Original Article
Theoretical analysis of strain- and
stress-based forming limit diagrams
J Strain Analysis
48(3) 177–188
Ó IMechE 2013
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DOI: 10.1177/0309324712468524
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Surajit Kumar Paul
Abstract
Forming limit diagram is extensively used in the analysis of sheet metal forming to define the limit of deformation of
materials without necking or fracture. This article contributes in construction of strain- and stress-based forming limit
diagrams by theoretical analysis of several available instability criteria, including bifurcation analysis of diffuse and
through-thickness neck formation, shear stress-based criteria onset of through-thickness necking, and so on, and comparative studies among different available theories are done with earlier published work on forming limit in different literatures. The scope of Tresca criterion in forming limit diagram is also investigated in this article. It is found that apart
from stress-based forming limit diagram, conventional failure criterion equivalent failure strain versus triaxiality (h) plot
is also strain path independent.
Keywords
Strain- and stress-based forming limit diagram, equivalent failure strain versus triaxiality plot, Hill–Tresca criterion, Hill–
Bressan–Williams criterion, Hill–Swift criterion, Storen–Rice criterion
Date received: 21 June 2012; accepted: 26 October 2012
Introduction
Sheet metal formability can be defined as the ability of
metal to deform without necking or fracture into
desired shape. Every sheet metal can be deformed without failing only up to a certain limit, which is normally
known as forming limit curve (FLC). FLC is generally
governed by localized necking, which eventually leads
to the ductile fracture. FLC can be represented as a
curve of the major strain (e1) at the onset of localized
necking for all values of the minor strain (e2), and the
full graph is named as forming limit diagram (FLD). A
schematic of FLD is illustrated in Figure 1. The FLC
can be split into two branches: ‘‘left branch’’ and ‘‘right
branch.’’ Keeler and Backhofen1 have first introduced
the ‘‘right branch’’ of FLC, which is valid for positive
major and minor strains. Goodwin2 has completed the
FLC by introducing the ‘‘left branch’’ of FLC, which is
applicable for positive major and negative minor
strains. FLC is solely applicable for proportional strain
path. Therefore, to construct FLC, different ratios of
major and minor strains are chosen in proportional
strain paths. The ‘‘left side’’ represents strain paths with
strain ratios (a = e2/e1) that vary from uniaxial tension
(a = 20.5) to plane strain (a = 0). On the ‘‘right
branch,’’ the strain ratios differ from plane strain to full
biaxial (a = 1) stretching. Usually, FLD is determined
by using one of the following two types of test method:
(a) Marciniak et al.’s3 in-plane test, where a sheet metal
sample is strained by a flat-bottomed cylindrical punch
and it creates a frictionless in-plane deformation of the
sheet, and (b) Nakazima et al.’s4 out-of-plane test
(dome), which uses a hemispherical punch. As this test
deformation is not frictionless, lubricants are used. The
necessary strain paths can be obtained by using different sample widths.
The strain levels in the stamped part should be
located below the FLC everywhere in order to avoid
necking of the material. By offsetting the FLC (generally 10%), a safety margin is normally introduced.
Usually by evaluating how close the strain state is to
the FLC, the risk of necking/failure is determined.
Rejection of the formed part not only depends on necking but also depends on other problems such as excessive thinning, wrinkling, or insufficient stretch.
Therefore, it is not sufficient to design a component
that can be manufactured in forming route by considering only the risk of failure through necking. Apart from
Research and Development, Tata Steel Limited, Jamshedpur, India
Corresponding author:
Surajit Kumar Paul, R&D, Tata Steel Limited, Jamshedpur 831001, India.
Email: paulsurajit@yahoo.co.in; surajit.paul@tatasteel.com
178
Figure 1. A schematic plot of forming limit diagram.
Journal of Strain Analysis 48(3)
Figure 3. A schematic plot of the forming limit diagram and
other failure limits.
FLC: forming limit curve.
Figure 2. Schematic representation of forming limit diagram
indicating safe forming region.
necking, all other failure conditions are normally also
evaluated by studying the strain levels. The details of
different zones of a FLD are constructed from the
FLC, as shown in Figure 2. Wrinkling may occur when
the minor stress in the sheet is compressive. Wrinkling
of the flange areas can be suppressed by the blank
holder. However, wrinkling may also occur in unsupported regions or regions in contact with only one tool.
