MECHANICS OF POLYMERS - Technische Universität Darmstadt · contact: [email protected]...
Transcript of MECHANICS OF POLYMERS - Technische Universität Darmstadt · contact: [email protected]...
contact: [email protected]
MECHANICS OF POLYMERS
by
Stefan Kolling
Technische Universität Darmstadt, WS 2013/14
Course Contents and Goals
Topics
Basics on continuum mechanics
(no chemistry!)
Classification of polymers
Material modeling
Damage and failure
Composites
(glass fiber reinforces plastics)
Goals
General aspects of structural analysis
with focus on numerical simulation
Background and fundamentals
Experimental requirements and input
data for numerical simulation
Limits of the chosen formulations
2 Mechanics of Polymers
Polymer Structures
Plastics is a group name comprising many different materials
Mechanical response at room temperature may be glassy or
rubbery
str
ess
1 2
3
4
5
strain
ε
1 glasslike behaviour
2 plastic or viscous flow
3 low ductility
4 high ductility
5 rubbery
amorphous
thermoplastic
crystalline
thermoplastic
thermoset plastic
(duroplast)
elastomer thermoplastic
4 Mechanics of Polymers
Glass Transition and Temperature – Strain Rate Relation
Example: polyethylene
TTc Tg
glass
rubber
G
0
AKTe
Ref
Ref
1 1log C
T T
Roughly: for certain thermoplastics, 10°C decrease of temperature
corresponds to an increase of one order of magnitude in strain rate,
so the rate effects have a higher relative importance than in the case of
metals
Arrhenius’ law
5 Mechanics of Polymers
Glass transition of PVB (Saflex):
Temperature
6 Mechanics of Polymers
„Room temperature“
Source: Hooper, Blackman, Dear – The mechanical behaviour of poly(vinyl butyral) at different strain magnitudes and strain rates, J Mater Sci (2012)
Consistency
Glass transistion and melting temperature
8
amorphous
= glassy
Tg [°C]
PS 105
PMMA 120
PVC 80
PC 150
PET 85
semicrystalline
Tm [°C]
PET 265
PBT 225
PA6 220
PA66 265
PE 110-135
PP 165
elastomers
Tg [°C]
BR -90
SBR -50
PEA -25
PBA -60
thermoplastics
Mechanics of Polymers
Usage of Polymers
In Automotive Industry
Percentage of polymeric
materials in a
middle class car (2003)
63,8%17,0%
4,7%
0,3%2,2%
0,5%
4,4%
7,1%
Stahl und Eisen
Polymere
Leichtmetalle
Betriebsstoffe
Sonstige Werkstoffe
Buntmetalle
Pozeßpolymere
Elektrik/Elektronik
steel
polymers
Al / Mg
other materials
63,8%17,0%
4,7%
0,3%2,2%
0,5%
4,4%
7,1%
Stahl und Eisen
Polymere
Leichtmetalle
Betriebsstoffe
Sonstige Werkstoffe
Buntmetalle
Pozeßpolymere
Elektrik/Elektronik
steel
polymers
Al / Mg
other materials
10 Mechanics of Polymers
Summary
Polymers make life easier, cheaper and more comfortable
They have a wide range of application in engineering
Basic knowhow of polymers is just a must for an analysis engineer
(at least for a good one)
For structural parts made from polymers, computational methods
are still topic of ongoing research and development projects
In what follows we care for analysis methods in the context of
modern mechanics, i,e. with focus on numerical simulations
12 Mechanics of Polymers
Basics on Continuum Mechanics - Contents
Introduction
Measure of Stress
Beam
Definition – Plane Stress – Principal Stress
True and Engineering Stress
Measure of Strain
Definition – Plane Strain – Principal Strain
True and Engineering Strain – Strain Rate
14 Mechanics of Polymers
Introduction
Newton‘s 2nd Law
„The alteration of motion is ever proportional to the
motive force impressed, and is made in the direction
of the right line in which that force is impressed.“
Consequences hereof:
the force depends on direction and is thus a vector quantity
there is no motive force in the case of statics, i.e. we have neither
translation nor rotation of the system!
This is the fundamental law of mechanics and contains the
conservation of momentum (1st law) and action-reaction (3rd law) as
special cases
Sir Isaac Newton
(1643 –1727)
15 Mechanics of Polymers
Introduction
Newton‘s 2nd Law (modern interpretation)
“The change of momentum of a body is proportional
to the impulse impressed on the body, and happens
along the straight line on which that impulse is
impressed ”
force = rate of momentum:
Case of statics: which leads to
In the case of statics vanishes the resulting force acting on a
body (equilibrium of forces).
Sir Isaac Newton
(1643 –1727)
( )dp d
F mvdt dt
0v 0F
16 Mechanics of Polymers
Introduction
And for rotation of a body:
moment = rate of angular momentum
Case of statics: which leads to
In the case of statics vanishes the resulting moment acting on a
body (equilibrium of moments).
Sir Isaac Newton
(1643 –1727) ( mv)
dL dM r F r
dt dt
0v 0M
17 Mechanics of Polymers
Introduction
Cartesian coordinates
right-hand system, i.e.
here:
x
z
yy
x
z
x
0x y ze e e
1 0 0 0 0
0 1 0 0 0 1 0
0 0 1 1 1
18 Mechanics of Polymers
Introduction
Definition of stress
beam under uniaxial tension
Stress is defined as the local force DN over local area DA
Usually, the unit of stress is 1N/mm² = 1MPa
Under uniaxial stress s we may thus compute the normal force N by
N
DN
DA
0limA
dN
A dA
Ns
D
D
D
A
dN dA N dAs s
A
19 Mechanics of Polymers
True and Engineering Stress
Consider a bar with constant cross section along the entire length
Engineering stress
True stress (Cauchy stress)
Relationship
for incompressible materials, i.e. A0l0=Al, else
00 1 ss
0l
FF
l
initial cross section A0
actual cross section A
0
0
F
As
F
As
0,
0,
necking, i.e.
