Note : Les descriptions sont présentées dans la langue officielle dans laquelle elles ont été soumises.
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High strength cold rolled and galvannealed steel sheet and
manufacturing process thereof
The present invention relates to a high strength cold rolled and galvannealed
steel sheet and to a method to obtain such steel sheet.
Decreasing the weight of vehicles to reduce CO2 emissions is a major
challenge in the automotive industry. This weight saving must be coupled with
safety requirements. To meet these requirements, an increased demand of
very high strength steels with tensile strength higher than 1450MPa have led
to steelmaking industry to continuously develop new grades.
These steels are usually coated with a metallic coating improving properties
such corrosion resistance. The metallic coatings can be deposited by hot-dip
galvanizing after the annealing of the steel sheets. To obtain an improved
spot weldability, the hot dip coating can be followed by an alloying treatment
to obtain a galvannealed steel sheet, so that the iron of the steel sheet
diffuses towards the zinc coating in order to obtain a zinc-iron alloy on the
steel sheet.
The publication W02019188190 relates to a high strength galvanized or
galvannealed steel sheet, having a tensile strength higher than 1470MPa. To
obtain such a level of tensile strength, the carbon content of the steel sheet
is
comprised between 0.200%wt and 0.280%wt, which may reduce the
weldability of the steel sheet. Moreover, the formation of ferrite and
bainite,
whose total amount of the sum of the two with pearlite is less than 2%, is
avoided to ensure good level of tensile strength. To do so, the soaking step
after cold rolling has to be performed at a temperature above Ac3.
The publication W02016199922 relates to a high strength galvannealed steel
sheet with a tensile strength higher than 1470MPa. The high amount of
carbon between 0.25% and 0.70% allow to obtain this high level of tensile
strength. But the weldability of the steel sheet may be reduced. After the
alloying step, the steel sheet must be cooled in a controlled manner, in order
to obtain at the end of the cooling, more than 10% of retained austenite.
After
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this cooling step, the galvannealed steel sheet is subjected to a step of
tempering to obtain tempered martensite, to promote bainite transformation
and to cause carbon to concentrate into retained austenite, in order to obtain
the desired final microstructure : between 10% and 60% of retained austenite,
less than 5% of high temperature tempered martensite, less than 5% of low
temperature tempered martensite, less than 10% of fresh martensite, less
than 15% of ferrite, less than 10% of pearlite, the balance being bainite.
These controlled cooling and tempering steps complicate the manufacturing
process.
The purpose of the invention therefore is to solve the above-mentioned
problem and to provide a galvannealed steel sheet having a tensile strength
above or equal to1450MPa and easily processable on conventional process
route.
In a preferred embodiment of the invention, the yield strength YS is above or
equal to 1050MPa.
The object of the present invention is achieved by providing a steel sheet
according to claim 1. The steel sheet can also comprise characteristics of
anyone of claims 2 to 5. Another object is achieved by providing the method
according to claim 6. The method can also comprise characteristics of anyone
of claims 7 to 8.
The invention will now be described in detail and illustrated by examples
without introducing limitations.
Hereinafter, Ac3 designates the temperature above which microstructure is
fully austenitic, Ad 1 designates the temperature above which austenite begins
to form.
The composition of the steel according to the invention will now be described,
the content being expressed in weight percent.
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The carbon content is comprised from 0.15% to 0.25% to ensure a
satisfactory strength. If the carbon content is too high, the weldability of
the
steel sheet is insufficient. A carbon content level below 0.15% does not make
it possible to achieve a sufficient tensile strength.
The manganese content is comprised from 2.4% to 3.5% to ensure
satisfactory strength and to limit bainitic transformation. Above 3.5% of
addition, the risk of central segregation increases to the detriment of the
ductility. An amount of at least 2.4% of manganese is mandatory in order to
provide the strength and hardenability of the steel sheet as well as to
stabilize
austenite. Preferably, the manganese content is comprised from 2.5% to
3.2%.
According to the invention, the silicon content is comprised from 0.30% to
0.90%. Silicon is an element participating in the hardening in solid solution.
A
silicon addition of at least 0.30% makes it possible to obtain sufficient
hardening of the ferrite and bainite. Above 0.90%, silicon oxides form at the
surface, which impairs the coatability of the steel. Moreover, silicon can
impair
the weldability. In a preferred embodiment, the silicon content is comprised
from 0.30% to 0.70%. In an other preferred embodiment, the silicon content is
comprised from 0.30% to 0.50%.
According to the invention, the chromium content is comprised from 0.30% to
0.70%. Chromium is an element participating in the hardening in solid
solution. A chromium content level below 0.30% does not make it possible to
achieve a sufficient tensile strength. The chromium content has to be below
or equal to 0.70% to obtain a satisfactory elongation at break and limit
costs.
According to the invention, the molybdenum content is comprised between
0.05% and 0.35%. A molybdenum addition of at least 0.05% improves the
hardenability of the steel and limits bainitic transformation before and
during
the hot dip coating. Above 0.35%, the addition of molybdenum is costly and
ineffective in view of the properties which are required. Preferably, the
molybdenum content is comprised between 0.05% and 0.20%.