During actual sheet metal forming operations, deformation limit is not only constrained by the necking limit,
that is FLC, but also constrained by the shear fracture
and thinning fracture limit that is depicted in Figure 3.5
The procedure for determining FLCs may differ
concerning the geometry of the forming punch used,
the specimen dimensions, the number of specimen geometries considered, the friction conditions during testing, the technique used for the evaluation of strain
states, and the type of curve-fitting used. Due to the
bending effects during forming, a small deviation from
linear strain paths may occur. The determination of the
experimental FLC is a quite lengthy procedure, which
is a real problem in the practical forming process
design. Nowadays, in the competitive market scenario
of the automotive industry, there is a strong demand to
reduce product design cycle time, which means that
there is not enough time to determine experimental
FLC. Therefore, a profound demand from the automotive industry comes to generate the FLC from different
theoretical and empirical formulas. The large scatter in
experimental results while determining a FLC is
another significant drawback. The most commonly
used failure criterion for sheet metal forming applications is still FLC despite of its all the drawbacks. This
is due to its simplicity, excellent performance, and for
its historical reasons in many cases.
Although the FLC method is widely used tool in
sheet metal forming process, it is valid only for proportional loading conditions, where the ratio of major and
minor plastic strains remains constant throughout the
forming process.6 Prediction by finite element method
(FEM) and experimental measurements have shown
that in most first draw forming operations are almost
proportional, hence the path-dependent limitations of
the FLC are often not considered. The issue of path
dependency of FLC cannot be ignored in the analysis
of secondary forming processes like redrawing and flanging dies where strain paths are not the same for the
first and second forming processes. In such cases, conventional FLC is not valid, major and minor strains lie
far below the FLC found to neck while in other areas
strains far above the conventional FLC found to be
safe from necking. The path dependence of the relation
between the stress and strain rates in the incremental
plasticity is the sole cause of the path dependency in the
strain-based FLC. The limitations of the strain-based
FLC are addressed by Kleemola and Pelkkikangas7 for
the analysis of flanging operations followed by a draw
forming operation for different metals and alloys. They
proposed an alternative solution that is known as
stress-based FLC to overcome the path dependency of
strain-based FLC. Arrieux et al.8 also proposed a similar stress-based criterion for all secondary forming
operations. Stoughton6 also proposed the stress-based
FLC in all forming operations, including the first draw
die, in order to get a robust measure of forming severity.
179
Paul
The FLC can be achieved before the onset of local
necking. The commonly used necking models are the
Swift diffuse criterion9 and the Hill local criterion.10
The Swift diffuse criterion was derived by assuming
that there is a maximum loading force and the Hill
localization criterion is obtained by assuming that there
is a maximum principal stress. Storen and Rice11 used
a bifurcation analysis to describe the behavior of the
FLC that arises from a vertex on the yield surface by
imposing force equilibrium between the necked and
nonnecked region of the metal. Another well-known
methodology is the geometric imperfection model proposed by Marciniak and Kuczynski,3,12 which is
referred as M–K model. FLC generated by the M–K
method depends on the size and shape of geometrical
imperfection. Therefore, exact FLC cannot be obtained
from the M–K method, but a band can be obtained or
calibrate it with at least one experimental point.13 All
these models are extensively used to generate theoretical
FLC. An alternative to the above-mentioned prediction
methods is proposed by Bressan and Williams;14 a novel
shear failure theory was used to calculate the maximum
shear stress to estimate the onset of local necking.
However, only the right-hand side of FLC can be generated by Bressan–Williams (BW) model, as they prescribed
in their original article. All these models support stressbased FLC. Since the stress-based FLC and the strainbased FLC are identical under proportional loading conditions, these models can equally be viewed to explain the
strain-based FLC under that condition. In this study,
Swift diffuse necking criterion,9 Hill local necking criterion,10 Storen and Rice11 bifurcation analysis, maximum
shear stress-based Tresca failure criterion,15 and Bressan
and Williams14 shear failure criterion are investigated.
where s1 and s2 are the major and minor principal true
stresses, and plane stress (s3 =0) condition is adopted.
seq is the equivalent true stress.
Associated flow rule can be described as
dep = dl
df
d
s
ð2Þ
where dl is the proportionality constant, and for uniaxial condition, it is equal to the effective strain rate; dep is
the plastic strain rate.
The ratio of the minor true strain rate (de2) to the
major true strain rate (de1) is defined by the parameter
a=
de2
de1
ð3Þ
Similarly, the ratio of the minor true stress (s2) to
the major true stress (s1) is defined by the parameter
b=
s2
s1
ð4Þ
This flow rule (equation (2)) leads to a relation
between a and b that can be expressed as
a=
b=
2b 1
2b
ð5Þ
1 + 2a
a+2
ð6Þ
The rate of change of the yield function can be
defined as
df
∂f
∂f
dl =
ds1 +
ds2
p
de
∂s1
∂s2
ð7Þ
The most commonly used representation of stress–
strain relation is the power law
Plasticity relations
Predictive capabilities of the existing models are validated by FLD data available in the literatures. The
material property details are given in Table 1.