0 0( )
( )
20 Mechanics of Polymers
2
0 01
s s
Engineering strain
Another definition of strain: true strain (Hencky’s strain)
An infinitesimal change of elongation dl related to the actual length l
defines the true strain increment d
True and Engineering Strain
0
0
0
0
ln ln ln ln
ll
ll
dld
l
dl ll l l
l l
FFx
0l lD
l
0
lnl
l
Heinrich Hencky
(1885-1951)
Mechanics of Polymers 21 * Hencky studied at the TH Darmstadt where he also received his PhD
0
0 0
l l l
l l
D
True Strain vs. Engineering Strain
Relationship between true and engineering strain
True and Engineering Values
0
0
l
l
D
small strain region
0, 0
0ll
0
00
0 0 0
1 1l ll l
l l l
D D
0ln 1
0
lnl
l
22 Mechanics of Polymers
Increase of Volume during Tensile Tests
Relative Volume for =const. :
Example: Terblend® N NM19 (ABS/PA blend by BASF)
Mechanics of Polymers 23
rela
tive v
olu
me [
-]
1st principle strain
volu
me [m
m³]
total volume V(t)
relative volume V(t)/V0
0
exp 1 2V
V
Courtesy of FAT AK27, experiments performed at EMI, Freiburg
True and Engineering Values
Engineering values are always related to the initial geometry
True values are always related to the actual geometry
The difference vanishes for small strain problems (linear
calculations)
Nonlinear FE analysis (e.g. crash) is based on true values and
gives thus true values in the output data!
All material data have to be converted to true data for input in such
FE-computations (see example in section “mechanics of
materials”)
24 Mechanics of Polymers
Stress as a Tensor Quantity
Consider now a beam under angular cross section and compute
Cauchy’s stress
Stress components depend on (the normal of the) cross section!
Later on we will therefore define stress by a second rank tensor
F
cosnF F
F
F
ns
F
F
sintF F
25 Mechanics of Polymers
3D Stress State: Transformation
Transformation in y-z-plane
Transformation matrix 𝚽 is valid for all vectors in ℝ3
For transformation of matrices, e.g. 𝐀 ∈ ℝ3𝑥3: 𝚽T𝐀𝚽
It seems that stresses are transformed rather than
matrices than vectors!
, , , ,P x y z P x
cos siny z
sin cosy z
rotary matrix in y-z-plane Φ
1 0 0
0 cos sin
0 sin cos
x x
y
z
y
z
P
Mechanics of Polymers 26
Stress Tensor
Definition of stress
Stress vector
The stress vector is defined as the local force over local area
Stress components depend on the normal of the cross section!
This mapping is given by the 2nd rank stress tensor s:
that is sometimes called Cauchy’s relation
y
x
z
FD
nt
AD
0limA
dFt
F
A dAD
D
D
t n σ
27 Mechanics of Polymers
Stress Tensor
Three-dimensional stress state (Cauchy stress)
In general, we have the following stress components
Balance of angular momentum results in the symmetry of the stress
tensor, i.e. 6 components are independently:
y
x
z
dx
dy
dz
zs
ys
xs
zy
zxyz
yxxy
xz
yx zx
xy
x
zy
xz yz
y
z
s
s
s
σ
xy xz
xy yz
xz y
y
T
x
z z
s
s
s
σ σ
Augustin Louis Cauchy
1789-1857
28 Mechanics of Polymers
12 13
12 23
13 2
11
22
33 3
T
s
s
s
σ σAlternatively:
Stress Tensor
Balance of angular momentum
zy
zy
yz
yz
sz
sz
sy
sy
y
z
x’
zx
zx
xz
xz
sz
sz
sx
sx
x
z
y’
sx
xy
xy
yx
yx
sx
sy
sy
z’
x
y
' 0 2 22 2
0
yz zy
yz zy
yz zy
dy dzM x dx dz dx dy
dx dy dz dx dy dz
' 0 2 22 2
0
zx xz
zx xz
zx xz
dz dxM y dx dy dz dy
dx dy dz dx dy dz
' 0 2 22 2
0
xy yx
xy yx
xy yx
dx dyM z dy dz dx dz
dx dy dz dx dy dz
29 Mechanics of Polymers
Stress Tensor
Computation of the stress vector 𝑡
Stress vector
Example: stress in x-z-plane
y
x
z
FD
nt
AD
0 0
1 1
0 0
xy xz xy
xy yz
xz yz
x
yz
y y
z
n t n
s
s
s
s
σ
0limA
dFt
F
A dAD
D
D
30 Mechanics of Polymers
Stress Tensor
Transformation (z-Rotation)
y
x
sy
yx
xy
sx
s
s
s s s s s
s s s s s
s s
1
2
1
22 2
1
2
1
22 2
1
22 2
x y x y xy
x y x y xy
x y xy
cos( ) sin( )
cos( ) sin( )
sin( ) cos( )
TΦ σΦ
31 Mechanics of Polymers
Objectivity of the Stress Tensor
The components of the stress tensor depend on the section under
consideration (tensor property)
Transformation of the coordinate system, however, may not affect
the state of stress (principle of objectivity), i.e. uniaxial stress
remains uniaxial stress :
y
x*
x
y*
0 0 0 0 0
0 0 0 * 0 0
0 0 0 0 0 0
32 Mechanics of Polymers
Stress Tensor
Principal stress
A unique transformation of the stress tensor s results in a stress
state for that no shear stress exist
We call this state principal stress and the corresponding axis principal
axis
xy xz
xy yz
xz yz
x
y
z
s
s
s
1
2
3
0 0
0 0
0 0
s
s
s
zs
ys
xs
zy
zxyz
