TECHNICAL FIELD
[0001] The present invention relates to high strength steel strips and sheets suitable for
applications in automobiles. In particular, the invention relates to high ductility
high strength complex phase cold rolled steel having a tensile strength of at least
1380 MPa and an excellent formability.
BACKGROUND ART
[0002] For a great variety of applications increased strength levels are a pre-requisite
for lightweight constructions in particular in the automotive industry, since car
body mass reduction results in reduced fuel consumption.
[0003] Automotive body parts are often stamped out of sheet steels, forming complex structural
members of thin sheet. However, such parts cannot be produced from conventional high
strength steels, because of a too low formability of the complex structural parts.
For this reason, multi-phase Transformation Induced Plasticity aided steels (TRIP
steels) have gained considerable interest in the last years, in particular for use
in auto body structural parts and as seat frame materials.
[0004] TRIP steels possess a multi-phase microstructure, which includes a meta-stable retained
austenite phase, which is capable of producing the TRIP effect. When the steel is
deformed, the austenite transforms into martensite, which results in remarkable work
hardening. This hardening effect acts to resist necking in the material and postpones
failure in sheet forming operations. The microstructure of a TRIP steel can greatly
alter its mechanical properties. The most important aspects of the TRIP steel microstructure
are the volume percentage, size and morphology of the retained austenite phase, as
these properties directly affect the austenite to martensite transformation, when
the steel is deformed. There are several ways by which it is possible to chemically
stabilize austenite at room temperature. In low alloy TRIP steels the austenite is
stabilized through its carbon content and the small size of the austenite grains.
The carbon content necessary to stabilize austenite is approximately 1 wt. %. However,
high carbon content in steel cannot be used in many applications because of impaired
weldability.
[0005] Specific processing routs are therefore required to concentrate the carbon into the
austenite in order to stabilize it at room temperature. A common TRIP steel chemistry
also contains small additions of other elements to help stabilizing the austenite
as well as aiding the creation of microstructures which partition carbon into the
austenite. In order to inhibit the austenite to decompose during the bainite transformation
it has generally been considered necessary to add relatively high amounts of manganese
and silicon.
[0006] TRIP-aided steel with a Bainitic Ferrite matrix (TBF)-steels have been known for
long and attracted a lot of interest, mainly because the bainitic ferrite matrix allows
an excellent stretch flangability. Moreover, the TRIP effect ensured by the strain-induced
transformation of metastable retained austenite islands into martensite, remarkably
improves their drawability.
[0007] Complex Phase (CP) steels are characterized by very high strength levels and at the
same time a high yield point and are therefore often used for crash-relevant components
in cars.
[0008] Although these steels disclose several attractive properties there is a demand for
steel sheets having a higher tensile strength in combination with a good workability,
in particular, in applications where the local elongation and is great of importance
for avoiding edge tearing, such as for advanced forming operations as bending and
roll forming.
DISCLOSURE OF THE INVENTION
[0009] The present invention is directed to cold rolled steels having a tensile strength
of at least 1380 MPa and an excellent formability, wherein it should be possible to
produce the steel sheets on an industrial scale in a Continuous Annealing Line (CAL).
The invention aims at providing a steel having a composition and microstructure that
can be processed to complicated high strength structural members, where the local
elongation is of importance. In particular, the steel strip or sheet of the present
invention should have a high hole expandability as expressed by the Hole Expanding
Ratio (HER) or (λ). In this application lambda (λ) will be used for this parameter.
Naturally, the steel should also have a good weldability, in particular with respect
to Resistance Spot Welding (RSW) since RSW is the dominating welding process used
in the mass fabrication of automobiles.
DETAILED DESCRIPTION
[0010] The invention is described in the claims.
[0011] The steel sheet has a composition consisting of the following alloying elements (in
wt. %):
C |
0.15 - 0.25 |
Si |
0.7 - 1.6 |
Mn |
2.2 - 3.2 |
Cr |
≤ 0.8 |
Mo |
≤ 0.2 |
Al |
0.03 - 1.0 |
Nb |
≤ 0.04 |
V |
≤ 0.04 |
Ti |
0.01 - 0.04 |
B |
0.001 - 0.005 |
Ti/B |
5 - 30 |
Cu |
≤ 0.15 |
Ni |
≤ 0.15 |
balance Fe apart from impurities,
the balance consists of iron and impurities.
