Estimating The Strain-Rate-Dependent Parameters of The Cowper-Symonds and Johnson-Cook Material Models Using Taguchi Arrays
Estimating The Strain-Rate-Dependent Parameters of The Cowper-Symonds and Johnson-Cook Material Models Using Taguchi Arrays
Estimating The Strain-Rate-Dependent Parameters of The Cowper-Symonds and Johnson-Cook Material Models Using Taguchi Arrays
In order to reduce R&D costs, a product’s behaviour during use is predicted with numerical simulations in the early phases of R&D. If a
structure is subjected to high-strain-rate loading this effect should be considered in the material models that are used for the numerical
simulations. This article shows how the strain-rate-dependent material parameters can be determined by combining the experimental data
with the numerical simulations. The presented methodology is based on the application of Taguchi arrays to find the most appropriate values
for the strain-rate-dependent parameters. The presented methodology is applied in a practical case, for which the parameters of the Cowper-
Symonds and Johnson-Cook material models are estimated.
Keywords: strain-rate-dependent material behaviour, finite-element method, explicit dynamics, Taguchi arrays
Highlights
• A procedure for modelling the strain-rate-dependent behaviour of materials is presented.
• The parameters of the Cowper-Symonds and Johnson-Cook material models are estimated on the basis of an impact
experiment.
• A simulation plan for estimating the material parameters is developed with the help of Taguchi orthogonal arrays.
• Flow stress according to the Johnson-Cook as follows. After the introductory section and the
material model [3]: theoretical background, the experimental arrangement
and the experimental results are presented. The article
σ flow = σ 0 + B ⋅ ( ε effp ) ⋅
n
+ Et ⋅ ε eff . (3)
p
that they cannot be simply measured and determined, = σ 0 + β ⋅ t ⋅ ε eff
⋅ 1 +
E − Et C
thus they are empirically determined through special
experimental and optimisation processes ([9] to For the C-S material model the strain rate
[13]). For the above-mentioned material models the influences only the yield stress σy. This means that the
parameters that consider the strain-rate dependence plastic curves (the flow stress as a function of strain)
were investigated for many different materials. In the are parallel. The larger the strain rate, the higher the
literature, their typical values for mild steel ([9], [10] flow-stress curve, see Fig. 1a. For high-strain-rate
and [11]), high-yield-strength steel [12], aluminium applications the parameters C and P in Eqs. (1) and
alloys [13], titanium alloys [13], etc. can be found. (3) are usually not estimated from the tensile test, due
Since, on the other hand, no link between the strain- to the limitations of the existing tensile-test equipment
rate parameters and the chemical composition of (maximum strain rates are up to a few hundreds of s-1).
the material was found, these parameters should Together with the tangent Et they were determined on
be identified individually for each material under the basis of the impact experiment.
consideration. Since the temperature effects were neglected in
In this article we will compare the performance our case, the simplified Johnson-Cook (J-C) material
of Cowper-Symonds and Johnson-Cook material model was applied with the parameter m from Eq. (2)
models when applied for simulating the impact of a being equal to 0. This material model is determined
ball on a thin steel plate. The parameters of the two with the following parameters ([16] and [17]): elastic
material models, which cannot be estimated from modulus E, Poisson’s number ν, reference yield stress
the tensile test, were determined from the impact s0, exponent of the flow-stress curve n, scale factor
experiments using the LS-DYNA explicit FE code B for the effective plastic strain, sensitivity c to the
that was combined with a Taguchi array to reduce the logarithm of the strain rate and material density ρ. The
numerical processing effort. The article is structured flow stress is then given by:
Estimating the Strain-Rate-Dependent Parameters of the Cowper-Symonds and Johnson-Cook Material Models using Taguchi Arrays 221
Strojniški vestnik - Journal of Mechanical Engineering 62(2016)4, 220-230
Fig. 1. Flow stress for a) the Cowper-Symonds material model and b) the Johnson-Cook material model
of magnitude, the logarithms of these parameters By applying the Taguchi arrays for the simulation
represent the nine-level factors in the Taguchi array. In plan the number of material-parameter combinations
this manner 81 combinations of the parameter triples that need to be simulated was reduced by a factor of
(Et, C, P) and (B, n, c) were obtained that cover the nine when compared to the full-factorial simulation
whole domains of these parameters, see Fig. 3 for the plan.