yxxy
xz
1s
2s
3s
y
x
z
21
3
Φ
TΦ σΦ
33 Mechanics of Polymers
Mohr‘s Circles for a three-dimensional state of stresses
Stress tensor in principal axes
Principal shear stresses
Centers of the three Mohr’s circles
34 Mechanics of Polymers
2 3
12
s s
3 1
22
s s
1 2
32
s s
1 2 3diag , ,s s sσ
2 31
2m
s ss
1 32
2m
s ss
s
3s2s1s
1ms
1 23
2m
s ss
3ms2ms
13
2
Christian Otto Mohr
1835 – 1918
Mohr‘s Circles for a three-dimensional state of stresses
Uniaxial stress
Biaxial stress
Hydrostatic stress
35 Mechanics of Polymers
1 2 30,2
s
diag ,0,0sσ
1 2 30,2
m m m m
ss s s s
s
sms
diag , ,0s sσ
1 2 3, 02
s
1 2 3,2
m m m m
ss s s s s
diag , ,s s sσ
1 2 3 0 1 2 3m m ms s s s
s
sms
Christian Otto Mohr
1835 – 1918
Equilibrium Conditions
Method of section: Consider a closed Volume V (boundary V) of a
deformed body B loaded by external forces and body forces
Equilibrium is fulfilled if
with Cauchy’s relation
Applying Gauß’ divergence theorem leads finally to
36 Mechanics of Polymers
V
B
B
q
n
t
dAiF
if
0, 1,2,3i i
V V
t dA f dV i
i it n σ
div
div 0
i i i i i
V V V V V V
i
V
t dA f dV n dA f dV dV f dV
f dV
σ σ
σJohann Carl Friedrich Gauß
1777 - 1855
Equilibrium Conditions
The global equation
is fulfilled for arbitrary volumes if
and as fully written out symbol equation:
Note the time consuming derivation in engineering mechanics!
37 Mechanics of Polymers
div 0i
V
f dV σ
div 0f σ , 0ji i ifs
xx dx
x
ss
xy
xy dxx
y
x
xy
xy
xs
ys
y
y dyy
ss
xy
xy dyy
xf
yfdx
dy
Stress Tensor
Principal stress
Eigenvalue problem
Characteristic equation / Cayley-Hamilton-Theorem
where I1, I2, I3 are the so-called invariants of the stress tensor s
Roots of the characteristic equation leads to 3 (real) eigenvalues, the
principal stresses s1 > s2 > s3
0
t n n
n
s
s
σ
σ 1
3 2
1 2 3
det 0
0 0
x xy xz
xy y yz
xz yz z
I I I
s
s s
s s s s s
s s
σ 1
dA
38 Mechanics of Polymers
Arthur Cayley
1821 - 1895
William Rowan Hamilton
1805 - 1865
n
t
Stress Tensor
Invariants of the stress tensor s
An invariant is a property of a system which remains unchanged
under some transformation
1 1 2 3tr( ) x y zI s s s s s s σ
222
2 2 2
1 2 1 3 2 3
1tr( ) tr( )
2
x y x z y z xy yz xz
I
s s s s s s s s s s s s
σ σ
3 1 2 3det( )
x xy xz
xy y yz
xz yz z
I
s
s s s s
s
σ
39 Mechanics of Polymers
Stress Tensor
Volumetric-deviatoric split
The average normal stress gives the pressure as
Thus, the hydrostatic stress state is given by
The difference between stress tensor s and hydrostatic stress state
defines the deviatoric stress tensor s
1
3m x y zp s s s s
13
13
13
0 0
0 0
0 0
x y z
m x y z
x y z
s s s
s s s s
s s s
1
13
13
13
2
2
2
x y z xy xz
m xy x y z yz
xy yz x y z
s s s
s s s s
s s s
s σ 1
40 Mechanics of Polymers
Stress Tensor
Invariants of the deviator s
An invariant is a property of a system which remains unchanged
under some transformation
I1, J2 (and J3) play an important role in the theory of plasticity
1 tr( ) 0x m y m z mJ s s s s s s s
2 2 2 2 2 22
2 2 21 2 2 3 3 1
1 1:
2 6
1
6
x y y z z x xy yz xzJ s s s s s s
s s s s s s
s s
3 det( )J s
41 Mechanics of Polymers
Stress Tensor
Equivalent stress se
The equivalent stress is a single stress value that can be compared to
the admissible stress of the material
The equivalent stress represents yield condition for ductile materials
and failure criterion for brittle materials
In common use is the equivalent stress that is related to
• maximum principal stress
• maximum shear stress
• octahedral shear stress oct
• VonMises stress svm
oct
e 1 2 3 = max , , s s s s
e max 1 2 2 3 3 1 = 2 = max , , s s s s s s s
42 Mechanics of Polymers
Stress Tensor
VonMises stress svm
Most popular criterion for equivalent stress
The vonMises stress is written in stress components as
The vonMises stress is directly related to the second invariant of the
deviatoric stress tensor and to the octahedral shear stress
2 2 21 2 2 3 3 1
2 2 2 2 2 212
2 2 2 2 2 2
2
2
6
3
vm
x y y z x z xy yz zx
x y z x y y z z x xy yz zx
s s s s s s s
s s s s s s
s s s s s s s s s
2
2
33 :
2vm Js s s
Richard von Mises
(1883-1953)
43 Mechanics of Polymers
3 2
2vm octs
Stress Tensor
Illustration of vonMises stress
for two components s and (e.g. beam) the vonMises stress over
shear stress represents a circle
For arbitrary 3D-stress state vonMises
stress represents a cylinder in the
principal stress space. The direction
of the cylinder is given by the
hydrostatic axis, i.e.
