Patent Application
20240209485
The present invention relates to 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 and high impact resistance. Moreover, one of the major challenges in the automotive industry is to decrease the weight of vehicles in order to improve their fuel efficiency in view of the global environmental conservation, without neglecting the safety requirements.
This weight reduction can be achieved in particular thanks to the use of steel parts with a predominantly martensitic microstructure.
It is challenging to produce very high strength steels which also have a good resistance to the formation of cracks under bending. Indeed, very high strength steels tend to crack early on when submitted to a bending load. This is detrimental to the crash worthiness of a part produced with such high strength steel, because even though the material is able to withstand very high loads thanks to its high tensile strength, once cracks start to appear in the part, these cracks will quickly propagate under the continued load and the part will fail prematurely.
A purpose of the current invention is to address the above-mentioned challenge and to provide a press hardened steel part having a combination of high mechanical properties with a tensile strength after hot stamping above or equal to 1800 MPa and a bending angle in the rolling direction normalized to 1.5 mm equal to or higher than 50° as measured by the VDA-238 standard.
Another purpose of the invention is to obtain a steel sheet that can be transformed by hot forming into such a press hardened steel part.
The present invention provides a 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, and referring to
A blank of steel refers to a flat sheet of steel, which has been cut to any shape suitable for its use. A blank has a top and bottom face, which are also referred to as a top and bottom side or as a top and bottom surface. The distance between said faces is designated as the thickness of the blank. The thickness can be measured for example using a micrometer, the spindle and anvil of which are placed on the top and bottom faces. In a similar way, the thickness can also be measured on a formed part.
Hot stamping is a forming technology which involves heating a blank up to a temperature at which the microstructure of the steel has at least partially transformed to austenite, forming the blank at high temperature by stamping it and quenching the formed part to obtain a microstructure having a very high strength. Hot stamping allows to obtain very high strength parts with complex shapes and presents many technical advantages. It should be understood that the thermal treatment to which a part is submitted includes not only the above described thermal cycle of the hot stamping process itself, but also possibly other subsequent heat treatment cycles such as for example the paint baking step, performed after the part has been painted in order to bake the paint. The mechanical properties of hot stamped parts below are those measured after the full thermal cycle, including optionally for example a paint baking step, in case paint baking has indeed been performed.
The ultimate tensile strength is measured according to ISO standard ISO 6892-1, published in October 2009. The tensile test specimens are cut-out from flat areas of the hot stamped part. If necessary, small size tensile test samples are taken to accommodate for the total available flat area on the part.
The bending angle is measured according to the VDA-238 bending standard. For the same material, the bending angle depends on the thickness. For the sake of simplicity, the bending angle values of the current invention refer to a thickness of 1.5 mm. If the thickness is different than 1.5 mm, the bending angle value needs to be normalized to 1.5 mm by the following calculation where α1.5 is the bending angle normalized at 1.5 mm, t is the thickness, and at is the bending angle for thickness t:
In the current invention, the bending angle was measured in the rolling direction, i.e. the direction along which the steel sheet travelled during the hot-rolling step. The bending angle was measured using a laser measurement device. When performing bending tests on hot stamped part, the samples are cut-out from flat areas of the part. If necessary, small size samples are taken to accommodate for the total available flat area on the part. If the rolling direction on the hot stamped part is not known, it can be determined using Electron Back-Scattered Diffraction (EBSD) analysis across the section of the sample in a Scanning Electron Microscope (SEM). The rolling direction is determined according to the intensity of the Orientation Density Function (ODF) representative of the major fibers at φ2=45°, where φ2 is the Euler angle as defined in “H.-J. Bunge: Texture Analysis in Materials Science—Mathematical Methods. 1st English Edition by Butterworth Co (Publ.) 1982” (see FIGS. 2.2 and 2.3 for the definition of φ2).
The bending angle of a part is representative of the ability of the part to resist deformation without the formation of cracks.
The composition of the steel according to the invention will now be described, the content being expressed in weight percent. The chemical compositions are given in terms of a lower and upper limit of the composition range, said limits being comprised within the possible composition range according to the invention.