parameters of the C-S material model and Fig. 4 for
Table 2. Parameter levels for the J-C material model
the parameters of the J-C material model.
Original parameter levels of parameter B [GPa]
Table 1. Parameters levels for the C-S material model 0.1000 0.1778 0.3162 0.5623 1.0000
1.7783 3.1623 5.6234 10.0000
Original parameter levels of parameter C [ms-1] Original parameter levels of parameter n [-]
0.2154 0.4642 1.0000 2.1544 4.6416 0.001 0.0024 0.0056 0.0133 0.0316
10.0000 21.5443 46.4159 100.0000 0.0750 0.1778 0.4217 1.0000
Original parameter levels of parameter P [-] Original parameter levels of parameter c [-]
1.0000 1.7783 3.1623 5.6234 10.0000 0.001 0.0024 0.0056 0.0133 0.0316
17.7828 31.6228 56.2341 100.0000 0.0750 0.1778 0.4217 1.0000
Original parameter levels of parameter Et [GPa]
0.1000 0.1778 0.3162 0.5623 1.0000
For each combination of the material parameters
1.7783 3.1623 5.6234 10.0000
six numerical simulations were carried out to account
for the six different boundary and initial conditions,
see Table 3. Therefore, when applying the simulation
plan according to the L81(910) Taguchi array 81·6 = 486
numerical simulations were performed for each of the
two material models.
A cost function that measures the deviations
of the experimental and simulation results was
defined so that it measured the difference between
the experimentally determined and simulated data
for the indentation depth H and the position of the
indentation centre Z for the specimen. The averages
of the experimentally determined values for these two
geometrical parameters for two specimen thicknesses
and three different velocities of the ball are listed in
Table 3. The cost function that was used to assess
Fig. 3. Distribution of C-S material-parameter combinations over the goodness-of-fit between the experiments and the
their domains simulations is defined as follows for the C-S and J-C
material models:
k
wH ⋅ ∑ ( H exp − H sim ) +
2
1 i =1
, (5a)
f ( Et , P, C ) =
k k
2
+(1 − wH ) ⋅ ∑ ( Z exp − Z sim )
i =1
k
wH ⋅ ∑ ( H exp − H sim ) +
2
1 i =1
, (5b)
f ( B , n, c ) =
k k
2
+(1 − wH ) ⋅ ∑ ( Z exp − Z sim )
i =1
where k is the number of experimental results with
Fig. 4. Distribution of J-C material-parameter combinations over different boundary and initial conditions (according
their domains to Table 3, k = 6). Hexp and Zexp, are the averaged
Estimating the Strain-Rate-Dependent Parameters of the Cowper-Symonds and Johnson-Cook Material Models using Taguchi Arrays 223
Strojniški vestnik - Journal of Mechanical Engineering 62(2016)4, 220-230
measured maximum indentation depth and its z The measured engineering stress-strain curves are
coordinate for the specimen. Hsim and Zsim are the presented in Fig. 6a and the resulting average true-
maximum indentation depth and its z coordinate stress–true-strain curve is presented in Fig. 6b. This
for the specimen obtained by simulations. wH was a true-stress–true-strain curve was determined with Eqs.
weighting factor in the two cost functions and was (6) and (7), see Dowling [22].
equal to 0.5 in our case.
ε = ln (1 + ε ) , (6)
2 EXPERIMENTAL ARRANGEMENT σ = σ (1 + ε ) . (7)
2.1 Measurement of a Static Stress-Strain Curve ε and σ were the corresponding average
engineering strain and stress, respectively.