2 23vms s
vonMises stress
experiments (steel)
1s
2s
3s
1 2 3s s s
44 Mechanics of Polymers
Stress Tensor
Illustration of vonMises stress
A cut through the s1-s2-plane of the cylinder gives an ellipse that
represents the state of plane stress
1s
2s
3s2s
1s
plane stress
2 2
1 2 1 2vms s s s s
45 Mechanics of Polymers
Stress Tensor
Illustration of vonMises stress
Invariant plane (BURZYŃSKI-plane)
State of pure shear at p=0
Uniaxial tension
vmsuniaxial
compression
uniaxial
tension
1
3
p
2
1 2
1,
3vmI p J s
0 0 1 1
0 0 0 33 3
0 0 0
x
x
vm
vm x
p trp
ss
s
s s
σσ
shear
31
46 Mechanics of Polymers
Stress Tensor
Triaxiality
The relation of pressure over vonMises stress can be used as a
measure of triaxiality:
vm
p
s
0.333
0.577
vm
p
s00.20.40.6
0
plane strain
biaxial tension uniaxial tension shear
47 Mechanics of Polymers
2
31
3
Stress Tensor
State of plane stress
Most of structural parts made from plastic are modeled by shell
elements that assume a so-called plane stress state,
i.e. in principal axis
What does this mean for the von Mises stress in the invariant plane?
1 1
2 2
3
( , ) 0 0
( , ) 0 0
0 0 00
s s
s s
s
x
y
sx
xy
xy
xy
xy sx
sy
sy
48 Mechanics of Polymers
Plane Stress
1
2
1 1
0 0
0 0 1 ( 1)
0 0 0
vmk k k
s
s s s
σ
triaxiality
1
2
1
( 1) ( 1)
3 1 ( 1)3 1 ( 1)vm
kp k
k kk k
s
s s
bounds:
0
( 1) 1lim lim lim
33 1 ( 1)k k k
k
k k
1 1
( 1) 2lim lim
33 1 ( 1)k k
k
k k
k
vm
p
s
uniaxial tension
biaxial tension
1s
12 ss k
uniaxial tension
biaxial tension
49 Mechanics of Polymers
Plane Stress
),(
),(
2
1
s
s
1s
lower bound: pvm2
3s (biaxial tension)
12 ss k
50 Mechanics of Polymers
Plane Stress - Summary
For shell-like structures, i.e. plane stress state, the vonMises stress
is bounded by
pvm2
3s
Triaxiality thus becomes
3
2
vm
p
s
This defines the requirements/restrictions for experimental work
vmsuniaxial
compression
uniaxial
tension
1
3
p
shear
31
322
3
biaxial
compression
biaxial
tension
51 Mechanics of Polymers
52
Strain Tensor
Reminder: 1D-definition of strain
Lets consider a bar with initial length l0 under uniaxial loading F
the local uniaxial strain is then defined as
If (and only if) the cross section of the bar and the material properties
(Young’s modulus) are constant along the length l0 , we may write
du
dxε
FF
dx
dx+du
FF
,x u
0 0
0
00 0
x l x l
x x
ldu dx l du dx dx l
l
D D ε ε ε ε ε
0l
Mechanics of Polymers
Strain Tensor
In a fully 3-dimesional structural part, the local strain is defined as
And the strain tensor is given analogue to the stress tensor as
T1
2 ε u u
12 13 23
1 1 1 1 1 1, ,
2 2 2 2 2 2xy xz yz
u v u w v w
y x z x z y
11 22 33, ,x y z
u v w
x y z
,y v,x u
,z w
1 1
2 2
1 1
2 2
1 1
2 2
x xy xz
xy y yz
xz yz z
ε
• in total 6 independent strain components
• symmetric by definition
• rotation of a body does not cause any strain
53 Mechanics of Polymers
Strain Tensor
Principal strains
For plane stress, we may expect the following deformation modes
This gives the state of plane strain, i.e. all z-components vanish:
sxsx
x
y
sy
sx
sx
sy
dx
dy
sy
sy
0.5yxdy
0.5xxdx
0.5yydy
0.5xydx0.5
1
2
1
2
x yx
yx y
ε
1
2
3
0 0
0 0
0 0
ε
1
2
0
0
ε respectively and
54 Mechanics of Polymers
Comparison: Plane Stress / Plane Strain
Plane strain vs. plane stress
Dog bone model (fracture mechanics)
In practice: plane stress = shell structures; plane strain = thick shells
3D stress state can only be computed by solids!
plain
stress
plane
strain
x crack
y
plane
strain plain
stress
1
2
0 0
0 0
0 0 0
s
s
σ
1
2
0 0
0 0
0 0 0
ε
55 Mechanics of Polymers
Generalizations
Initial (reference) and current (actual) configuration
We consider an undeformed body B0. A material point X within this
body is defined by its spatial coordinates. This state is called
reference configuration.
The deformed body B is characterized by its coordinates x. This state
is called current or actual configuration.
56 Mechanics of Polymers
y
x
z
Generalizations
Displacement
Deformation gradient
Transformation of a volume element dV by the Jacobian J
Relation between the deformation gradient and the displacement
57 Mechanics of Polymers
Generalizations
Measure of strain
the deformation gradient can be uniquely decomposed into a proper
orthogonal rotation tensor R = R−T with det R = 1 and a symmetric and
positive definite right stretch tensor U = UT and left stretch tensor V =
VT respectively
The squares of the right and left stretch tensor define the second rank
left and right Cauchy-Green tensor
With these geometrical measures we may define measures of strain
58 Mechanics of Polymers
Green-Lagrange strain
Euler-Almansi strain
Logarithmic strain
If the displacement gradient is small enough,
the difference between current configuration
and reference configuration vanishes.