All the mathematical formulations described in this
article are derived from isotropic plasticity theory. Von
Mises yield function and associated flow rule are used
for all analyses.
Von Mises yield function can be defined as
qffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
f = seq = s21 + s22 s1 s2
ð1Þ
seq = Keneq
ð8Þ
where K and n are material constants, K is power law
coefficient, and n is power law exponent.
By rearranging equations (1) and (4), equivalent
stress (seq) can be written as
qffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
seq = s1 1 b + b2
ð9Þ
Similarly, equivalent plastic strain increment (deeq)
can be written as
Table 1. Material constants details.
Serial no.
Material
Reference
1
2
3
4
5
DP600
TRIP 600
Steel Fep04
AISI 1012 low carbon steel
AA3105-U Al alloy
Uthaisangsuk et al.16
Uthaisangsuk et al.16
Brunet and Morestin17
Nurcheshmeh and Green18
Aghaie-Khafri and Mahmudi19
K (MPa)
950
1090
522
238
236
n
Uniform
elongation
Thickness
(mm)
0.16
0.21
0.237
0.35
0.26
0.16
0.26
—
—
0.15
1.0
1.0
—
—
1.0
180
Journal of Strain Analysis 48(3)
pffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
2
deeq = pffiffiffi de1 1 + a + a2
3
ð10Þ
Triaxiality (h) is the ratio of mean stress (sm) and
equivalent stress (seq), and it can be expressed as
h=
sm
1+a
= pffiffiffipffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
seq
3 1 + a + a2
ð11Þ
where mean stress (sm) is
sm =
1
ðs1 + s2 + s3 Þ
3
ð12Þ
All those relationships are used in next section to
derive the FLC by various criteria.
FLD prediction methods
FLC-zero (FLC0) is the most important parameter in
the FLC. It is the major principal strain at the onset of
necking at plane strain condition, that is, the minor
principal strain is equal to zero. Experimentally, FLC0
can be determined form tensile test with specimen geometry of large sample width compared to its length.
The parameter FLC0 is often also defined from empirical formula or makes approximation from similar
metals. An empirical formula used to determine FLC0,
in a wide range of steels, was proposed by Keeler and
Brazier20
13:3 + 14:13t
n
for n40:21
FLC0 = ln 1 +
100
0:21
ð13Þ
where t is the sheet thickness measured in millimeters,
and n is the strain hardening exponent in power law
expression (equation (8)). In equation (13), FLC0 is represented in true strain.
Actually, stress-based FLC can be directly constructed from Swift, Hill, Storen and Rice, and Bressan
and Williams models. By imposing proportional straining condition, strain-based FLCs can be obtained from
those stress-based FLCs. In this study, proportional
straining condition is assumed in the beginning, and
for simplicity, strain-based FLCs are first shown and
then mapped in the stress space.
Swift diffuse necking criterion
For sheet metal forming, Swift9 proposed a diffuse neck
criterion, which described as diffuse neck starts when
the load reaches a maximum along both principal directions. The diffuse necking condition can be expressed
by the constraints in the form of equation (14)
ds1 = s1 de1
ð14Þ
ds2 = s2 de2
From equations (2), (7), and (14), we can obtain the
following set of points defining swift instability (for
details see Stoughton and Zhu’s21 study)
Figure 4. FLC from Swift diffusive necking theory for different
strain hardening exponents.
e1
e2
0
B
B
=B
@
2nð2 bÞ 1 b + b2
1
C
2
3
4 3b 3b
+ 4b 2 C
C
2nð1 2bÞ 1 b + b A
ð15Þ
4 3b 3b2 + 4b3
Equivalent strain can be obtained from equation (10)
and equivalent stress from equation (8). Stress-based
FLC can be generated from equations (4) and (9). In
equation (15), power law exponent n is equal to uniform
elongation eUL; therefore, eUL can be used instead of n.
FLC generated from Swift diffusive necking theory is
portrayed in Figure 4, for different n values.