[0012] The importance of the separate elements and their interaction with each other as
well as the limitations of the chemical ingredients of the claimed alloy are briefly
explained in the following. All percentages for the chemical composition of the steel
are given in weight % (wt. %) throughout the description. Upper and lower limits of
the individual elements can be freely combined within the limits set out in the claims.
The arithmetic precision of the numerical values can be increased by one or two digits
for all values given in the present application. Hence, a value reported as e.g. 0.1
% can also be expressed as 0.10 or 0.100 %. The amounts of the microstructural constituents
are given in volume % (vol. %).
C: 0.15 - 0.25 %
[0013] C stabilizes the austenite and is important for obtaining sufficient carbon within
the retained austenite phase. C is also important for obtaining the desired strength
level. Generally, an increase of the tensile strength in the order of 100 MPa per
0.1 %C can be expected. When C is lower than 0.15 % then it is difficult to attain
a tensile strength of 1380 MPa. If C exceeds 0.25 %, then the weldability is impaired.
The upper limit may thus be 0.24, 0.23 or 0.22 %. The lower limit may be 0.16, 0.17,
0.18, 0.19, or 0.20 %.
Si: 0.7 - 1.6 %
[0014] Si acts as a solid solution strengthening element and is important for securing the
strength of the thin steel sheet. Si suppresses the cementite precipitation and is
essential for austenite stabilization.
[0015] However, if the content is too high, then too much silicon oxides will form on the
strip surface, which may lead to cladding on the rolls in the CAL and, as a result
thereof, to surface defects on subsequently produced steel sheets. The upper limit
is therefore 1.6 % and may be restricted to 1.5, 1.4, 1.3 or 1.2 %. The lower limit
may be 0.75 or 0.80 %.
Mn: 2.2 - 3.2 %
[0016] Manganese is a solid solution strengthening element, which stabilises the austenite
by lowering the M
s temperature and it also prevents ferrite and pearlite to be formed during cooling.
In addition, Mn lowers the A
c3 temperature and is important for the austenite stability. At a content of less than
2.2 % it might be difficult to obtain the desired amount of retained austenite, a
tensile strength of 980 MPa and the austenitizing temperature might be too high for
conventional industrial annealing lines. In addition, at lower contents it may be
difficult to avoid the formation of polygonal ferrite. However, if the amount of Mn
is higher than 2.8 %, problems with segregation may occur because Mn accumulates in
the liquid phase and causes banding, resulting in a potentially deteriorated workability.
The upper limit may therefore be 3.1, 3.0, 2.9, 2.8, 2.7, 2.6, 2.5 or 2.4 %. The lower
limit may be 2.3 or 2.4%.
Cr: ≤ 0.8 %
[0017] Cr is effective in increasing the strength of the steel sheet. However, a deliberate
addition of Cr is not necessary according to the present invention. Cr is an element
that forms ferrite and retards the formation of pearlite and bainite. The A
c3 temperature and the M
s temperature are only slightly lowered with increasing Cr content. Cr results in an
increased amount of stabilized retained austenite. The amount of Cr is limited to
0.8 %. The upper limit may be 0.75, 0.70, 0.65, 0.60, 0.55, 0.50, 0.45 or 0.40, 0.35,
0.30 or 0.25 %. The lower limit may be 0.01, 0.05, 0.10, 0.15, 0.20 or 0.25 %. The
lower limit of Cr is 0.10 % in a preferred embodiment of the present invention.
Al: 0.03 - 1.0 %
[0018] Al promotes ferrite formation and is also commonly used as a deoxidizer. Al, like
Si, is not soluble in the cementite and therefore it delays the cementite formation
during bainite formation considerably. Additions of Al result in a remarkable increase
in the carbon content in the retained austenite. However, the M
s temperature is also increased with increasing Al content. A further drawback of Al
is that it results in a drastic increase in the A
c3 temperature. However, a main disadvantage of Al is its segregation behavior during
casting. During casting Mn is enriched in the middle of the slabs and the Al-content
is decreased. Therefore, in the middle of the slab a significant austenite stabilized
region or band may be formed. This results, at the end of the processing, in martensite
banding and in the that low strain internal cracks are formed in the martensite bands.
