Patent Application
20240117457
The present invention deals with a low density steel sheet presenting a microstructure mainly comprising austenite. The steel sheet according to the invention is particularly well suited for the manufacture of safety or structural parts for vehicles such as land motor vehicles.
Environmental restrictions are forcing automakers to continuously reduce the CO2 emissions of their vehicles. To do that, automakers have several options, whereby their principal options are to reduce the weight of the vehicles or to improve the efficiency of their engine systems. Advances are frequently achieved by a combination of the two approaches. This invention relates to the first option, namely the reduction of the weight of the motor vehicles. In this very specific field, there is a two-track alternative:
The first track consists of reducing the thicknesses of the steels while increasing their levels of mechanical strength. Unfortunately, this solution has its limits on account of a prohibitive decrease in the rigidity of certain automotive parts and the appearance of acoustical problems that create uncomfortable conditions for the passenger, not to mention the unavoidable loss of ductility associated with the increase in mechanical strength.
The second track consists of reducing the density of the steels by alloying them with other, lighter metals. Among these alloys, the low-density ones have attractive mechanical and physical properties while making it possible to significantly reduce the weight.
In particular, US 2003/0145911 discloses a Fe—Al—Mn—Si light steel having good formability and high strength. However, the ultimate tensile strength of such steels does not go beyond 800 MPa which does not allow taking full advantage of their low density for parts of all kinds of geometry.
A purpose of various embodiments of the present invention therefore is to provide a steel sheet presenting a density below 7.2, an ultimate tensile strength of at least 1300 MPa, a yield strength of at least 1200 MPa and a tensile elongation of at least 5%.
In a preferred embodiment, the steel sheet according to an embodiment of the present invention presents a density equal or below 7.1 or even equal or below 7.0, a ultimate tensile strength of at least 1400 MPa, a yield strength of at least 1300 MPa and a tensile elongation of at least 6%.
This object is achieved by providing a cold rolled and annealed steel sheet in accordance with a first embodiment of the present invention, comprising by weight: 0.6<C<1.3%, 15≤Mn<35%, 6.0≤Al<15%, Si≤2.40% S≤0.015%, P≤0.1%, N≤0.1%, possibly one or more optional elements chosen among Ni, Cr and Cu in an individual amount of up to 3% and possibly one or more elements chosen among B, Ta, Zr, Nb, V, Ti, Mo, and W in a cumulated amount of up to 2.0%, the remainder of the composition making up of iron and inevitable impurities resulting from elaboration; the microstructure of said sheet comprising at least 0.1% of intragranular kappa carbides, wherein at least 80% of such kappa carbides have an average size below 30 nm, optionally up to 10% of granular ferrite, the remainder being made of austenite; an average grain size of the austenite being below 6 μm, an average aspect ratio of the austenite being between 2 and 10, an average grain size of the ferrite, when present, being below 5 μm, and an average aspect ratio of the ferrite, when present, being below 3.0; and the density of said steel sheet being equal or below 7.2 and its tensile elongation being at least 5.0%.
Another object is achieved by providing a method for producing a steel sheet comprising: feeding a slab which composition comprising by weight: 0.6<C<1.3%, 15≤Mn<35%, 6.0≤Al<15%, Si≤2.40%, S≤0.015%, P≤0.1%, N≤0.1%, possibly one or more optional elements chosen among Ni, Cr and Cu in an individual amount of up to 3% and possibly one or more elements chosen among B, Ta, Zr, Nb, V, Ti, Mo, and W in a cumulated amount of up to 2.0%, the remainder of the composition making up of iron and inevitable impurities resulting from elaboration; reheating the slab at a temperature above 1000° C. and hot rolling it with a final rolling temperature of at least 800° C. to provide a hot rolled sheet; coiling the hot rolled steel sheet at a coiling temperature below 600° C. to provide a coiled hot rolled sheet, first cold-rolling the coiled hot rolled steel sheet at a reduction comprised between 30 and 80% to provide a first cold rolled sheet, first annealing the first cold rolled sheet by heating it up to a first annealing temperature between 700 and 1000° C., holding it at the first annealing temperature during less than 5 minutes and cooling it at a rate of at least 30° C./s to provide a first annealed sheet; second cold-rolling the first annealed steel sheet at a reduction comprised between 10 and 50% to provide a second cold rolled sheet; second annealing the second cold sheet by heating it up to a second annealing temperature between 400 and 700° C., holding it at the second annealing temperature during 1 minute to 150 hours and cooling it at a rate of at least 30° C./s.