According to the invention the carbon ranges from 0.3% to 0.4% to ensure a satisfactory strength. Above 0.4% of carbon, weldability and bendability of the steel sheet may be reduced. If the carbon content is lower than 0.3%, the tensile strength will not reach the targeted value.
The manganese content ranges from 0.5% to 1.0%. Above 1.0% of addition, the risk of MnS formation is increased to the detriment of the bendability. Below 0.5% the hardenability of the steel sheet is reduced.
The silicon content ranges from 0.4% to 0.8%. Silicon is an element participating in the hardening in solid solution. Silicon is added to limit carbides formation. Above 0.8%, silicon oxides form at the surface, which impairs the coatability of the steel. Moreover, the weldability of the steel sheet may be reduced.
The chromium content ranges from 0.1% to 1.0%. Chromium is an element participating in the hardening in solid solution and must be higher than 0.1% to ensure sufficient strength. The chromium content is preferably below 0.4% to limit processability issues and cost. Preferably the chromium content ranges from 0.1% to 0.4%.
Molybdenum content ranges from 0.1% to 0.5%. Molybdenum improves the hardenability of the steel. Below 0.1%, the tensile strength is not reached. Molybdenum is preferably not higher than 0.4% to limit costs.
Niobium ranges from 0.01% to 0.1%. Niobium improves ductility of the steel. Above 0.1% the risk of formation of NbC or Nb(C,N) carbides increases to the detriment of the bendability. Preferably the niobium content ranges from 0.03% to 0.06%.
According to the invention, the aluminium content ranges from 0.01% to 0.1% as it is a very effective element for deoxidizing the steel in the liquid phase during elaboration. Aluminium can protect boron if titanium content is not sufficient. The aluminium content is lower than 0.1% to avoid oxidation problems and ferrite formation during press hardening. Preferably the aluminium content ranges from 0.03% to 0.05%.
According to the invention, the titanium content ranges from 0.008% to 0.03% in order to protect boron, which would be trapped within BN precipitates. Titanium content is limited to 0.03% to avoid excess TiN formation. As will be explained in more detail further, it is possible to add the appropriate amount of Ti to capture the residual N content by measuring the N level of the liquid steel before adding Ti.
According to the invention, the boron content ranges from 0.0005% and 0.003%. Boron improves the hardenability of the steel. The boron content is not higher than 0.003% to avoid slab breaking issues during continuous casting.
Phosphorous is controlled to below 0.020%, because it leads to fragility and weldability issues.
Calcium is controlled to below 0.001% because the presence of Calcium in the liquid steel can lead to the formation of coarse precipitates which are detrimental to bendability.
Sulphur is controlled to below 0.004% because the presence of Sulphur in the liquid steel can lead to the formation of MnS precipitates which are detrimental to bendability.
Nitrogen is controlled to below 0.005% preferentially below 0.004% even more preferentially below 0.003%. The presence of Nitrogen can lead to the formation of precipitates such as TiN or TiNbCN, which are detrimental to the bendability.
Nickel is optionally added, up to a level of 0.5%. Nickel can be used to protect the steel from delayed cracking.
The remainder of the composition of the steel is iron and impurities resulting from the smelting.
The microstructure of the coated steel sheet according to the invention will now be described.
The steel sheet has a microstructure comprising, in surface fraction, from 60% to 95% of ferrite, the rest being martensite-austenite islands, pearlite or bainite.
The 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 transforms into martensite-austenite islands, pearlite or bainite during the cooling of the steel sheet.
The total amount of ferrite in the steel sheet microstructure is a function of the chemical composition, the annealing temperature TA and the soaking time tA. The highest the annealing temperature TA in the range of 700° C. to 850° C. and the longest the time time tA in the range of 10 seconds to 20 minutes, the more austenite will be formed during annealing. After annealing, the transformation of the formed austenite into martensite, bainite or ferrite will depend mainly on the cooling speed. Preferably, the cooling speed is below 10° C./s in order to form as much soft phases (ferrite, bainite) as possible This allows for good processability of the steel sheet before hot stamping.
Referring to
Said skin layers 2 have a skin layer inclusion population wherein the cumulated surface fraction of oxides, MnS and TiNbCN is equal to or less than 75*10−6. The method used to measure said inclusion population will be further detailed below.