On the other hand, Si and Cr are also enriched during casting. Hence, the propensity
for martensite banding may be reduced by alloying with Si and Cr, since the austenite
stabilization due to the Mn enrichment is counteracted by these elements. For these
reasons the Al content is preferably limited. The upper level may be 0.9, 0.8, 0.7,
0.6, 0.5, 0.4, 0.3, 0.2 or 0.1 %. The lower limit may be set to 0.04, 0.05, 0.06,
0.07, 0.08, 0.09 or 0.1 %. If Al is used for deoxidation only, then the upper level
may then be 0.09, 0.08, 0.07 or 0.06 %. For securing a certain effect the lower level
may set to 0.03 or 0.04 %.
Nb: ≤ 0.04%
[0019] Nb is commonly used in low alloyed steels for improving strength and toughness, because
of its influence on the grain size. Nb increases the strength elongation balance by
refining the matrix microstructure and the retained austenite phase due to the precipitation
of NbC. The steel may contain Nb in an amount of ≤ 0.04 %, preferably ≤ 0.03 %. A
deliberate addition of Nb is not necessary according to the present invention. The
upper limit may therefore be restricted to ≤ 0.01 %.
V: ≤ 0.04%
[0020] The function of V is similar to that of Nb in that it contributes to precipitation
hardening and grain refinement. The steel may contain V in an amount of ≤ 0.04 %,
preferably ≤ 0.03 %. A deliberate addition of V is not necessary according to the
present invention. The upper limit may therefore be restricted to ≤ 0.01 %.
Ti: 0.01 - 0.04 %
[0021] Ti is commonly used in low alloyed steels for improving strength and toughness, because
of its influence on the grain size by forming carbides, nitrides or carbonitrides.
In particular, Ti is a strong nitride former and can be used to bind the nitrogen
in the steel. However, the effect tends to be saturated above 0.04 %. In order to
having a good fixation of N to Ti the lower amount should be 0.01 % and may be set
to 0.02 %.
B: 0.001 - 0.005 %
[0022] B suppresses the formation of ferrite and improves the weldability of the steel sheet.
In order to have a noticeable effect at least 0.001 % should be added. However, excessive
amounts of B deteriorate the workability. The upper limit is therefore 0.005 %. A
preferred range is 0.002 - 0.004 %.
Ca ≤ 0.01
[0023] Ca may be used for the modification of the non-metallic inclusions. The upper limit
is 0.01% and may be set to 0.005 or 0.004 %.
Cu: ≤ 0.15 %
[0024] Cu is an undesired impurity element that is restricted to ≤ 0.15 % by careful selection
of the scrap used. The upper limit may be restricted to 0.12, 0.10, 0.08 or 0.06 %.
Ni: ≤ 0.15 %
[0025] Ni is also an undesired impurity element that is restricted to ≤ 0.15 % by careful
selection of the scrap used. The upper limit may be restricted to 0.12, 0.10, 0.08
or 0.06 %.
[0026] Other impurity elements may be comprised in the steel in normal occurring amounts.
However, it is preferred to limit the amounts of P, S to the following optional maximum
contents:
P: ≤ 0.02 %
S: ≤ 0.005 %
[0027] It is also preferred to control the nitrogen content to the range:
N: 0.003 - 0.005 %
[0028] In this range a stable fixation of the nitrogen can be achieved.
Ti/B: 5 - 30
[0029] The ratio Ti/B is preferably adjusted to be in the range of 5 - 30 in order to secure
an optimal fixation of the nitrogen in the steel, resulting in free unbounded boron
in the steel. Preferably, such ratio can be adjusted to be in the range of 8 - 11.
[0030] The cold rolled steel sheets of the present invention have a microstructure mainly
consisting of retained austenite embedded in a matrix of tempered martensite (TM),
i.e. the amount of tempered martensite is at least ≥ 40 %, generally ≥ 50 %.