Then, the symmetric part of the displacement
gradient describes the infinitesimal strain
Generalizations
Leonhard Euler
(1707-1783)
59 Mechanics of Polymers
Generalizations
Measure of stress
Stress vector in current and reference configuration
The symmetric Cauchy stress tensor σ is also referred
to as true stress tensor. The Piola-Kirchhoff stress
tensor P is the nominal or engineering stress:
Since P is unsymmetric, it is instructive to introduce the so-called
second Piola-Kirchhoff stress S as
This quantity has no physical meaning but is just defined as a
symmetric measure in the reference configuration
Gustav Robert Kirchhoff
(1824-1887)
60 Mechanics of Polymers
Material Modeling
Rheological Models
Classification of Materials
Linear Elasticity
Hyperelasticity
Visco-Elasticity
Plasticity and Visco-Plasticity
Mechanics of Polymers 61
Rheological Basic Models
Spring
Damper (dashpot)
Slider
Mechanics of Polymers 62
s s
E
s
s
s ssy
s
E
linear (elasticity)
non-linear (hyperelasticity)
s
linear
non-linear
(not available in most FE packages)
non-linear hardening
linear hardening
perfect plasticity
sy
Rheological Models
These basic models in combination allow for the formulation of all
kind of stress-strain relations
Examples:
Mechanics of Polymers 63
s s
visco-elasticity
s
elasto-visco-plasticity
s
s
s
Classification of Materials
From an engineering point of view (focus on simulation), it is
instructive to subdivide materials according to their mechanical
behavior into
elastic materials
viscous materials
plastic materials
Examples
Nearly all materials are elastic for small deformations. At large
deformations, rubber-like materials and recoverable foams are (non-
linear) elastic
Polymers are strain rate dependent to some degree. Under cyclic
loading they convert mechanical energy to heat which causes material
damping
Plastics show permanent deformation above yield stress
usually we have a combination of them
64 Mechanics of Polymers
Classification of Materials
To characterize a material phenomenologically, we consider a
uniaxial tensile/compression test with unloading
Hereby we use engineering stresses and engineering strains for a
rough subdivision where A0 is the initial cross section and l0 the initial
length.
For the dynamic response, strain rate dependent tests are performed
subsequently (pendulum test, drop tower test, ...)
0
FA 0
1ll
t
FF
F
0l
cross section A0
65 Mechanics of Polymers
Linear Elastic Materials
The loading path follows a straight stress-strain path
The deformations remain small and the unloading
path corresponds to the loading path
Slope corresponds to Young’s modulus1 E
This behaviour is called linear elastic
s
F
F
1E
Thomas Young
(1773-1829)
1the idea can be traced back to a paper by Leonhard Euler published in 1727, some 80 years before Young's publication
66 Mechanics of Polymers
The linear relation between stress sij and
strain kl is mapped by the 4th rank
elasticity tensor Cijkl :
Symmetry:
Cijkl = Cjikl because of the stress tensor symmetry sij = sji
Cijkl = Cijlk because of the strain tensor symmetry kl = lk
Cijkl = Cklij holds if a strain energy density W exists, such that
(Schwarz’ theorem)
Linear Elasticity: Elasticity Tensor
σ Cε ij ijkl klCs
67 Mechanics of Polymers
2 2
,ij
ij ijkl
ij kl ij kl kl ij
W W WC
ss
Karl Hermann Amandus Schwarz
(1843 –1921)
Because of the elasticity tensor symmetry
we may rearrange all stress tensor components in a
6-dimensional vector (and also for the strain
tensor components)
The relation between these two vectors is mapped
by a 6x6 matrix which contains all elastic constants:
Linear Elasticity: Voigt’s Notation
Woldemar Voigt
(1850-1919)
68 Mechanics of Polymers
Linear Elasticity
In anisotropic materials, the number of constants depends on the
internal structure
triclinic
rhombic
tetragonal
69 Mechanics of Polymers
Linear Elasticity
In anisotropic materials, the number of constants depends on the
internal structure
hexagonal (transverse isotropic)
cubic
isotropic
70 Mechanics of Polymers
Linear Elasticity
Isotropic linear elastic materials can be expressed
by 2 parameters
where l and m are Lamé constants; alternatively
E = Young’s modulus and = Poisson’s ratio
m
m
m
mlll
lmll
llml
00000
00000
00000
0002
0002
0002
C
Gabriel Lamé
(1795-1870)
3 2E
m l m
l m
2
l
l m
Siméon Denis Poisson
(1781-1840)
71 Mechanics of Polymers
Plane Stress vs. Plane Strain: Note the Difference!
Plane stress (ESZ)
Plane strain (EVZ)
Mechanics of Polymers 73
Non-Linear Elastic Materials
The loading path follows a non-linear stress-strain curve
The unloading path ideally corresponds to the loading path.
This behaviour is called hypoelastic or hyperelastic depending on
the theoretical formulation
s
F
F
74 Mechanics of Polymers
Non-Linear Elastic Materials
Examples: Rubber-like materials where internal damping can be
neglected
engine mount
Hardy-disc tire
head impactor
s
75 Mechanics of Polymers
Hyperelasticity
Definition
In a hyperelastic material, both stress and strain energy are path-
independent functions of the current deformation
Consequently, the strain energy function W per unit undeformed
volume can be used as a potential function to compute the stress
by derivation:
In hyperelasticity it exists a strain energy function from which the
stresses can be computed by derivation with respect to the strain
Mechanics of Polymers 76
2W W
E C
2
1
2 1: ( ) ( )
t
t
W dt W W E E E
Hyperelasticity
The given definition of hyperelasticity is equivalently fulfilled by the
first law of thermodynamics (energy balance, no dissipation):
rate of internal work
rate of free energy
Inserting yields:
Mechanics of Polymers 77
2W W
C E
Hyperelasticity
W can be expressed in terms of total strain E or principal stretch
ratios λ𝑖 =𝑙𝑖
𝑙0𝑖 respectively
True stress in global reference frame:
True stress in principal (true stress) reference frame:
78
WE
xGrad x
X
F
ikj
iλ
W
λλσ
1
Mechanics of Polymers
T1 1
2 2 E C 1 F F 1
T0
T
12
VW W
J V
σ F F
E F F 1
1
Jσ
1 2 3
2 3 1 1 3 2 2 1 3
1 1 1i.e. , and
W W Wσ σ σ
λ λ λ λ λ λ λ λ λ
Hyperelasticity
For an isotropic material the energy function should depend only
on the strain invariants , e.g. in terms of C = FTF:
or on the principal stretches:
Invariants of the right Cauchy-Green tensor:
79
1 2 3, ,W W I I I
2 2 2
1 1 2 3
2 2 2 2 2 2 2
2 1 1 2 2 3 3 1
22 2 2 2
3 1 2 3 2
0
: tr
1:
2
det( )
I
I I
VI J
V
l l l
l l l l l l
l l l
1 C C
C C
C
Mechanics of Polymers
12 2 2 2C C
C C C
W W W WI III
I II III
1 1 C C
1
Jσ
1 2 3, ,W W l l likj
iλ
W
λλσ
1
Hyperelastic Material Laws
Conditions for incompressible behavior
Full incompressibility cannot be enforced in explicit codes
To treat the rubber as an unconstrained material, a hydrostatic
work term is included in the strain energy function, e.g.