Hill local necking criterion
Hill10 assumed that a local neck will form with an angle c
to the direction of the major principal stress. The orientation angle of the neck with
respect of loading axes may be
pffiffiffiffiffiffiffi
expressed as c = tan1 ( a). Due to the square root in
the expression, the instability described in equation (16)
has physical significance only when a is negative. The
reduction in thickness and the effect of strain hardening
balance each other exactly when local neck formed. This
means that the fractions within the material reach a state
where traction increments equal to zero, and from there,
the following criterion for local necking can be derived
ds1
= s 1 ð 1 + aÞ
de1
ð16Þ
For proportional straining, the familiar strain-based
Hill’s expression appears
e1 =
n
1+a
ð17Þ
In equation (17), power law exponent n is equal to
uniform elongation eUL; therefore, eUL can be used
instead of n. The set of points defining Hill’s instability
can be expressed as
181
Paul
e1
e2
0 eUL 1
+aA
= @ 1eUL
a
1+a
for b \ 0
ð18Þ
The equivalent strain at local necking can be
expressed as
pffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
2eUL 1 + a + a2
pffiffiffi
ð19Þ
eeq =
3ð 1 + aÞ
Equivalent stress for power law expression can be
written as
pffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi!n
2eUL 1 + a + a2
pffiffiffi
ð20Þ
seq = K
3 ð 1 + aÞ
From equation (20), a path-independent stress-based
FLC can be derived as
pffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi!n 1
Kð2 + aÞ
2eUL 1 +a + a2
pffiffiffi
C
B pffiffiffipffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi2
C
B 3 1 +a + a
3ð1+ aÞ
s1
C forb \0
!
=B
ffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
p
n
C
B
s2
2eUL 1 +a + a2 A
@ Kð1+ 2aÞ
pffiffiffi
pffiffiffipffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
3ð1+ aÞ
3 1 +a + a2
0
ð21Þ
A similar derivation has been shown by Stoughton
and Zhu21 and Alsos et al.22
Using power law expression, the stress-based FLC
can be constructed as
!n 1
Kð2 + aÞ
3a2 + nð2 + aÞ2
pffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi C
B pffiffiffipffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi2ffi
B 3 1 + a + a ð1 + 2aÞ 3ð1 + a + a2 Þ C
s1
!n C
=B
C
B
s2
3a2 + nð2 + aÞ2
A
@ Kð1 + 2aÞ
pffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
pffiffiffipffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
3 1 + a + a2 ð1 + 2aÞ 3ð1 + a + a2 Þ
0
ð24Þ
Hill–Swift criterion
Poor shape of FLC is observed in the negative region
of a (Figure 1) by Swift theory. Hill’s criterion is applicable for negative value of a. Limitation of Hill–Swift
(HS) theory can be eliminated by the combination of
the two. In HS theory, Hill criterion is applied for a
negative value of a, and Swift criterion is applied for a
positive value of a. Figure 5 shows the effect of power
law exponent (n) in FLC by HS theory.
Storen–Rice bifurcation criterion
Storen and Rice11 introduced a bifurcation that allows
a neck to form in-plane strain. They introduce a vertex
on the yield surface whose discontinuity grows until a
plane strain plastic strain increment is possible. Thus,
they got two sets of solutions, those two solutions for
FLD in two directions of sheets (rolling and transverse
directions). Using one solution, FLC can be constructed as (Stoughton and Zhu’s21 study)
0
1
3a2 + nð2 + aÞ2
C
B
B 2ð1 + 2aÞð1 + a + a2 Þ C
e1
C
ð22Þ
=B
B a 3a2 + nð2 + aÞ2 C
e2
A
@
2ð1 + 2aÞð1 + a + a2 Þ
The equivalent strain from e1 can be expressed as
2
eeq =
Figure 5. FLC from the Hill–Swift theory for different strain
hardening exponents.
3a2 + nð2 + aÞ
pffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
ð1 + 2aÞ 3ð1 + a + a2 Þ
ð23Þ
FLCs generated from Storen-Rice (SR) theory for
different values of power law exponent (n) are shown in
Figure 6. This figure shows that the FLC shapes
become distorted for high value of n.
BW shear instability criterion
An interesting way of predicting stability of sheets was
proposed by Bressan and Williams14 and applied to the
problem of ship grounding by Alsos et al.22 To derive
BW instability criterion, they make three basic assumptions, which are as follows: (a) shear instability is initiated in the direction through the thickness at which the
material element experiences no change of length, (b)
instability starts when local shear stress exceeds a critical value, and (c) elastic components of strains are
neglected during calculation.
The orientation of the plane of critical shear stress
can be predicted by
cos 2u =
a
2+a
ð25Þ
where u represents the direction of the localization band
predicted by the BW criterion. And critical shear stress
(tcr) is predicted by
t cr =
s1
sin 2u
2
ð26Þ
By combining equations (25) and (26), we can obtain
the BW criterion
182
Journal of Strain Analysis 48(3)
Hill–Bressan–Williams criterion
The mathematical expression of the BW criterion is
valid for both positive and negative values of minor
strain. The initial BW criterion was used for the positive
quadrant of the FLD. Therefore, the Hill and BW criterion have been combined into one criterion in order
to cover the full range of a, from now on referred to as
the Hill–Bressan–Williams (HBW) criterion. In the
HBW criterion, Hill criterion is applied for the negative
value of a, and the BW criterion is applied for the positive value of a.