The inventors have found that there is a correlation between the bending angle and the skin layer inclusion population, in particular the oxides, MnS and TiNbCN population. By controlling said skin inclusion population it is possible to improve the bending angle without adversely affecting other product properties, such as for example the tensile strength.
The following is a description of the methodology that was used in order to characterize the inclusions in the steel sheet and steel parts. It should be understood that this is only one possible methodology and that other protocols can also be implemented.
The inclusions present in the steel sheet have been characterized using a Scanning Electron Microscope (SEM) with Field Effect Gun (FEG). A Tescan Mira 3 SEM was used at a 14 kV power setting. Furthermore, the inclusions were analyzed using Energy Dispersive Spectrometry (EDS). A 120 mm2 Bruker EDS probe was used.
The sample is divided into 3 areas (Top skin, bottom skin, bulk, as described previously). Each area is divided into fields. In each field, inclusions are detected. A zoom is made on each inclusion to catch morphological features and perform EDS analysis. A double gray level threshold is set to catch particles (on a scale going from 0 to 255, 0 being black and 255 being white):
Using the information of the EDS probe, the shape and brightness level, each particle is then classified in one of the following categories: TiN, NbC, TiNbCN, alumina, Complex oxides, Oxisulfides, MnS.
The next step is to compute for the whole set of inclusions and for each particle family the following characteristics:
The surface faction of inclusions combines in one single parameter information both on the density level of particles and on their average size. The inventors have found that the surface fraction of inclusions is a good indicator of cleanliness and correlates well, in the case of specific inclusions, to some key in-use properties, such as the bending angle.
The coated steel sheet according to the invention can be produced by any appropriate manufacturing method and the person skilled in the art can define one. It is however preferred to use the method according to the invention comprising the below described steps.
In the following description, the term ladle refers to the vessel used to contain the liquid steel during the refining process. The term tundish refers to the container in which the liquid steel is poured before casting it into moulds—the tundish is used in continuous casting: it allows to have a buffer of liquid steel available for casting in between finishing pouring one ladle and opening the following ladle.
A semi-product able to be further hot-rolled, is provided with the steel composition described above. Particular care should be taken in the refining of said semi-product, in particular in the liquid phase and during casting, in order to manage the inclusion population.
In a first embodiment the liquid steel refining process comprises the following steps:
In a second embodiment the liquid steel refining process comprises the following steps:
More generally, it is preferable to refine the steel by performing the main additions of Mn, Si, Cr, Mo, Nb and B under vacuum, using for example a vacuum degasser. This allows for low nitrogen content in the steel and in turn allows for better control of nitrogen containing inclusions in the steel.
More generally, the inclusion flotation time is defined as the total amount of time the liquid steel spends after Mn, Cr, Si, Mo, Nb and B are added and before the casting step starts.
In order to control the inclusion surface fraction in the skin of the steel sheet, the inclusion flotation time should be controlled above a minimum inclusion flotation time tf. The value of tf will depend on the specific industrial setup which is used to produce the steel. It will depend on the production route in the steel shop as well as on the geometric configuration of the ladles that are used to process the liquid steel. Because the inclusion flotation time is related to fluid dynamics and movement of small particles within the liquid steel, the minimum inclusion flotation time necessary to reach the desired level of specific inclusions in the skin of the steel will depend on the size of the ladles, their diameter, height, volume etc. For example, the minimum inclusion flotation time is 60 minutes. For example, the minimum inclusion flotation time is 53 minutes.
In order to determine the minimum inclusion flotation time tf for a given steel composition and a given industrial equipment and production route, it is recommended to apply the following method:
After the liquid steel refining step, the method for manufacturing the steel sheet according to the present invention preferably comprises the following steps:
In summary, the above described process comprises preferably the following successive steps:
The press part manufacturing process and ensuing pressed part characteristics will now be detailed.
A steel blank is cut out of the steel sheet according to the invention and heated in an annealing furnace. Preferably, the steel blank is heated to a temperature comprised from 880° C. to 950° C. during 10 seconds to 15 minutes to obtain a heated steel blank. The heated blank is then transferred to a forming press before being hot formed and die-quenched to obtain a pressed part.