This work term is also known as
“Equation of State” (EOS)
A confined compression test allows
validation of the hydrostatic penalty K
80
0.5 2 1 3
E EG
0.5 0.5lim lim
3 1 2
EK
1 2 3 1J l l l
1 lnvolW K J J
Mechanics of Polymers
lateral
confinement
One-Parameter Laws: Blatz-Ko
General form for polyurethane foam rubbers (1962):
Simplification (e.g. implemented in LS-DYNA):
81
21
311
12
311
23
3
231
I
I
IGII
GW
11
32
463.0
1
31
IIG
WT 2 11
12 1
1 2
G JJ
σ FF 1
Mechanics of Polymers
Two-Parameter Laws: Mooney-Rivlin
General form of the energy function:
Clearly a stress-free initial state requires:
D is a penalty coefficient related to hydrostatic response:
A Poisson ratio > 0.497 will usually work fine
82
22
1 2 3 3( 3) ( 3) 1 1W A I B I C I D I
BA
C 2
l
l
l
212
51125
00
00
00
BA
DF
T 2 2
1 3 33
2 2 14 1 4
BA BI DI I CI
J J J
σ FF C 1
Mechanics of Polymers
Two-Parameter Laws: Mooney-Rivlin
engineering stress s in uniaxial tension or compression:
This allows to determine A and B by fitting a test result
Linearization:
gives the small strain modulus E=6(A+B)
83
1/2
1/22
0 0
F 0 01
20 0
BA
ls
ll
lll
6 1A Bs l
Mechanics of Polymers
Two-Parameter Laws: Mooney-Rivlin
Uniaxial tensile test
84
2
12 1
1
s
B
A
1 1
1 l
s
l1
eng. stress vs. eng. strain
Mechanics of Polymers
Multiple Parameter Models: Ogden’s Law
In Ogden’s energy function deviatoric and volumetric stresses are
uncoupled:
Principal true stresses follow from derivation
The summed part is clearly deviatoric
If we assume full incompressibility, the deviatoric stresses are a
function of the principal stretch ratios
85
3
* * 1/3
1 2 3 1/31 1
1 1 ln , where and j
nj i
i i i
i j j
W K J J J JJ
m ll l l l l l
Mechanics of Polymers
J
JK
J
n
j k
ki
j
i
j
j1
31
3
1
**
l
lm
s
* * *1
, , , , ,i id i j k i id i j k
JJ K p
Js s l l l s s l l l
Multiple Parameter Models: Ogden’s Law
for n=2, 1=2 and 2=-2, we get Mooney-Rivlin’s material for the
incompressible case:
86 Mechanics of Polymers
3 2 3 31 2
1 1 1 11 2
2 2 2 2 2 21 21 2 3 1 2 3
2 2 2 2 2 21 2 1 21 1 2 2 3 3 1 1 2
1 2
1 1 1
3 32 2
3 3 3 32 2 2 2
3 3
j j jj
i i i
i j i ij
A B
W
I I I
A I B I
m m ml l l
m ml l l l l l
m m m ml l l l l l
*
1 2 3 1, i iJ l l l l l
Further Strain Energy Functions in Terms of Invariants
88
)1(21
3I2
21
2
v
v
Jv
vμW
b
2
1 2 v
vJ Jm
τ σ 1 b
Blatz-Ko Material
Mooney-Rivlin Material
25.01 )1D()1C()3B(II)3A(I),II,I( JJJWbbbb
2 2 42 (A BI ) 2B 4 (D ( 1) C ) J J J J 2
bτ σ b b 1
Yeoh Material / Neo-Hooke Material
3
3
2
21 )3(IC)3(IC)3(IC bbb
W
b)()(τ~bb
3IC63IC4C 2
321
Mechanics of Polymers
Further Strain Energy Functions in Terms of Invariants
89
Van der Waals Material (User Defined)
2
3
2
2
3~
3
21ln 3
IaW m lm
bb
II 1I ~
I
)3/()3~
( 2
mI l
2
bbbτ ' 1 2 )1(I 2' 2~ WW
2
1
2
3~
21
1
2
1~'
Ia
I
WW
m
Mechanics of Polymers
Further Strain Energy Functions in Terms of Invariants
90
27I
1050
119I
20
13I
2
1 3
2
2
bbbNN
W m
...243I
673750
51981I
7000
19 5
4
4
3 bbNN
bτbbbb
...134750
I 519
1750
I 19
350
I 11
10
I
2
12~
4
4
3
3
2
2
NNNNm
Arruda Boyce Material (MT 127)
Mechanics of Polymers
Further Strain Energy Functions in Terms of Principal Stretches
91
11
3321
1
jjjj nbbbbm
j j
jJ
nb
CW lll
Simplified Rubber Model (material no. 181)
i 1,2,3
1211
1
1 n
nbb
m
j
j
jjCJ llτ
Uniaxial Tension:
nnearly incompressibility:
Mechanics of Polymers
Further Strain Energy Functions in Terms of Principal Stretches
92
3
1
β
i2
2
2
2
1λ2
))3(I1ln()3(I1
)3(I )1(
2 i
ec GGW
b
b
b
Extended Tube Material (User Defined)
llll
ll 2
221-22
421 2
3))-2(1(
)1(1
2 ec GGJτ
Uniaxial Tension:
Mechanics of Polymers
Applications: Non-Homogenous Shear
93
Simulation of complex deformation
Parameter identification of material models
based on additional uniaxial tensile tests
satisfactory approximation up to 50 %
strain
Mat_181 result identical to experiment
Mechanics of Polymers
Applications: Non-Homogenous Shear
94
good agreement for displacements in x-direction
satisfactory agreement in z-direction
Mechanics of Polymers