The methodology that was described in Section 1
was applied to characterise the strain-rate-dependent
material behaviour of a mild steel E185. Its static 2.2 Experimental Determination of the Material Behaviour
material properties (elastic modulus, yield stress, at High Strain Rates
ultimate tensile stress) were measured according to
the ASTM E8/E8M standard [21] on Zwick/Roell The main objective was to determine the strain-rate-
Z050 testing equipment. dependent material parameters for simulating the
behaviour of a mild-steel sheet metal that is used
as a shield during a turbine burst test. To identify
the corresponding material parameters we designed
experimental apparatus for shooting a steel ball at a
flat specimen. The experimental arrangement was
based on the ASTM D5420 standard [23], which
describes a test method for measuring the impact
resistance of a flat rigid plastic specimen by means
of a striker impacted by a falling weight. During the
impact between the ball and the flat specimen strains
can be measured on the left-hand side of the specimen
with strain gauges. After the impact test the gross
Fig. 5. Zwick/Roell Z050 test stand and the specimen geometric data, i.e., the indentation depth H and the
position of the indentation centre Z, were measured,
The test stand and the specimen geometry are see Fig. 7.
presented in Fig. 5. A total of 21 specimens were The experimental apparatus was mounted on a
tested. The average yield stress and the ultimate tensile testing machine that was originally built for burst tests
strength were 185 MPa and 350 MPa, respectively. on supercharger structures, see Fig. 7.
Fig. 6. a) Measured engineering stress-strain curves; and b) the resulting true-stress–true-strain curve
Fig. 7. a) An experimental device; b) front view and c) upper view of the experimental specimen
To study the different dynamic behaviours of point to the border is progressive and it is difficult to
steel plates with different thicknesses, balls with a calculate the true strain-rate value at the spot of the
diameter of 12 mm and a weight of 7 g were shot at strain gauges. The simulated peak strain rate at the
the centre of the specimens at an angle of 20° with impact point was 5000 s-1.
different velocities that depended on the specimen
thickness, see Table 3. The initial conditions and the Table 3. Combinations of boundary conditions and results from
plate thicknesses where chosen with regard to the experiments
machine’s limitations and the expected application Position of
Average Measured max.
of the results (thin-shelled supercharger burst shield). Experiment Specimen
ball indentation
the max.
condition thickness indentation
The specimens (see Fig. 7) were metal plates with velocity depth, average, depth, average,
number [mm]
dimensions of 98 mm × 60 mm. Two different sheet- [m/s] Hexp [mm] Zexp [mm]
metal thicknesses were tested: 1 mm and 1.5 mm. The 1 1 103 11.37 34.83
specimens were fixed along the shorter side. The free 2 1 109 12.12 34.89
area of the specimen was 60 mm × 60 mm. The impact 3 1 121 13.07 35.11
velocities were measured on the testing machine just 4 1.5 121 10.38 30.19
before the impact point using photo-sensors. For each 5 1.5 131 11.53 29.60
combination of the steel-plate thickness and the impact 6 1.5 139 12.65 30.49
velocity, three test repetitions were usually performed.
The average and the standard deviation of the From the results in Table 3 we can see that the
indentation depth and the position of the indentation scatter of the experimental results is relatively small,
centre are presented in Table 3. Some of the plate which means that the experimental arrangement was
specimens were also equipped with strain gauges appropriate for our study. Furthermore, we can see
for measuring the strains to obtain the strain rates. that the indentation depth increases with the increasing
Such specimen preparation was time consuming and velocity. The indentation depth at a thickness of 1.5
there were only a few specimens for which the strain mm is smaller than for the 1-mm-thick steel plate.