Hill–Tresca criterion
Figure 6. FLC from Storen–Rice theory for different strain
hardening exponents.
2t cr
s1 = qffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
a 2
1 2+
a
ð27Þ
A similar derivation is given by Alsos et al.22
Bressan and Williams initially suggested to conduct
the material constant calibration from uniaxial tensile
test or biaxial tensile test. The material constant for
BW model can be calibrated from plane strain,
a = 022 condition, or simply from Hill’s analysis. The
BW criterion can be calibrated by considering that
the Hill expression and the BW criterion will be the
same at plane strain condition. From equation (21)
(s1 vs ^e1 expression), the critical BW shear stress
takes the following form
n
1
2n
t cr = pffiffiffi K pffiffiffi
3
3
ð28Þ
In equation (28), 2n is equal to uniform elongation
2eUL; therefore, 2eUL can be used instead of 2n. Then,
rearranging equations (27) and (28), we can obtain
n
2e
pUL
ffiffi
2
3
s1 = pffiffiffi K qffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
a 2
3
1
ð29Þ
2+a
Therefore, the set of points for stress-based FLC can
be expressed as
s1
s2
n 1
1
2 + a 2eUL
pffiffiffi
B pffiffi3ffi K pffiffiffiffiffiffiffiffiffiffiffiffi
1+a 3 C
C
=B
@ 1
2a + 1 2eUL n A
pffiffiffi K pffiffiffiffiffiffiffiffiffiffiffiffi pffiffiffi
3
3
1+a
0
ð30Þ
With the help of equations (3) and (8)–(10), conversion from stress-based FLC to strain-based FLC can be
made.
The deformation comes from slip mechanism, which
can be described as, the slip will occur on certain preferred combinations of crystallographic planes when
shear stress reaches a critical limit. Furthermore,
experimental observation reveals that the direction of
maximum shear stress is close to the failure planes.14,23
Therefore, it can be assumed that the instability may
occur before any visual signs of local necking.
Accordingly, a shear stress-based instability criterion
can be used to calculate the point of local necking.
Therefore, Tresca’s maximum shear stress-based theory15 is used in this investigation to predict necking of
sheet materials. In this investigation, Hill’s criterion is
used for the negative strain ratios, that is, drawing
operation, and Tresca’s criterion is used for the positive
strain ratios, that is, stretching operation.
According to the Tresca criterion, instability
can occur when maximum shear stress exceeds a critical
value at any location. Distance from Tresca’s hexagon
center to top side in the first quadrant can be defined as
s1 = str
ð31Þ
The parameter str can be determined from plane
strain condition. According to the Hill criterion, equivalent strain can be determined when necking starts inplane strain condition from equation (19) by putting
a = 0. Therefore, equivalent strain at plane strain condition becomes
2
eeqtr = pffiffiffi eUL
3
ð32Þ
where n = eUL for power law relationship.
Therefore, equivalent stress will be
n
2
seqtr = K pffiffiffi eUL
3
ð33Þ
The Tresca parameter (str) will be
n
2
2
str = pffiffiffi K pffiffiffi eUL
3
3
ð34Þ
183
Paul
Figure 7. TRIP 600:16 (a) strain-based FLC, (b) stress-based FLC, and (c) equivalent failure strain versus triaxiality (h) plot.
Therefore, for stretching (0 4 a 4 1), stress-based
FLC can be represented as
0
1
n
p2ffiffi K p2ffiffi eUL
s1
3
3
ð35Þ
=@
nA
s2
1 + 2a p2ffiffi
p2ffiffi eUL
K
2+a
3
3
Similarly to the BW criterion, conversion from
stress-based to strain-based FLC can be made with the
help of equations (3) and (8)–(10).
Discussion
There are several types of failure criteria available to
define the limit of sheet metal deformation. They are
(a) strain-based FLC or FLC or eFLC,1,2,20 (b) stressbased FLC or forming stress limit curve (FSLC) or
sFLC,6–8 and (c) extended stress-based FLC
(XSFLC).24 Apart from these three, one more criteria
that is widely used to define failure limit in general is
also shown; it is (d) equivalent failure strain versus
triaxiality plot.25,26 Stress-based FLC and XSFLC are
similar types of representation for ordinary forming
operations; therefore, to avoid repetition instead of
two, only stress-based FLC is discussed in latter part of
this section.