Other characteristics and advantages of the invention will become apparent from the following detailed description of the invention.
Without willing to be bound by any theory it seems that the low density steel sheet according to the invention allows for an improvement of the mechanical properties thanks to this specific microstructure.
Regarding the chemical composition of the steel, carbon plays an important role in the formation of the microstructure and reaching of the targeted mechanical properties. Its main role is to stabilize austenite which is the main phase of the microstructure of the steel as well as to provide strengthening. Carbon content below 0.6% will decrease the proportion of austenite, which leads to the decrease of both ductility and strength of the alloy.
As a main constituent element of the intragranular kappa carbide (Fe,Mn)3AlCx, carbon promotes the precipitation of such carbides. However, a carbon content above 1.3% can promote the precipitation of such carbides in a coarse manner on the grain boundaries, what results in the decrease of the ductility of the alloy.
Preferably, the carbon content is between 0.80 and 1.3%, more preferably between 0.8 and 1.0% by weight so as to obtain sufficient strength.
Manganese is an important alloying element in this system, mainly due to the fact that alloying with very high amounts of manganese and carbon stabilizes the austenite down to room temperature, which can then tolerate high amounts of aluminium without being destabilized and transformed to ferrite or martensite. To enable the alloy to have a superior ductility, the manganese content has to be equal or higher to 15%. However, when the manganese content is over 35%, the precipitation of β-Mn phase will deteriorate the ductility of the alloy.
Therefore, the manganese content should be controlled to be equal or greater than 15.0%, but lower than equal to 35%. In a preferred embodiment, it is equal or greater than 15.5% or even than 16.0%. Its amount is more preferably between 18 and 30% and even between 18 and 25%.
Aluminum addition to high manganese austenitic steels effectively decreases the density of the alloy. In addition, it considerably increases the stacking fault energy (SFE) of the austenite, leading in turn to a change in the strain hardening behavior of the alloy. Aluminium is also one of the primary elements of nanosized kappacarbide (Fe,Mn)3AlCx and therefore its addition significantly enhances the formation of such carbides. The aluminium concentration of the present alloys should be adjusted, on one hand, to guarantee the austenite stability and the precipitation of kappa carbides, and on the other to control the formation of ferrite. Therefore, the aluminium content should be controlled to be equal or greater than 6.0%, but lower than equal to 15%. In a preferred embodiment, aluminium content is between 7 and 12% and preferably between 8 and 10%.
Silicon is a common alloying element for high manganese and aluminium steels. It has a very strong effect on the formation of ordered ferrite D03. Besides, silicon was shown to enhance the activity of carbon in austenite and to increase the partitioning of carbon into the kappa carbides. In addition, silicon has been described as an effective alloying element that can be used to delay or prevent the precipitation of brittle β-Mn phase. However, above a content of 2.40%, it reduces the elongation and tends to form undesirable oxides during certain assembly processes, and it must therefore be kept below this limit. Preferably, the content of silicon is below 2.0% and advantageously below 1.0
Sulfur and phosphorus are impurities that embrittle the grain boundaries. Their respective contents must not exceed 0.03 and 0.1% so as to maintain sufficient hot ductility.
Nitrogen content must be 0.1% or less so as to prevent the precipitation of AlN and the formation of volume defects (blisters) during solidification.