gauges did not break off during the measurements. Besides, it is clear from Table 3 that for the 1.5-mm-
Nevertheless, some strain measurements were thick specimens, the point with the deepest indentation
successful and an agreement between the measured is approximately 30 mm from the lower side of the
and simulated strain rates for the 1-mm-thick plate specimen, just in the centre of the impact. This is not
and the impact velocity of 109 m/s was as follows: the the case for the 1-mm-thick specimens, for which the
measured peak strain rate was approximately 160 s-1, point with the largest indentation is 5 mm from the
whereas the simulated values at that spot were 200 s-1 centre of the impact. The lack of displacement of the
to 250 s-1. The major causes for the difference of 30 % deepest imprint for the thicker plate is a consequence
were the idealisation of the FE model and the FE mesh of the fact that after the plastification almost all of the
resolution, since the strain-rate decay from the impact kinetic energy of the ball was consumed. This was not
Estimating the Strain-Rate-Dependent Parameters of the Cowper-Symonds and Johnson-Cook Material Models using Taguchi Arrays 225
Strojniški vestnik - Journal of Mechanical Engineering 62(2016)4, 220-230
the case for the thinner plate and the ball proceeded dimensions of the specimen were recorded for further
in its direction of travel, though causing an extension processing, like in the experiment (Fig. 7).
of the imprint in the vertical direction. This implies The C-S material model was applied using the
different impact dynamics for the specimens with MAT_PLASTIC_KINEMATIC (MAT3) material
different thicknesses and this should be replicated by model from LS-DYNA ([16] and [17]). This material
the numerical simulations if the strain-rate-dependent model is defined with the following parameters, see
material parameters are properly identified. also Eqs. (1) and (3): material density, elastic modulus,
Poisson’s ratio, yield stress σ0, tangent modulus Et and
3 RESULTS AND DISCUSSION the C-S parameters P and C. The parameters Et, P and
C were estimated using the procedure from Section 1
3.1 FE Model for Identification of the Material Parameters and the above-described FE model.
The J-C material model was applied using the
MAT_SIMPLIFIED_ JOHNSON_COOK (MAT98)
The LS-DYNA explicit dynamic FE code was used
material model from LS-DYNA ([16] and [17]).
to identify the material parameters of the C-S and J-C
This material model is defined with the following
material models [16]. The FE model that was used
parameters, see also Eq. (2): material density, elastic
to simulate the ball-impact experiment from Section
modulus, Poisson’s ratio, yield stress σ0, and the J-C
2 is presented in Fig. 8. The steel sheet model had parameters B, n and c. The latter three parameters
5436 four-node and three-node shell finite elements. were estimated using the procedure from Section 1
The mesh density around the impact area was larger and the above-described FE model.
than in the wider region of the specimen model, to The values of the other material parameters were
accurately simulate the indentation. The mesh density fixed in our simulation: the material density was 7850
was chosen to optimise the processing time for a kg/m3, the elastic modulus was 2.1·105 N/mm2, the
reasonable accuracy of the deformation. The rigid ball yield stress was σ0 = 185 MPa (see Fig. 6) and the
was modelled with 448 solid finite elements. In the Poisson’s ratio was ν = 0.3. The reference strain rate
finite-element model, the nodes on both sides of the ε0 for the J-C model was 1 s-1 and was taken as a
thin sheet-metal plate were fixed (Fig. 8). A rigid ball default value from LS-DYNA. This value usually
was shot into the centre of the sheet at an angle of 20° follows from the tensile-test arrangement. However,
with different impact velocities, which are presented its choice does not phenomenologically influence the
in Table 3. results, since the variation of the parameter ε0
monotonically influences the changes of the estimated
parameter c:
C1 ε( 1 )
= ln (02 ) . (1)
C2 ε0
Fig. 9. Cost-function values for the original domains of the Fig. 12. Cost-function values for the narrowed domains of the
Cowper-Symonds parameters Johnson-Cook parameters
Estimating the Strain-Rate-Dependent Parameters of the Cowper-Symonds and Johnson-Cook Material Models using Taguchi Arrays 227
Strojniški vestnik - Journal of Mechanical Engineering 62(2016)4, 220-230
We actually performed a “nested” Taguchi efficient for estimating the parameters of material
simulation plan in the second phase of the simulations. models that govern the material’s behaviour at high
The resulting distributions of cost-function strain rates. The added value of our approach is
values for the narrowed domains are presented in meaningful, especially in the cases when the number
Fig. 11 for the C-S parameters and in Fig. 12 for the of parameters that need to be identified is relatively
J-C parameters. The best three combinations of the high, with a wide range of potential parameter values.