The effect of prestraining on subsequent strainbased FLC can be determined by the following two
assumptions:6 (a) in the second loading stage, the material does not yield plastically until the effective stress
rises to the same level of stress attained at the end of
the prestrain loading stage, that is, pure isotropic hardening is considered. (b) Material fails after prestraining
at the exactly same equivalent failure strain/stress as it
is in the as-received condition. This assumptions work
well in the absence of shear stresses, as this is the case
in the usual FLD experiments, where the principal axes
are aligned with the coordinate axis. For prestraining,
the power law equation (equation (8)) becomes
n
seq = K ePSeq + eeq
ð36Þ
where ePSeq is the equivalent strain during prestraining
and seq and eeq are the equivalent stress and strain,
respectively, in the second loading stage. With the help
of equations (9), (10), and (36), FLC after prestraining
can be constructed.
TRIP 600 steel
In this subsection, experimental FLC of TRIP 600
steel represented by Uthaisangsuk et al.16 is compared
with FLC derived theoretically from different criteria.
The material constants are tabulated in Table 1.
Strain-based FLC, stress-based FLC, and equivalent
failure strain versus triaxiality (h) plots are shown in
184
Journal of Strain Analysis 48(3)
Figure 8. DP 600:16 (a) strain-based FLC, (b) stress-based FLC, and (c) equivalent failure strain versus triaxiality (h) plot.
Figure 7 for TRIP 600 steel. TRIP 600 has clearly
higher uniform elongation than its strain hardening
exponent, because the deformation mechanism is
influenced by the phase transformation that occurred
during straining.16 Therefore, during theoretical FLC
derivation by different criteria, n is equal to uniform
elongation (eUL) of the material used. The HBW criterion shows relatively good agreement with experimental data.
DP 600 steel
Experimental FLC of DP 600 steel presented by
Uthaisangsuk et al.16 is used in this study to compare
the FLC drawn from various criteria. In Figure 8,
strain-based FLC, stress-based FLC, and equivalent
failure strain versus triaxiality (h) plots are depicted.
DP 600 steel microstructure contains soft ferrite matrix
and hard martensite distributed in soft matrix. During
deformation, strain partitioning takes place among soft
and hard phases.16,27,28 The presence of different phases
makes damage initiation complex in multiphase steels,
in single-phase steel damage, that is, necking initiates
from initiation and coalescence of voids, but in DP steel
damage also initiates from cracking of hard phase,
decohesion of hard and soft phases, and so on.16
Complexity in deformation and damage is also reflected
in FLC. The HBW criterion predicts FLC better than
other models. The same is also reflected in stress-based
FLC and equivalent failure strain versus triaxiality (h)
plot.
AA 3105 Al alloy
Aghaie-Khafri and Mahmudi19 generated experimental
FLC of AA 3105 Al alloy, which has been used in
this study. The uniform elongation (eUL) of this Al alloy
is lower than the strain hardening exponent (n). As uniform elongation is showing good correlation with
FLC0; therefore, n equal to uniform elongation (eUL) is
used for this material. None of the models are able to
predict the FLC of AA 3105 Al alloy; only the SR criterion predicts relatively well in the range of 0 4 a 4 1
but over predict in the range of 20.5 4 a 4 0, and the
Hill criterion shows relatively well result in the range of
20.5 4 a 4 0, which is shown in Figure 9.
AISI 1012 low carbon steel
Nurcheshmeh and Green18 generated experimental
FLC of base material and of 10% tensile prestraining
for AISI 1012 low carbon steel. Their experimentally
generated data are used to examine the different models
predicting capabilities. FLC predictions by different
criteria are shown in Figure 10(a) for base material
and in Figure 10(b) for FLC after 10% tensile
Paul
185
Figure 9. AA 3105 Al alloy:19 (a) strain-based FLC, (b) stress-based FLC, and (c) equivalent failure strain versus triaxiality (h) plot.
Figure 10. AISI 1012 low carbon steel:18 (a) strain-based FLC for base material, (b) strain-based FLC after material uniaxial tensile
prestrained to 10%, (c) stress-based FLC, and (d) equivalent failure strain versus triaxiality (h) plot.
186
Journal of Strain Analysis 48(3)
Figure 11. Steel Fep04:17 (a) strain-based FLC for base material, (b) strain-based FLC after material uniaxial tensile prestrained to
10%, (c) strain-based FLC after material equibiaxial tensile prestrained to 15%, (d) stress-based FLC, and (e) equivalent failure strain
versus triaxiality (h) plot.
prestraining. For prestraining condition, path dependency of strain-based FLC is well predicted by theoretical isotropic plasticity formulation. Therefore, it can be
said that the path dependency of strain-based FLC
arises from path-dependent stress–strain plasticity theories. For both FLCs, base material and material after
10% uniaxial tensile prestraining are comparatively well
predicted by the HBW criterion. Experimental stressbased FLC can be generated by transforming FLC
from strain space to stress space by J2 plasticity theory.