Applications: Non-Homogenous Shear
95
well reproduced displacements in x-direction
misleading results in z-direction
quite reasonable agreement with uniaxial experiments, but
not capable to simulate combined non-homogeneous deformation
Mechanics of Polymers
Applications - Hardy Disc
96
Based on this uniaxial tests, parameter identification
compression test bending test System:
Iterative validation of compression test with Ogden material
Based on Ogden material parameters creation of uniaxial tests
Mechanics of Polymers
Applications - Hardy Disc under Compression
97
Good approximation in x-direction
Neo-Hooke material shows slight stiffening
Mechanics of Polymers
Applications - Hardy Disc under Bending Load
98
Well approximations in both loading cases with Extended Tube-, Yeoh- and
Van der Waals-material
Mooney-Rivlin / Mat181 based on uniaxial tests may lead to differences
Mechanics of Polymers
Example of a transmission-disk
99
Hardy-disc:
Du Bois, Faßnacht & Kolling, LS-DYNA Forum, Bad Mergentheim,
2002
Validation
compression
test
Timmel, Kaliske & Kolling, LS-DYNA Forum, Bamberg 2004
deformation EuroNCAP
Courtesey of Daimler AG, Sindelfingen
Mechanics of Polymers
Non-Linear Viscous Materials
The loading path follows again a non-linear stress-strain curve
Now, the unloading path does not correspond to the loading path
and a hysteresis loop is formed
We will call this behaviour visco-hyperelastic or “strain rate
dependent hyperelastic” respectively
F
F
s
100 Mechanics of Polymers
Example: PU foam, strain rate dependency (RG50)
Dynamic test, loading only (no unloading)
nonlinear viscosity!
[EMI 1999, Mills 2003]
101 Mechanics of Polymers
• Extremely high compression
up to 98%
• Stability problems
• Time step size!
• Contact problems
• Sharp impactors cause high
deformation gradients in foam
parts
• Lagrangean finite elements
cannot follow the
corresponding deformed
shapes unlimitedly
Example: PU-Foam
102 Mechanics of Polymers
Linear Viscous Materials
The loading path follows a slightly non-linear stress-strain curve
Now, the unloading path does not correspond to the loading path
and a hysteresis loop is formed
We will call this behaviour visco-elastic
Example: thermoplastics at small strains
F
F
s
103 Mechanics of Polymers
Linear Viscoelasticity
Maxwell1 element (1867)
1 James Clerk Maxwell (1831 – 1879), Scottish theoretical physicist and mathematician
s s
E
1 1
S D
S D
S S S S
D D
E E E
s s s
s s
s s
s
Equilibrium
Total strain
Material law
104 Mechanics of Polymers
0 1 2 3 4 5 6 7 8 9 100
0.1
0.2
0.3
0.4
0.5
0.6
0.7
0.8
0.9
1
dimensionless time t E/ [-]
dim
en
sio
nle
ss s
tre
ss s
/ E
0
Maxwell element – sudden loading: 𝜀 𝑡 = 𝜀0 = 𝑐𝑜𝑛𝑠𝑡
Exponential decay equation
Linear Viscoelasticity
0 0
E 0E
Es s
0
0 0
( ) expE
t t
E
s s
s
In this dimensionless
diagram, the response is
independent on the chosen
material parameters
105 Mechanics of Polymers
Maxwell element – sudden loading: 𝜀 𝑡 = 𝜀0 = 𝑐𝑜𝑛𝑠𝑡
Notation:
wherw 𝜏 =𝜂
𝐸=:
1
𝛽 is the exponential time constant and is the
decay rate. Thus the relaxation function yields
Linear Viscoelasticity
0 0
E
106 Mechanics of Polymers
0 0 0( ) exp exp expE t
t t ts s s s
0
0
( )( ) exp exp
( )
tE t t E t
t
ss
Maxwell Element + Spring in parallel
logarithmic plotting
of the relaxation
function gives a
better overview
Alternatively:
Linear Viscoelasticity
107 Mechanics of Polymers
0 0
E0
E
E0 / 0
0 0( ) expE t E E t
log ( )E t
log t
0
E0+E
E
0 0( ) expG t G G t
Generalized Maxwell Element
In 3D expressed by convolution integrals:
The relaxation functions are represented in
terms of Prony series consisting of a set of
material parameters that have to be identified (measured)
Linear Viscoelasticity
108 Mechanics of Polymers
0G
1G
2G
3G
11 / G
22 /G
33 / G
00
0
1
( ) expN
i i
i
G t G G t
visc d
10
visc
10
s εi
ki
t Nt β
i
i
t Nt β
i v
i
t G e d
p t K e ε d
Gaspard de Prony
(1755 - 1839)
visc visc visc( ) ( ) ( )t t p t σ s 1
How to Measure the Relaxation Curves?