[0031] The microstructure may also contain up to 40 % bainitic ferrite (BF) and up to 20
% fresh martensite (FM). The latter may be present in the final microstructure because,
depending on its stability, some austenite may transform to martensite during cooling
at the end of the overaging step. The amount of FM may be limited to 15, 10, 8 or
5 %. Retained austenite (RA) is a prerequisite for obtaining the desired TRIP effect.
The amount of retained austenite should therefore be in the range of 2 - 20 %. The
lower limit of retained austenite may be set to 3, 4, 5, 6, 7 or 8 %. A preferred
range is 5 - 15 %. The amount of retained austenite was measured by means of the saturation
magnetization method described in detail in
Proc. Int. Conf. on TRIP-aided high strength ferrous alloys (2002), Ghent, Belgium,
p. 61-64.
[0032] Polygonal ferrite (PF) is not a desired microstructural constituent and is therefore
limited to ≤ 10 %, preferably ≤ 5 %, ≤ 3 % or ≤ 1 %. Most preferably, the steel is
free from PF.
[0033] The mechanical properties of the claimed steel are important and at least one of
the following requirements should be fulfilled:
tensile strength (Rm) |
≥1380 |
MPa |
yield strength (Rp0.2) |
≥ 1000 |
MPa |
total elongation (A80) |
≥ 5 |
% |
hole expansion ratio (λ) |
≥ 40 |
% |
yield ratio (Rp0.2/ Rm) |
≥ 0.60 |
|
[0034] Preferably, all these requirements are fulfilled at the same time.
[0035] The lower limit for the tensile strength (R
m) may be set to 1390, 1400, 1410, 1420 or 1430 MPa.
[0036] The lower limit for the yield strength (R
p0.2) may be set to 1010, 1020, 1030, 1040, 1050 or 1460 MPa.
[0037] The lower limit for the total elongation (A
80) may be set to 6 or 7 %.
[0038] The lower limit for the hole expansion ratio (λ) may be set to 45, 50, 55 or 60 %.
[0039] The lower limit for the yield ratio (R
p0.2/ R
m) should be at least 0.60 and may be set to 0.64, 0.66, 0.68, 0.70 or 0.72.
[0040] The R
m, R
p0.2 and A
80 values are derived according to the European norm EN 10002 Part 1, wherein the samples
were taken in the longitudinal direction of the strip.
[0041] The hole expanding ratio (λ) is determined by the hole expanding test according to
ISO/WD 16630:2009 (E). In this test a conical punch having an apex of 60 ° is forced
into a 10 mm diameter punched hole made in a steel sheet having the size of 100 x
100 mm
2. The test is stopped as soon as the first crack is determined and the hole diameter
is measured in two directions orthogonal to each other. The arithmetic mean value
is used for the calculation.
[0042] The hole expanding ratio (λ) in % is calculated as follows:

wherein Do is the diameter of the hole at the beginning (10 mm) and Dh is the diameter
of the hole after the test.
[0043] The product of the tensile strength and the hole expansion ratio R
m x λ was calculated to evaluate the balance between the strength and the workability
formability i.e. the stretch- flangeability.
[0044] The product of the tensile strength and the hole expansion ratio R
m x λ of the cold rolled steel of the present invention should preferably be at least
60000 MPa%. The lower limit of this product can be set to 65000, 70000,75000, 80000
or 85000 MPa%.
[0045] The bendability was evaluated by the ratio of the limiting bending radius (Ri), which
is defined as the minimum bending radius with no occurrence of cracks, and the sheet
thickness, (t). For this purpose, a 90° V-shaped block is used to bend the steel sheet
in accordance with JIS Z2248. The samples were examined both by eye and under optical
microscope with 25 times magnification in order to investigate the occurrence of cracks.
The value obtained by dividing the limit bending radius with the thickness (Ri/t)
should be less than 5. Preferably, the value (Ri/t) should be ≤ 4, ≤ 3 or ≤ 2.