Nickel has a positive effect on penetration of hydrogen into the steel and, therefore it can be used as a diffusion barrier to hydrogen. Nickel can also be used as an effective alloying element because it promotes the formation of ordered compounds in ferrite, such as the B2 component, leading to additional strengthening. However, it is desirable, among others for cost reasons, to limit the nickel addition to a maximum content of 4.0% or less and preferably between 0.1 and 2.0%. In another embodiment, the nickel amount is below 0.1%.
Chromium may be used as optional element for increasing the strength of the steel by solution hardening. It also enhances the high temperature corrosion resistance of the steels according to the invention. However, since chromium reduces the stacking fault energy, its content must not exceed 3.0% and preferably between 0.1% and 2.0% or between 0.1 and 1.0%. In another embodiment, the chromium amount is below 0.1%.
Likewise, optionally, an addition of copper with a content not exceeding 3.0% is one means of hardening the steel by precipitation of copper-rich precipitates. However, above this content, copper is responsible for the appearance of surface defects in hot-rolled sheet. Preferably, the amount of copper is between 0.1 and 2.0%, or between 0.1 and 1.0%. In another embodiment, the chromium amount is below 0.1%.
Boron has a very low solid solubility and a strong tendency to segregate at the grain boundaries, interacting strongly with lattice imperfections. Therefore, boron can be used to limit the precipitation of intergranular kappa carbides. Preferably, the amount of boron is below 0.1%.
Niobium can simultaneously increase strength and toughness in the steel since it is an effective grain refiner. In addition, tantalum, zirconium, niobium, vanadium, titanium, molybdenum and tungsten are also elements that may optionally be used to achieve hardening and strengthening by precipitation of nitrides, carbo-nitrides or carbides. However, when their cumulated amount is above 2.0%, preferably above 1.0%, there is a risk that an excessive precipitation may cause a reduction in toughness, which has to be avoided.
The microstructure of the steel sheet according to embodiment of the invention comprises at least 0.1% of kappa carbides, optionally up to 10% of granular ferrite, the remainder being made of austenite.
The austenitic matrix presents an average grain size below 6 μm and preferably below 4 μm, more preferably below 3 μm and has an average aspect ratio between 2 and 10, preferably between 2.0 and 6.0, or even between 2.0 and 4.0.
The kappa carbides (Fe,Mn)3AlCx are present in the microstructure of the steel sheet according to the invention, with a minimum amount of 0.1% in area fraction, preferably of 0.5%, more preferably of 1.0% and advantageously of more than 3%. At least 80% of such kappa carbides have an average size below 30 nm, preferably below 20 nm, more preferably below 15 nm, advantageously below 10 nm or even below 5 nm. They precipitate inside the austenitic grains (so called intragranular kappa carbides). The homogenous and coherent precipitation of the nanosized -kappa carbide increases the strength of the alloy. The presence of intergranular kappa carbides is not admitted as such intergranular coarse kappa carbides may cause a decrease in the ductility of the steel.
Ferrite can also be present in the microstructure of the sheet according to the invention up to an amount of 10.0% in area fraction, preferably up to 5.0% or more preferably up to 3.0%. However, the ferrite morphology is limited to a granular geometry, excluding ferrite in form of bands, as they drastically degrade the ductility and formability of the steel. When present, the ferritic grains have an average grain size below 5 μm and preferably below 1 μm. The average aspect ratio of the ferrite, when present, is below 3.0 and preferably below 2.5. Such ferrite can be under the form of regular disordered ferrite a or ordered as a B2 structure with a (Fe,Mn)Al composition or as a D03 structure with a (Fe,Mn)3Al composition is also possible, so that a, B2 and D03 structures can, in general, be observed in the steel according to the invention.
To protect the steel sheet according to the invention from corrosion, in a preferred embodiment, the steel sheet is covered by a metallic coating. The metallic coating can be an aluminum-based coating or a zinc-based coating.
Preferably, the aluminium-based coated comprises less than 15% Si, less than 5.0% Fe, optionally 0.1 to 8.0% Mg and optionally 0.1 to 30.0% Zn, the remainder being Al.
Advantageously, the zinc-based coating comprises 0.01-8.0% Al, optionally 0.2-8.0% Mg, the remainder being Zn.