Time-temperature shift function (WLF shift)
Analytical approximation by Williams, Landel and Ferry1
Mechanics of Polymers 109
1M.L. Williams, R.F. Landel, J.D. Ferry: The Temperature Dependence of Relaxation Mechanisms in Amorphous
Polymers and Other Glass-forming Liquids. Journal of the American Chemical Society 77, 1955, pp. 3701
( )T
tG t f
a
( )g
T
g
A T Ta
B T T
with
A = 17.44K and B = 51.6K
for amorphous polymers
t
G
t
G
WLF
T4
T3
T2
T1
Relaxation Tests
How to Measure the Relaxation Curves?
Dynamic mechanical analysis (DMA)
Mechanics of Polymers 110
TTg
glass
rubber
G
ˆ( ) sinx t x t
( ), ( ),G T G
e.g. DMA/SDTA861e by Mettler Toledo
• fmax = 1000 Hz
• T= -150 °C - 500 °C
Plasticity: Thermoplastics
Visco-plastic Materials (Thermoplastics, Thermosets, …)
Permanent (plastic) deformation
in contrast to elastic materials
The unloading path ideally
follows a straight line (Hooke)
All polymers are strain rate
dependent to some degree, i.e.
they are visco-plastic
Von Mises yield criterion is usually used in practise
(OK for most of the metals not for plastics!)
F
F
s
111 Mechanics of Polymers
Localization and Increase of Volume during plastic flow
Mechanics of Polymers 112
Strain at break depends on the
chosen mean area
The decrease of the stress after
yield strength is a artefact of
the mean area, not a material
property.
Crazing
Crazing is the notion of formation of surface cracks
As a consequence thereof:
change of colour to white detectable
crazing leads to plastic (permanent) deformation with increase of
volume
crazing leads to low yield stress values in uniaxial/biaxial tension
seems to occur under high values of hydrostatic tension
113
Crazing
Mechanics of Polymers
Mechanical Behavior of Thermoplastics (Uniaxial Loading)
114
0
5
1 0
1 5
2 0
2 5
0 0 ,0 5 0 ,1 0 ,1 5 0 ,2 0 ,2 5 0 ,3 0 ,3 5 0 ,4 0 ,4 5 0 ,5
wahre Dehnung
wahre
Spannung
Zug
Druck
Tru
e S
tress
True strain
Tru
e S
tress
Different yielding under
tension/compression (and
shear)
Plastic incompressibility for
compression only (p 0.5)
Under tension foam-like (p
0)
Yield curve AND Young‘s Modulus
are strain rate dependent
Non-linear elasticity
Uniform necking due to
stabilisation
No Von Mises type of plasticity!
Visco-elasto-visco-plasticity
True strain
Tensile Test
Compression Test
0
1 0
2 0
3 0
0 0 ,1 0 ,2 0 ,3 0 ,4 0 ,5 0 ,6
wahre Dehnung
wahre
Spannung
0.1mm/s
7mm/s
500mm/s
Mechanics of Polymers
Material Models
Yield Criteria
Define a yield function f that is zero on the yield surface and less than
zero for elastic states:
• In terms of the stress tensor
• In terms of invariants
Pressure independent yielding: von Mises
where
115 Mechanics of Polymers
ˆ ( )ijf f s 0
ˆ ( , , )f f I I I 1 2 3 0
ˆ ( )f f J 2 0
J 2
2 0ys 3
1s
2s
3s
116
Material Models
Pressure dependent yielding (Thermoplastics, …)
For materials that show dependency on triaxiality (most of the
thermoplastics) special yield criteria have to be used
tension
shear
p0
vms
ts
biaxial
tension
biaxial tension
t
shear
s
ss
3
1
compression
compression
c
cs
tension
t
ts
vonMises
SAMP
Mechanics of Polymers
vmf A A p A ps 2 2
0 1 2 0
Experimental Data vs. SAMP - Polyvinyl Chloride (PVC)
117
exp. results taken from Bardenheier 1982
Mechanics of Polymers
Experimental Data vs. SAMP - Polystyrene (PS)
118
exp. results taken from Bardenheier 1982
Mechanics of Polymers
Experimental Data vs. SAMP - Polycarbonate (PC)
119
exp. results taken from Bardenheier 1982
Mechanics of Polymers
Material Models
Isotropic Hardening Curve
f(s) = 0 corresponds the initial yield surface
(p) is a monotonically increasing function of the hardening
parameter p (usually the effective plastic strain)
120 Mechanics of Polymers
( ) ( )pf s 0
1s
2s 3s
s
p
ys
Example: Validation of a Component Test (PP-T10)
Typical behaviour for
thermoplastics:
material cards that are
fitted for uniaxial tension
yield a too soft responds
under bending
and compression
Different yield curves
under compression
and tension
are necessary!
displacement
forc
e
122 Mechanics of Polymers
Associated and Non-Associated Flow Rules
Practical stability condition (Drucker’s first postulate)
Convex yield surface
Associated flow (Drucker’s second postulate)
Plastic strain increments and plastic stress increments are in same
direction:
i.e. plastic flow occurs perpendicular to the yield surface
Non-associated flow
Plastic potential is defined for the direction of yielding
Thus, plastic Poisson’s ratio can be influenced directly!
Mechanics of Polymers 123
p
ij ijd ds 0
p fd d l
s
p gd d l
s
Material Models for Polymers – Summary
Many robust and reliable material models for polymer materials are
available (most of them in commercial FE-packages, too)
The most popular models are implemented in a tabular way due to their
user-friendliness (no parameter identification)
Using the presented models, the deformation behavior of the structure can
be reproduced pretty good
Consideration of the manufacturing process (molding for plastic
components) gives a further improvement of the simulation
Anisotropy is a topic of recent development (integrative simulation)
124 Mechanics of Polymers