[0046] The yield strength of the cold rolled steel of the present invention can be increased
by subjecting the steel to Bake Hardening (BH). The increase in yield strength after
2 % stretching in a tensile test BH
2 may be at least 30 MPa, wherein the BH
2 -value is determined in accordance with DIN EN10325. The lower limit may be set to
35, 40 or 45 MPa.
[0047] The mechanical properties of the steel strips and sheets of the present invention
can be largely adjusted by the alloying composition and the microstructure. Conventional
steelmaking using continuous casting and hot rolling is used to produce a hot rolled
strip. The hot rolled strip is pickled and thereafter batch annealed at about 580
°C for a total time of 10 hours in order to reduce the tensile strength of the hot
rolled strip and thereby reducing the cold rolling forces before cold rolling to a
final thickness. The cold rolled strips may thereafter be subjected to continuous
annealing in a Continuous Annealing Line (CAL).
The microstructure may be adjusted by the heat treatment in the CAL, in particular
by the isothermal treatment temperature in the overaging step. Usually, such isothermal
treatment temperature in the overaging step is a bit below Ms temperature (such as
50°C to 100°C below Ms) but it is possible to heat treat in the overaging step at
Ms temperature or up to 100°C above Ms.
[0048] As an alternative, it is possible to use the Quench and Partitioning (Q&P) process
to adjust the mechanical properties of the steel sheet. The material is then annealed
and thereafter cooled to a temperature below the M
s temperature, reheated to a partitioning temperature above the M
s temperature, held at this temperature for partitioning and finally cooled to room
temperature. Optionally, the material subjected to Q&P may also be subjected to a
batch annealing step at a low temperature (about 200 °C) in order to fine tune the
mechanical properties, in particular the yield strength and the hole expansion ratio.
[0049] The material produced via isothermal route in the CAL may also be subjected to a
batch annealing step at a low temperature (about 200 °C) in order to fine tune the
mechanical properties, in particular the yield strength and the hole expansion ratio.
EXAMPLE
[0050] A steel having the following composition was produced by conventional metallurgy
by converter melting and secondary metallurgy:
C |
0.20 |
Si |
0.85 |
Mn |
2.5 |
Cr |
0.34 |
Al |
0.049 |
Ti |
0.026 |
B |
0.0035 |
Cu |
0.01 |
Ni |
0.01 |
P |
0.01 |
S |
0.0005 |
N |
0.0035 |
balance Fe and impurities.
[0051] The steel was continuously cast and cut into slabs. The slabs were reheated and subjected
to hot rolling to a thickness of about 2.8 mm. The hot rolling finishing temperature
was about 900 °C and the coiling temperature about 550 °C. The hot rolled strips were
pickled and batch annealed at about 580 °C for a total time of 10 hours in order to
reduce the tensile strength of the hot rolled strip and thereby reducing the cold
rolling forces. The strips were thereafter cold rolled in a five stand cold rolling
mill to a final thickness of about 1.35 mm and finally subjected to continuous annealing
in a Continuous Annealing Line (CAL).
[0052] The annealing cycle consisted of heating to a temperature of about 850 °C, soaking
for about 120 s, cooling during 30 seconds to an overaging temperature of about 250
°C, thereafter isothermal holding at the overaging temperature for about 3 minutes
and finally cooling to the ambient temperature. The strip thus obtained had a matrix
of TM and contained 9 % BF, 8% FM and 11% RA. The strip had a tensile strength (R
m) of 1450 MPa and a yield strength (R
p0.2) of 1080 MPa. The total elongation (A
80) was 7% and the hole expansion ratio (λ) was 59 %. Accordingly, the product R
mxλ was 85500 MPa%.
[0053] The R
m and R
p0.2 values are derived according to the European norm EN 10002 Part 1, wherein the samples
were taken in the longitudinal direction of the strip. The elongation (A
80) is derived in accordance with the same norm.
[0054] The hole expanding ratio (λ) is the mean value of three samples subjected to hole
expansion tests (HET) according to ISO/TS16630:2009 (E).
INDUSTRIAL APPLICABILITY
[0055] The material of the present invention can be widely applied to high strength structural
parts in automobiles. The high ductility high strength cold rolled steel strips and
sheets of the present invention are particularly well suited for the production of
parts having high demands on the local elongation.