According to the invention, the aluminium content is comprised between
0.001% and 0.09% as it is a very effective element for deoxidizing the steel
in
the liquid phase during elaboration. The aluminium content is lower than
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0.09% to avoid oxidation problems and ferrite formation during cooling after
intercritical soaking. Preferably the aluminium amount is between 0.001% and
0.06%.
Titanium is added in an amount between 0.01% and 0.06% to provide
precipitation strengthening and to protect boron against the formation of BN.
According to the invention, the boron content is comprised between 0.0010%
and 0.0040%. As molybdenum, boron improves the hardenability of the steel.
The boron content is lower than 0.0040% to avoid a risk of breaking the slab
during continuous casting. Niobium is added between 0.01% and 0.05% to
refine the austenite grains during hot-rolling and to provide precipitation
strengthening.
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 0.008 % for N.
The microstructure of the cold rolled and galvannealed steel sheet according
to the invention will now be described.
After cold rolling, the cold rolled steel sheet is heated to a soaking
temperature Tsoak and maintained at said temperature for a holding time tsoak,
both chosen in order to obtain, at the end of this intercritical soaking, a
steel
sheet with a microstructure consisting of between 85% and 95% of austenite
and between 5% and 15% of ferrite.
A part of austenite is transformed in bainite after the cooling after the
intercritical soaking, during the hot dip coating.
During the cooling step at room temperature after the galvannealing step,
austenite transforms in martensite. The cold rolled and galvannealed steel
sheet has a final microstructure consisting of, in surface fraction, between
80% and 90% of martensite, the balance being ferrite and bainite.
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These 80% to 90% of martensite ensures a good level of tensile strength.
This martensite comprises auto tempered martensite and fresh martensite.
The sum of ferrite and bainite is between 10% and 20% in order to ensure
that the galvannealing step is successful.
5 In a preferred embodiment of the invention, the ferrite is above or equal
to
5%. In an other preferred embodiment of the invention, the bainite is above or
equal to 5%.
The cold rolled and galvannealed steel sheet according to the invention has a
tensile strength TS above or equal to 1450 MPa. In a preferred embodiment
of the invention, the yield strength YS is above or equal to 1050 MPa. TS and
YS are measured according to ISO standard ISO 6892-1.
The 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 heated to a temperature
comprised from 1150 C to 1300 C, so to make it possible to ease hot rolling,
with a final hot rolling temperature FRT comprises from 850 C to 950 C.
The hot-rolled steel is then cooled and coiled at a temperature Tcoil
comprised from 250 C to 650 C.
After the coiling, the sheet is pickled to remove oxidation.
The steel sheet is annealed to an annealing temperature TA comprised from
500 C and 650 C and maintaining at said temperature TA for a holding time tA
in order to improve the cold-rollability.
After the annealing, the sheet can be pickled to remove oxidation.
The steel sheet is then cold rolled with a reduction rate between 20% and
80%, to obtain a cold rolled steel sheet, having a thickness that can be, for
example, between 0.7 mm and 3 mm, or even better in the range of 0.8 mm
to 2 mm. The cold-rolling reduction ratio is preferably comprised between
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20% and 80%. Below 20%, the recrystallization during subsequent heat-
treatment is not favored, which may impair the ductility of the cold-rolled
and
galvannealed steel sheet. Above 80%, the force required to deform during
cold-rolling would be too high.
The cold rolled steel sheet is then reheated to a soaking temperature Tsoak
comprised from Ad 1 and Ac3 and maintained at said temperature Tsoak for a
holding time tsoak comprised from 30s and 200s so to obtain, at the end of
this
intercritical soaking, a microstructure comprising between 85% and 95% of
austenite and between 5% and 15% of ferrite.
The cold rolled steel sheet is then cooled to a temperature comprised from
440 C to 480 C in order for the sheet to reach a temperature close to the
coating bath, before to be coated by continuous dipping in a zinc bath at a
temperature Tzn comprised from 450 C to 480 C. The hot dip coated steel
sheet is then reheated to a galvannealed temperature TGA comprised from
510 C to 550 C, and maintained at said temperature TGA for a holding time tGA
comprised from lOs to 30s.
The steel sheet is then cooled to room temperature to obtain a cold rolled and
galvannealed steel sheet.
In a preferred embodiment of the invention, the annealing step of the hot
rolled steel sheet is performed by batch in an inert atmosphere, at a heat-
treating temperature TA comprised from 500 C to 650 C and maintaining at
said TA temperature for a holding time tA comprised from 1800s to 36000s.
In an other preferred embodiment of the invention, the annealing step of the
hot rolled steel sheet is performed by continuous annealing, at a heat-
treating
temperature TA comprised from 550 C to 650 C. and maintaining at said TA
temperature for a holding time tA comprised from 30s to 100s.
The invention will be now illustrated by the following examples, which are by
no way !imitative.