The microstructure of the pressed part comprises in surface fraction, more than 95% of martensite and less than 5% of bainite+ferrite. Furthermore, the pressed part according to the invention comprises a bulk portion and a top and bottom skin layer, wherein the skin layers occupy the outermost 10% of the thickness on either side of the bulk. Said skin layers have a skin layer inclusion population wherein the cumulated surface fraction of oxides, MnS and TiNbCN is equal to or less than 75*10−6.
The pressed part according to the invention has a bending angle in the rolling direction normalised to 1.5 mm of at least 50° and a tensile strength TS of at least 1800 MPa. Such high tensile strength and bending angle confer to said part a very good mechanical resistance, especially in the case of a crash. They afford a very good energy absorption capacity and anti-intrusion capacity, thereby increasing the safety of the vehicle.
The invention will be now illustrated by the following examples, which are by no way limitative.
5 different samples were tested coming from 8 different heats A, B, C, D, E, F, G and H of steel produced using an industrial production route. Samples 11, 12, 13, 14, 15 and 16 are according to the invention, samples R1, R2 are reference samples.
The tested compositions are gathered in the following table wherein the element contents are expressed in weight percent:
53
55
130
44
50
47
38
26
81
80
The following process parameters were applied in the steel shop and the following skin layer inclusions surface fraction was observed—the underlined values are not according to the invention:
The following process parameters were applied along the production route:
59
57
60
49
45
The following microstructures, bending angles and tensile strength were measured on the samples, the underlined values are not according to the invention:
Table 4 shows that the samples according to the invention (references I1, I2, I3, I4, I5 and I6) have a tensile strength above 1800 MPa and a bending angle in the rolling direction normalized to 1.5 mm above 50° thanks to their specific composition and skin layer inclusions.
Referring to table 2, there is a relationship between the inclusion flotation time and the skin layer cumulated surface fraction of oxides, MnS and TiNbCN. the inclusion flotation time represents the total amount of time the liquid steel spends after adding Mn, Cr, Si, Mo, Nb and B and before the continuous casting step starts.
The inventors have found that when using the specific composition of the invention and when increasing the inclusion flotation time above a minimum inclusion flotation time if, it is possible to control the skin layer cumulated surface fraction of oxides, MnS and TiNbCN below a critical level which ensures good bending resistance. In the industrial configuration that was used to produce the samples given in the current examples, the minimum inclusion flotation time if is 53 minutes. The value of tf will depend on the specific industrial setup which is used to produce the steel.
When the inclusion flotation time is equal to or above tf=60 minutes the skin layer cumulated surface fraction of oxides, MnS and TiNbCN fraction is equal to or below 75*10−6. When the inclusion flotation time is less than tf=53 minutes the skin layer cumulated surface fraction of oxides, MnS and TiNbCN fraction is above 75*10−6.
The inventors have found that when the steel is submitted to a bending load, the inclusion surface fraction in the skin layers plays an important role in improving the resistance of the material to crack formation. Surprisingly, this is not the case for all types of inclusions. For example, NbC inclusions do not seem to have a significant impact on the bending properties of the steel. On the other hand, it was found that the cumulated surface fraction of oxides, MnS and TiNbCN plays an important role in the bending performance. Reducing the cumulated surface fraction of oxides, MnS and TiNbCN helps to improve the bending performance.
Referring to table 4, the samples according to the invention (I1, I2, I3, I4, I5 and I6), which all have a skin layer cumulated surface fraction of oxides, MnS and TiNbCN equal to or below 75*10−6, all have a bending angle in the rolling direction normalized to 1.5 mm of at least 50° and also a tensile strength of at least 1800 MPa. On the other hand, the reference samples (R1, R2), while maintaining tensile strength above 1800 MPa all have a bending angle in the rolling direction normalized to 1.5 mm below 50°. Therefore, the steel produced according to the invention will exhibit better resistance to crack formation when submitted to a load while exhibiting a very high tensile strength, which will improve the crash-worthiness and the safety of the part produced using said material.
| Number | Date | Country | Kind |
|---|---|---|---|
| PCT/IB2021/053725 | May 2021 | WO | international |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/IB2022/053987 | 4/29/2022 | WO |
