single phase may be formed, and quenching and hot forming thereof using a mold. To obtain such properties, the base steel sheet comprises a thin ferrite layer lower than 50 μm at the surface, and the carbides size and density should be controlled. This ferrite layer in the substrate permits inhibition of the propagation of the fine cracks formed on the plating layer to the base but leads to a low bendability with bending angle lower than 70°.
The publication WO2018179839 relates to a hot-pressed part obtained by hot pressing a steel sheet having a microstructure changing in the thickness direction, with a soft layer made of at least 90% of ferrite, a transition layer made of ferrite and martensite and a hard layer mainly martensitic and has both high strength and high bendability. To obtain such properties, the cold rolled steel sheet is annealed in an atmosphere with a dew point temperature from 50° C. to 90° C., which could be harmful to aluminum alloy coating.
It is an object of the present invention to provide a press hardened steel part having a combination of high mechanical properties with the tensile strength TS above or equal to 1500 MPa and bending angle higher than 70°. Preferably, the press hardened steel part according to the invention has yield strength YS above or equal to 1250 MPa.
Another purpose of the invention is to obtain a coated steel sheet that can be transformed by hot forming into such a press hardened steel part.
The present invention provides a coated steel sheet made of a steel having a composition comprising, by weight percent:
The invention will now be described in detail and illustrated by examples without introducing limitations, with reference to the appended figures:
The composition of the steel according to the invention will now be described, the content being expressed in weight percent.
According to the invention the carbon content is comprised from 0.26% to 0.40% to ensure a satisfactory strength. Above 0.40% of carbon, weldability and bendability of the steel sheet may be reduced. If the carbon content is lower than 0.26%, the tensile strength will not reach the targeted value.
The manganese content is comprised from 0.5% to 1.8%. Above 1.8% of addition, the risk of central segregation increases to the detriment of the bendability. Below 0.5% the hardenability of the steel sheet is reduced. Preferably the manganese content is comprised from 0.5% to 1.3%.
According to the invention, silicon content is comprised from 0.1% to 1.25%. Silicon is an element participating in the hardening in solid solution. Silicon is added to limit carbides formation. Above 1.25%, silicon oxides form at the surface, which impairs the coatability of the steel. Moreover, the weldability of the steel sheet may be reduced. Preferably, the silicon content is from 0.2% to 1.25%. More preferably the silicon content is from 0.3% to 1.25%. More preferably, the silicon content is from 0.3% to 1%.
The aluminum content is comprised from 0.01% and 0.1% as it is a very effective element for deoxidizing the steel in the liquid phase during elaboration. Aluminum can protect boron if titanium content is not enough. The aluminum content is lower than 0.1% to avoid oxidation problems and ferrite formation during press hardening. Preferably the aluminum content is comprised from 0.01% to 0.05%.
According to the invention, the chromium content is comprised from 0.1% to 1.0%. Chromium is an element participating in the hardening in solid solution and must be higher than 0.1%. The chromium content is below 1.0% to limit processability issues and cost.
The titanium content is comprised from 0.01% to 0.1% in order to protect boron from formation of BN. Titanium content is limited to 0.1% to avoid TiN formation.
According to the invention, the boron content is comprised from 0.001% to 0.004%. Boron improves the hardenability of the steel. The boron content is not higher than 0.004% to avoid a risk of breaking the slab during continuous casting.
Some elements can optionally be added.
Nickel may be added as an optional element up to 0.5% as it can substantially reduce the sensitivity to delayed fracture.
Molybdenum content can optionally be added up to 0.40%. As boron, molybdenum improves the hardenability of the steel. Molybdenum is not higher than 0.40% to limit cost.
According to the invention, niobium can optionally be added up to 0.08% to improve ductility of the steel. Above 0.08% of addition, the risk of formation of NbC or Nb(C,N) carbides increases to the detriment of the bendability. Preferably the niobium content is below or equal to 0.05%.
Calcium may be also added as an optional element up to 0.1%. Addition of Ca at the liquid stage makes it possible to create fine oxides which promote castability of continuous casting.
The remainder of the composition of the steel is iron and impurities resulting from the smelting. In this respect, P, S and N at least are considered as residual elements which are unavoidable impurities. Their content is less than 0.010% for S, less than 0.020% for P and less than 0.010% for N.
The microstructure of the coated steel sheet according to the invention will now be described.
A section of a coated steel sheet of the invention is schematically represented on
The bulk of the coated steel sheet (2) has a microstructure comprising, in surface fraction, from 60% to 90% of ferrite, the rest being martensite-austenite islands, pearlite or bainite.