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Examples
2 grades, which compositions are gathered in table 1, were cast in
semi-products and processed into steel sheets following the process
parameters gathered in table 2.
Table 1 - Compositions
The tested compositions are gathered in the following table wherein
the element contents are expressed in weight percent.
Ac1( Ac3
Steel C Mn Si Cr Mo Al Ti B Nb P S N
C) ( C)
A 0.18 2.8 0.49
0.41 0.10 0.04 0.03 0.0022 0.02 0.01 0.0020.004 735 805
B 0.15 2.6 0.45 0.48 0.03 0.01 0.03 0.0020
0.013 0.01 0.0020.004 715 820
1() Steel A is according to the invention. Steel B out of the invention
Underlined values: not corresponding to the invention
For a given steel, Ad 1 and Ac3 are measured through dilatometry tests and
metallography analysis.
Table 2 ¨ Process parameters
Steel semi-products, as cast, were reheated to 1200 C, hot rolled with
finish rolling temperature FRT of 910 C, coiled at a temperature Tod! of 550
C.
Some steel sheets are first annealed to a temperature TA of 600 C, and
maintained at said TA temperature for a holding time tA before to be pickled.
Steel sheets are then cold rolled at a reduction rate of 45%. The cold rolled
steel sheets are reheated to a soaking temperature Tsoak and maintained at
said temperature during tsoak, and coated by hot dip coating in a zinc bath at
a
temperature Tzn of 460 C, followed by galvannealing, with a galvannealed
temperature TGA comprised from 510 C to 550 C and maintained at said
temperature during tGA of 20s. The following specific conditions were applied:
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Trials Steel Annealing Soaking
Galvannealing
TA( C) Tsoak( C) tsoak (5) TGA ( C)
1 A 600 790 180 540
2 A 600 790 138 520
3 A 600 843 138 520
4 A 600 810 138 520
B - 790 180 520
Underlined values: not corresponding to the invention
5 The cold rolled steel sheets were analyzed after soaking and the
corresponding microstructure elements were gathered in table 3.
Table 3: Microstructure of the cold rolled steel sheets after soaking
Trials Austenite (c)/0) Ferrite (c)/0)
1 94 6
2 94 6
3 wo 0
4 wo 0
5 90 10
Underlined values: not corresponding to the invention
In order to quantify this microstructure at the end of the soaking, the steel
sheets are quenched after the soaking to transform 100% of austenite in
martensite, austenite being instable at room temperature. Martensite amount
thus corresponds to the austenite amount at the end of the soaking.
Martensite and ferrite amounts are then quantified through image analysis.
The cold rolled and galvannealed steel sheets were then analyzed and the
corresponding microstructure elements and properties were respectively
gathered in table 4 and 5.
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Table 4: Microstructure of the cold rolled and qalvannealed steel sheets
Martensite (c)/o) Ferrite + Bainite Ferrite (c)/0) Bainite (`)/0)
Trials
(0/0)
1 85 15 5 10
2 89 11 5 6
3 98 2 0 2
4 92 8 0 8
75 25 15 10
Underlined values: not corresponding to the invention
5
The surface fractions are determined through the following method: a
specimen is cut from the cold-rolled and galvannealed steel sheet, polished
and etched with a reagent (Nital), to reveal the microstructure. The
determination of the surface fraction of each constituent are performed with
image analysis through optical microscope: Martensite has a darker contrast
than ferrite and bainite. Bainite is quantified by measuring the difference of
martensite fractions of the sample quenched after soaking and of the sample
cooled after galvannealing. The bainite is identified thanks to the carbides
inside this bainite.
Table 5: Properties of the cold rolled and qalvannealed steel sheets
Trials TS (MPa) YS (MPa) Success of GA
1 1522 1095 Yes
2 1634 1055 Yes
3 1519 1163 No
4 1611 1096 No
5 1363 954 Yes
Underline values: Insufficient TS or YS, or fail of the galvannealing step.
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The success of the galvannealing step is checked by measuring the amount
of iron in the coating. The steel is galvannealed if the iron content in the
coating is between 7% and 12%.
5 The examples show that the steel sheet according to the invention, namely
examples 1 and 2 are the only one to show all the targeted mechanical
properties with success of the galvannealing, thanks to their specific
composition and microstructures. The mechanical properties are ensured
thanks to the martensite between 80% and 90%. The galvannealing step is
10 ensured thanks to the presence of ferrite and bainite in a total
comprised
between 10% and 20%.
In trials 3 and 4 steel A is heated above a temperature Tsoak ensuring between
85% and 95% of austenite and between 5% and 15% of ferrite at the end of
the soaking, thus forming too many austenite and not enough ferrite. This
leads to the formation of less than 10% of the sum of ferrite and bainite at
the
end of the hot dip coating, which hinder the galvannealing step.
In Trial 5, the absence of molybdenum, which is a hardening element
delaying the bainitic transformation, leads to the formation of 25% of the sum
of ferrite and bainite at the end of the hot dip coating. Then, martensite
formed during the last cooling step is less than 80% which leads to a low
value of mechanical properties.