1. A cold rolled steel strip or sheet having
a) a composition consisting of (in wt. %):
C |
0.15 - 0.25 |
Si |
0.7 - 1.6 |
Mn |
2.2 - 3.2 |
Cr |
≤ 0.8 |
Mo |
≤ 0.2 |
Al |
0.03 - 1.0 |
Nb |
≤ 0.04 |
V |
≤ 0.04 |
Ti |
0.01 - 0.04 |
B |
0.001 - 0.005 |
Ti/B |
5 - 30 |
Cu |
≤ 0.15 |
Ni |
≤ 0.15 |
Ca |
≤ 0.01 |
balance Fe apart from impurities,
b) a multiphase microstructure comprising (in vol. %):
tempered martensite |
≥ 40 |
bainitic ferrite |
≤ 40 |
fresh martensite |
≤ 20 |
retained austenite |
2 - 20 |
polygonal ferrite |
≤ 10 |
c) the following mechanical properties
a tensile strength (Rm) |
≥ 1380 |
MPa |
yield strength (Rp0.2) |
≥ 1000 |
MPa |
total elongation (A80) |
≥ 5 |
% |
hole expansion ratio (λ) |
≥ 40 |
% |
bendability (Ri/t) |
≤ 5 |
|
2. A cold rolled steel strip or sheet according to claim 1, wherein the steel composition
comprises
and optionally at least one of
Cu |
≤ 0.10 |
Ni |
≤ 0.10 |
Nb |
≤ 0.005 |
V |
≤ 0.01 |
Ca |
≤ 0.005 |
3. A cold rolled steel strip or sheet according to claim 1 or 2, wherein the amount of
retained austenite is at least 4 vol. % and the amount of polygonal ferrite is less
than 6 vol. %.
4. A cold rolled steel strip or sheet according to claim 1, 2 or 3, wherein the multiphase
microstructure fulfils the following requirements (in vol. %):
tempered martensite |
≥ 50 |
bainitic ferrite |
≤ 30 |
fresh martensite |
≤ 15 |
retained austenite |
5 - 15 |
polygonal ferrite |
≤ 5 |
and/or least one of the following requirements
hole expansion ratio (λ) |
≥ 50 |
% |
Rmxλ |
≥ 60000 |
MPa% |
yield ratio (Rp0.2/ Rm) |
≥ 0.60 |
|
5. A cold rolled steel strip or sheet according to any of the preceding claims, wherein
the increase in yield strength after 2 % stretching in a tensile test, the BH2-value, is least 30 MPa.
6. A cold rolled steel strip or sheet according to any of the preceding claims, wherein
the multiphase microstructure fulfils at least one of the following requirements (in
vol. %):
tempered martensite |
≥ 60 |
bainitic ferrite |
≤ 20 |
fresh martensite |
≤ 10 |
retained austenite |
6 - 14 |
polygonal ferrite |
≤ 3 |
and/or least one of the following requirements
hole expansion ratio (λ) |
≥ 55 |
% |
Rmxλ |
≥ 65000 |
MPa% |
7. A cold rolled steel strip or sheet, wherein the steel composition fulfils at least
one of the of the following requirements with respect to the impurity contents (in
wt. %):
P |
≤ 0.02 |
S |
≤ 0.005 |
N |
0.002 - 0.006 |
8. A cold rolled steel strip or sheet according to any of the preceding claims, having
a) a composition fulfilling at least one of the following requirements with respect
to the impurity contents (in wt. %):
P |
≤ 0.01 |
S |
≤ 0.003 |
N |
0.003 - 0.005 |
Sn |
≤ 0.015 |
Zr |
≤ 0.006 |
As |
≤ 0.012 |
Ca |
≤ 0.005 |
H |
≤ 0.0003 |
O |
≤ 0.0020 |
9. A cold rolled steel strip or sheet according to any of the preceding claims fulfilling
all requirements of claims 1, 2 and 3 and, optionally, the requirements of claim 4.
10. A cold rolled steel strip or sheet according to any of the preceding claims, wherein
the cold rolled steel is provided with a Zn containing layer.