This ferrite is formed during the intercritical annealing of the cold rolled steel sheet. The rest of the microstructure is austenite at the end of the soaking, which transform into martensite-austenite islands, pearlite or bainite during the cooling of the steel sheet.
The decarburized layer present on top of the bulk is obtained during the annealing of the cold rolled steel sheet thanks to the control of the atmosphere in the furnace to set a dew point temperature strictly higher than −10° C. and below or equal to 20° C.
The coated steel sheet according to the invention can be produced by any appropriate manufacturing method and the man skilled in the art can define one. It is however preferred to use the method according to the invention comprising the following steps:
A semi-product able to be further hot-rolled, is provided with the steel composition described above. The semi product is reheated at a temperature comprised from 1150° C. to 1300° C.
The steel sheet is then hot rolled at a finish hot rolling temperature comprised from 800° C. to 950° C.
The hot-rolled steel is then cooled and coiled at a temperature Tcoil lower than 670° C., and optionally pickled to remove oxidation.
The coiled steel sheet is then optionally cold rolled to obtain a cold rolled steel sheet. The cold-rolling reduction ratio is preferably comprised from 20% to 80%. Below 20%, the recrystallization during subsequent heat-treatment is not favored, which may impair the ductility of the steel sheet. Above 80%, there is a risk of edge cracking during cold-rolling.
The steel sheet is then annealed in an HNx atmosphere with from 0% to 15% of H2, to an annealing temperature TA comprised from 700° C. to 850° C. and maintained at said annealing temperature TA for a holding time tA comprised from 10s to 1200s, in order to obtain an annealed steel sheet. Below 700° C., the kinetic of formation of the decarburized layer is too slow to obtain a ferrite layer in its upper part. The holding time tA is above or equal to 10 s to allow the ferrite layer to form, and below or equal to 1200s in order to limit the thickness of this ferrite layer.
During this annealing, the atmosphere in the furnace is controlled to have a dew point temperature TDP1 strictly higher than −10° C. and below or equal to +20° C. in order to form a decarburized layer according to the invention. If TDP1 is below or equal to −10° C., the formation of the decarburized layer is slowed down and the ferrite layer is not formed in its upper part. The bendability of the steel part will be too low. If TDP1 is higher than 20° C., the surface of the steel sheet may be completely oxidized, impairing coatability and mechanical properties of the sheet
In an embodiment of the invention the annealed steel sheet is heated to an annealing temperature T2 comprised from 700° C. to 850° C. and maintained at said temperature T2 for a holding time t2 comprised from 10s to 1200s, the atmosphere having a dew point TDP2 strictly higher than −10° C. and below or equal to +20° C.
The steel sheet is then coated with an aluminum alloy coating.
The microstructure of the press hardened steel part according to the invention will now be described. A section of the press hardened steel part is schematically represented on
The steel part comprises successively from the bulk to the surface of the steel part:
During the heating of the steel blank cut out of the steel sheet according to the invention, all microstructural elements of the bulk are transformed into austenite, and the ferrite of the decarburized layer is transformed into austenite with wider grain size than the austenite of the bulk. After hot forming, the steel part is then die-quenched. The interdiffusion layer grows from the former wide grain size austenite layer, thus having larger grain width than prior austenitic grain size in the bulk. The ratio between the ferritic grain width in the interdiffusion layer GWint over prior austenite grain size in the bulk PAGSbulk, satisfies following equation:
(GWint/PAGSbulk)−1≥30%
in order to improve bendability of the steel sheet, without deteriorating mechanical properties.
The ferritic grain width is the average distance between two parallel grain boundaries of the interdiffusion layer, grain boundaries being oriented in the direction of the thickness of the sheet. The combination of annealing temperature TA, annealing time tA and dew point temperature TDP1 according to the invention promotes the formation of large grain width GWint in the interdiffusion layer. Moreover, the thermal treatment of the steel blank before the press forming, rules the austenitic grain growth and so the PAGS in the bulk.
In an embodiment, the press hardened steel part may further comprise a martensite layer with a carbon gradient between the bulk and the interdiffusion layer, as represented by (8) in
The press hardened steel part according to the invention has a tensile strength TS above or equal to 1500 MPa and a bending angle higher than 70°. The bending angle has been determined on press hardened parts according to the method VDA238-100 bending Standard (with normalizing to a thickness of 1.5 mm).
In a preferred embodiment of the invention, the yield strength YS is above or equal to 1250 MPa. TS and YS are measured according to ISO standard ISO 6892-1.
The press hardened steel part according to the invention can be produced by any appropriate manufacturing method and the man skilled in the art can define one. It is however preferred to use the method according to the invention comprising the following steps:
The invention will be now illustrated by the following examples, which are by no way limitative.