It can be observed from Figure 10(c) that experimental
stress-based FLC for both base material and material
after 10% tensile prestraining is almost the same.
Similarly, in Figure 10(d), also experimental equivalent
failure strain versus triaxiality (h) plot for both base
material and material after 10% tensile prestraining is
almost the same. Therefore, from Figure 10(c) and (d),
it can be observed that both stress-based FLC and
equivalent failure strain versus triaxiality (h) plot are
strain path independent.
187
Paul
Steel Fep04
1.
17
Brunet and Morestin investigated the effect of nonlinear strain paths in FLC for steel Fep04. The specimens were first prestrained in uniaxial and equibiaxial
tension; thereafter, FLCs were generated. In Brunet
and Morestin’s experiments, uniaxial tensile prestraining was done at 10% strain level and equibiaxial tensile
prestraining was conducted at 15% strain level. Strainbased FLC predictions by different theories are shown
in Figure 11(a) for base Fep04 steel sheet, Figure 11(b)
for Fep04 steel sheet after 10% uniaxial tensile prestraining, and Figure 11(c) for Fep04 steel sheet after
15% equibiaxial tensile prestraining. The HBW criterion predicts well in base material as well as in uniaxial
prestrained material. Similarly, like AISI 1012 low carbon steel, strain-based FLC for uniaxial and equibiaxial
tensile prestraining conditions generated from theoretical isotropic plasticity formulation for steel Fep04 is
also capable to capture path dependency of strain-based
FLC. This path dependency of strain-based FLC solely
arises from path-dependent stress–strain plasticity theories, which is observed in this study.
The HBW criterion predicts well is also reflected on
stress-based FLC in Figure 11(d) and equivalent failure
strain versus triaxiality (h) plot in Figure 11(e).
Experimental pure, uniaxial and biaxial prestrained
FLCs are converted into stress space from strain space
and are shown in Figure 11(d). Few experimental
points in biaxial prestrained FLC are excluded during
conversion from strain space to stress space, because
principal strains in the second loading operation is
small, and there is a possibility of error during transformation. From Figure 11(d), it can be observed that
experimental stress-based FLC for the base material,
materials after uniaxial and biaxial prestraining is
almost the same. These results have supported the earlier finding that stress-based FLC is strain path independent. Equivalent failure strains are calculated from
pure, uniaxial, and biaxial prestrained experimental
FLC and are plotted with triaxiality (h) in Figure
11(e). It can be observed from Figure 11(e) that equivalent failure strain versus triaxiality (h) plot for pure,
uniaxial, and biaxial prestrained conditions is almost
the same, that is, equivalent failure strain versus triaxiality (h) plot is also strain path independent.
Concluding remarks
Theoretical formulations of strain- and stress-based FLD
by different instability criteria are presented in this study;
they are the HS criterion, the SR criterion, the Hill–Tresca
criterion, and the HBW criterion. Comparative studies are
also done among those FLDs generated from different criteria with the help of experimental data available in the literatures, TRIP 600 steel, DP600 steel, AA 3105 Al alloy,
AISI 1012 low carbon steel, and steel Fep04. From this
study, the following conclusions can be made:
2.
3.
4.
This investigation supports the statement by
presenting data of AISI 1012 low carbon steel
and Fep04 steel that the stress-based FLD is
strain path independent.
Path dependency of strain-based FLC arises from
path-dependent stress–strain plasticity theories.
From the same data, it is also confirmed that the
conventional equivalent failure strain versus
triaxiality (h) plot is also strain path independent.
FLCs generated through the HBW criterion
match comparatively well among the discussed
models with the experimental FLCs taken from
the literatures in the range of uniaxial tension to
equibiaxial tension (20.5 4 a 4 1).
Funding
This research received no specific grant from any funding agency in the public, commercial, or not-for-profit
sectors.
Acknowledgement
The author acknowledges Dr Rahul Kr. Verma and Dr
Saurabh Kundu, R&D, Tata Steel Limited, Jamshedpur,
India, and Dr Soumitra Tarafder, Head HRG, National
Metallurgical Laboratory, Jamshedpur, India, for their
valuable suggestions.
References
1. Keeler SP and Backhofen WA. Plastic instability and
fracture in sheet stretched over rigid punches. ASM
Trans Q 1964; 56: 25–48.
2. Goodwin GM. Application of strain analysis to sheet
metal forming in the press shop. SAE paper 680093,
1968.