C-S parameters Et, P and C and the J-C parameters With the Taguchi orthogonal array, a reasonable
B, n and c for the narrowed domains are much closer estimate of the material parameters can be found with
together when compared to the original domains for a relatively small computing effort and a short time.
those parameters. The average values from the three For example, if we applied a methodology that is based
best solutions are listed in Table 5. We can conclude on genetic algorithms and was originally developed
from Table 5 that our estimations of the parameters Et, for estimating the foam-material-model parameters
P, C and B, n, c are comparable to the values reported
[18], the processing times would be approximately
for mild steels in the literature ([9] to [11]), despite
100-times longer. This would be appreciated if the
different experimental arrangements and the fact that
numbers of parameters to be identified and the wide
the strain rates during the experiments were 10 or
ranges were to be increased.
more times higher in our case. We can conclude that
we obtained reasonable estimates of the parameters Et,
P, C and B, n, c for our case. 4 CONCLUSIONS
Plastic flow curves σ − ε effp for the two material
models are presented in Fig. 13. They were calculated The article presents a general approach to estimating
for different strain rates with the averaged parameters the parameters that govern a material’s behaviour
Et, P, C and B, n, c from Table 5. We can see from this at high strain rates. In our approach the Taguchi
figure that the estimates of the parameters for both experimental design was combined with the FE code
material models were consistent, because the flow LS-DYNA to estimate the material parameters using
curves span a similar domain of the σ − ε effp space for the results of the impact test between the ball and thin
the two material models. sheet metal. The presented approach was applied to
From the results we can conclude that the the realistic case of a material-parameter estimation
described methodology, which combines the nested for two different material models, i.e., the C-S and the
design with the FE simulations, can be very time J-C material models.
Table 4. The best three combinations for the original domains of the C-S and J-C material parameters
Parameter C [ms-1] Parameter P [/] Parameter Et [GPa] Cost-function value [/]
Cowper-Symonds Combination 1 21.5443 5.6234 1.0000 1.524
material model Combination 2 46.4159 10.000 1.0000 1.588
Combination 3 2.1544 3.1623 1.0000 1.826
Parameter B [GPa] Parameter n [/] Parameter c [/] Cost-function value [/]
Johnson-Cook Combination 1 0.1778 0.1778 1.0000 2.020
material model Combination 2 0.5623 0.4217 0.0056 2.259
Combination 3 1.7783 1.0000 0.0056 2.129
Table 5. The average of the best three combinations for the narrowed domains of the C-S and J-C material parameters
Parameter C [ms-1] Parameter P [/] Parameter Et [GPa] Cost-function value [/]
Our average 41.0133 6.2000 0.9550 1.522
Cowper-Symonds
Belingardi et al. [12] 3.006–4.987 1.329–1.619 - -
material model
Marais et al. [10] 2.000 5.000 - -
Markiewicz et al. [11] 1.150 7.750 - -
Parameter B [GPa] Parameter n [/] Parameter c [/] Cost-function value [/]
Johnson-Cook Our average 1.9250 0.8183 0.0972 2.138
material model Singh et al. [9] 0.779–2.692 0.743–0.928 0.0144–0.021 -
Marais et al. [10] 0.292 0.310 0.025 -
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