The steel sheet according to embodiments of the present 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, which comprises the following steps:
The steel sheets according to embodiments of the present invention are preferably produced through a method in which an semi product, such as slabs, thin slabs, or strip made of a steel according to the present invention having the composition described above, is cast, the cast input stock is heated to a temperature above 1000° C., preferably above 1050° C. and more preferably above 1100° C. or 1150° C. or used directly at such a temperature after casting, without intermediate cooling.
The hot-rolling step is performed at a temperature above 800° C. To avoid any cracking problem through lack of ductility by the formation of ferrite in bands, the final rolling temperature is preferably above or equal to 850° C.
After the hot-rolling, the strip has to be coiled at a temperature below 600° C. and preferably above 350° C. In a preferred embodiment, the coiling is performed between 350 and 450° C. to avoid excessive kappa carbides precipitation.
The hot-rolled product obtained by the process described above is cold-rolled after a possible prior pickling operation has been performed in the usual manner.
The first cold-rolling step is performed with a reduction rate between 30 and 80%, preferably between 50 and 70%.
After this rolling step, a first annealing is performed by heating the sheet up to an annealing temperature comprised between 700 and 1000° C., holding it at such temperature during less than 5 minutes and cooling it at a rate of at least 30° C./s, more preferably of at least 50° C./s and even more preferably of at least 70° C./s. Preferably, this annealing is carried out continuously.
By controlling annealing temperature and time, either a fully austenitic or a two phase structure with the characteristics above can be obtained.
After this first annealing step, pre-straining of the materials was performed by means of a second cold rolling step with a reduction rate between 10 and 50%, preferably between 15% and 40%. The steel sheet may have increased strength through strain hardening by undergoing this second cold rolling step.
After this second rolling step, a second annealing is performed by heating the sheet up to an annealing temperature comprised between 400 and 700° C., holding it at such temperature during 1 minutes to 150 hours and cooling it at a rate of at least 30° C./s, more preferably of at least 50° C./s and even more preferably of at least 70° C./s. Preferably, this annealing is carried out continuously. During this second annealing a compromise is obtained between ultra-high strength and formability via the intragranular kappa carbide precipitation and partial recovery of the material.
After those two annealing steps, the steel sheet may optionally be submitted to a metallic coating operation to improve its protection against corrosion. The coating process used can be any process adapted to the steel of the embodiments of the present invention. Electrolytic or physical vapor deposition can be cited, with a particular emphasis on Jet Vapor Deposition. The metallic coating can be based on zinc or on aluminium, for example.
Five grades, which compositions are gathered in table 1, were cast in slabs and processed following the process parameters gathered in table 2.
C
5.72
5
C
6
C
7
8
11
5
6
7
8
10
11
170
The resulting samples were then analyzed and the corresponding microstructure elements and mechanical properties were respectively gathered in table 3 and 4.
5
No
6
No
7
No
8
12
11
Yes
No samples showed any presence of intergranular Kappa carbides nor of β-Mn phase, except samples 8 and 11. Kappa carbides amounts of trials 1 to 4 were above 0.1%, whereas they were under 0.1% for trials 5, 6 and 7. More than 80% of the Kappa carbides of trials 1 to 4 and 9 and 10 had an average grain size below 20 nm.
The examples show that the steel sheets according to the invention are the only one to show all the targeted properties thanks to their specific composition and microstructures.
| Number | Date | Country | Kind |
|---|---|---|---|
| PCT/IB2016/000696 | May 2016 | WO | international |
This is a Continuation of U.S. patent application Ser. No. 16/302,999 filed on Nov. 19, 2018 which is a National Phase of PCT/162017/000615, filed on May 23, 2017 which claims priority to International Patent Application PCT/162016/000696, filed on May 24, 2016. All of the above are hereby incorporated by reference herein.
| Number | Date | Country | |
|---|---|---|---|
| Parent | 16302999 | Nov 2018 | US |
| Child | 18529599 | US |