3. Marciniak Z, Kuczynski K and Pokora T. Influence of
the plastic properties of a material on the forming limit
curve for sheet metal in tension. Int J Mech Sci 1973; 15:
789–805.
4. Nakazima K, Kikuuma T and Hasuka K. Study on the
formability of steel sheets. Yawata technical report no. 264,
1968, pp.141–154.
5. Marciniak ZA and Duncan J. Mechanics of sheet metal
forming. London: Edward Arnold, 1992.
6. Stoughton TB. General forming limit criterion for sheet
metal forming. Int J Mech Sci 2000; 42: 1–27.
7. Kleemola HJ and Pelkkikangas MT. Effect of predeformation and strain path on the forming limits of steel,
copper, and brass. Sheet Metal Ind 1977; 63: 591–599.
8. Arrieux R, Bedrin C and Boivin M. Determination of an
intrinsic forming limit stress diagram for isotropic metal
sheets. In: Proceedings of the 12th Biennial Congress of
the IDDRG, Santa Margherita Ligure, Italy, 1982,
pp.61–71.
9. Swift HW. Plastic instability under plane stress. J Mech
Phys Solids 1952; 1: 1–18.
10. Hill R. On discontinuous plastic states with special reference to localized necking in thin sheets. J Mech Phys
Solids 1952; 1: 19–30.
188
11. Storen S and Rice JR. Localized necking in thin sheets.
J Mech Phys Solids 1975; 23: 421–441.
12. Marciniak Z and Kuczynski K. Limit strains in the processes of stretch forming sheet steel. J Mech Phys Solids
1967; 1: 609–620.
13. Ghazanfari A and Assempour A. Calibration of forming
limit diagrams using a modified Marciniak–Kuczynski
model and an empirical law. Mater Design 2012; 34:
185–191.
14. Bressan JD and Williams JA. The use of a shear instability criterion to predict local necking in sheet metal deformation. Int J Mech Sci 1983; 25: 155–168.
15. Tresca H. Mémoire sur l’écoulement des corps solides
soumis à de fortes pressions. CR Acad Sci Paris 1864;
59: 754.
16. Uthaisangsuk V, Prahl U and Bleck W. Characterisation
of formability behaviour of multiphase steels by micromechanical modeling. Int J Fracture 2009; 157: 55–69.
17. Brunet M and Morestin F. Experimental and analytical
necking studies of anisotropic sheet metals. J Mater Process Tech 2001; 112(2–3): 214–226.
18. Nurcheshmeh M and Green DE. Prediction of sheet
forming limits with Marciniak and Kuczynski analysis
using combined isotropic–nonlinear kinematic hardening.
Int J Mech Sci 2011; 53(2): 145–153.
19. Aghaie-Khafri M and Mahmudi R. Predicting of plastic
instability and forming limit diagrams. Int J Mech Sci
2004; 46(9): 1289–1306.
20. Keeler SP and Brazier WG. Relationship between laboratory material properties and press shop formability. In:
Journal of Strain Analysis 48(3)
21.
22.
23.
24.
25.
26.
27.
28.
Proceedings of conference on microalloy 1977, vol. 75,
pp.517–528.
Stoughton TB and Zhu X. Review of theoretical models
of the strain-based FLD and their relevance to the stressbased FLD. Int J Plasticity 2004; 20(8–9): 1463–1486.
Alsos HS, Hopperstad OS, Törnqvist R, et al. Analytical
and numerical analysis of sheet metal instability using a
stress based criterion. Int J Solids Struct 2008; 45(7–8):
2042–2055.
Wierzbicki T, Bao Y, Lee YW, et al. Calibration and evaluation of seven fracture models. Int J Mech Sci 2005; 47:
719–743.
Simha CHM, Gholipour J, Bardelcik A, et al. Prediction
of necking in tubular hydroforming using an extended
stress-based FLC. J Eng Mater: T ASME 2007; 129(1):
136–147.
Bai Y and Wierzbicki T. Application of extended Mohr–
Coulomb criterion to ductile fracture. Int J Fracture
2010; 161: 1–20.
Johnson GR and Cook WH. Fracture characteristics of
three metals subjected to various strains, strain rates,
temperatures and pressures. Eng Fract Mech 1985; 21(1):
31–48.
Paul SK. Real microstructure based micromechanical
model to simulate microstructural level deformation
behavior and failure initiation in DP 590 steel. Mater
Design 2013; 44: 397–406.
Paul SK and Kumar A. Micromechanics based modeling
to predict flow behavior and plastic strain localization of
dual phase steels. Comp Mater Sci 2012; 63: 66–74.