6 grades, which compositions are gathered in table 1, were cast in semi-products and processed into steel sheets, then steel parts, following the process parameters gathered in table 2.
The tested compositions are gathered in the following table wherein the element contents are expressed in weight percent.
E
0.003
F
0.21
3
−10
4
−40
5
E
10800
6
F
Steel semi-products, as cast, were reheated at 1200° C., hot rolled with a finish hot rolling temperature comprised from 800 to 950° C., coiled at 550° C. and cold rolled with a reduction rate of 60%. Steel sheets are then heated to a temperature TA and maintained at said temperature for a holding time tA, in an HNx atmosphere with 5% of H2, having a controlled dew point. The steel sheets were then cooled down to a temperature from 560 to 700° C. and then hot dip coated with an aluminum-silicon coating comprising 10% of silicon.
Samples 1,2,5 and 6 did undergo a second annealing at a temperature T2 before coating, the steel sheet being maintained at said T2 temperature for a holding time t2, in an HNx atmosphere with 5% of H2 and a controlled dew point. The following specific conditions were applied:
The coated steel sheets were analyzed, and the corresponding properties of decarburized layer are gathered in table 3.
3
—
4
no
—
5
140
6
The coated steel sheets were then cut to obtain a steel blank, heated at 900° C. during 6 minutes and hot-formed. The steel parts were analyzed and the corresponding microstructure, ferritic grain width in interdiffusion layer GWint, and prior austenite grain size in the bulk PAGSbulk are gathered in table 4. Mechanical properties are gathered in Table 5.
3
27%
4
−2%
5
10% ferrite
70% bainite
20% martensite
6
The surface fractions, ferritic grain width in the interdiffusion layer and PAGS are determined through the following method: a specimen is cut from the press hardened steel part, polished and etched with a reagent known per se, to reveal the microstructure. The section is afterwards examined through optical or scanning electron microscope, for example with a Scanning Electron Microscope with a Field Emission Gun (“FEG-SEM”) at a magnification greater than 5000×, coupled to a BSE (Back Scattered Electron) device.
3
36
4
42
5
34
6
1410
65
Mechanical properties of the tested samples were determined and gathered in the following table:
The examples show that the steel parts according to the invention, namely examples 1-2 are the only one to show all the targeted properties thanks to their specific compositions and microstructures.
The coated steel sheet is then hot formed.
The grain width of ferrite formed in the interdiffusion layer (5) is a heritage of the pure ferrite layer in which austenite formation takes place during heating, with larger grain size. The interdiffusion layer grows on this large austenite grain size. The grain width of ferrite in the interdiffusion layer (6) is then larger than prior austenite grain size in the bulk (7), leading to good bendability with bending angle higher than 70°.
The coated steel sheet is then hot formed.
The grain width of ferrite formed in the interdiffusion layer (6) is a heritage of the pure ferrite layer in which austenite formation takes place during heating, with larger grain size. The interdiffusion layer grows on this large austenite grain size. The grain width of ferrite in the interdiffusion layer (6) is then larger than prior austenite grain size in the bulk (7), leading to good bendability with bending angle higher than 70°. Moreover, due to the thick ferrite layer (4) in the coated steel sheet, a layer of martensite with a carbon gradient is formed between the bulk and the interdiffusion layer in the press hardened steel part, leading to tensile strength higher than 1500 MPa.
In trial 3, the coated steel sheet has a decarburized layer, without ferrite layer in its upper part, as represented schematically in
The coated steel sheet is then hot formed.
In trial 4, the low dew point temperature TDP1 of −40° C. implies an absence of the decarburized layer and ferrite layer in the coated steel sheet.
The coated steel sheet is then hot formed.
In trial 5, the steel sheet is maintained during 10800s at soaking temperature, which form in the coated steel sheet, a thicker ferrite layer in the decarburized layer than previous trials.
The coated steel sheet is then hot formed and
During die quenching of the steel part, the ferrite layer is still present and the layer of austenite with carbon gradient transforms into a martensite layer with gradient of carbon, leading to a multi-phased layer. This triggers a decrease of yield strength.
In trial 6, the steel sheet has a low carbon level of 0.21%. This low carbon content combined to the process parameters, leads to a decarburized layer in the coated steel sheet with the ferrite layer. Nevertheless, the yield strength and tensile strength of the press hardened steel part are not achieved because of the low level of carbon.
| Number | Date | Country | Kind |
|---|---|---|---|
| PCT/IB2020/062045 | Dec 2020 | WO | international |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/IB2021/061291 | 12/3/2021 | WO |
