Lecture: Mechanical Properties: Macro Viewpoint

Textbook: Plastics: Materials and Processing (Third
Edition), by A. Brent Young (Pearson, NJ, 2006).
Structure and Properties of Engineering Polymers
Lecture: Mechanical Properties: Macro Viewpoint
Nikolai V. Priezjev

Mechanical Properties: Macro Viewpoint
• Mechanical properties of solids (forces, elastic behavior)
• Mechanical properties of liquids – viscous flows (Newtonian non-
Newtonian regimes, viscosity measurements)
• Viscoelastic materials (definitions, time dependence, short-range, long-
range interactions)
• Plastic stress-strain behavior definitions, mechanical models
• Creep, toughness, impact strength, hardness
• Reinforcements, fillers, toughness modifiers
Reading: Chapter 4 of Plastics: Materials and Processing by A. Brent Strong
https://www.slideshare.net/NikolaiPriezjev

Molecular Weight, Crystallinity and Properties
• Molecular weight Mw: Mass of a mole of chains.
• Tensile strength (TS):
-- often increases with Mw.
--Why? Longer chains are entangled (anchored) better.
• % Crystallinity: % of material that is crystalline.
--TS and E often increase
with % crystallinity.
--Annealing causes
crystalline regions
to grow. % crystallinity
increases.
crystalline
region
amorphous
region
smaller Mw larger Mw

“Semicrystalline” Polymers
~10 nm spacing
Oriented chains with long-range order
Amorphous disordered polymer chains in
the “intercrystalline” region

Molecular structures in both melt and solid states
Schematic representations of the molecular structures in both melt and
solid states for (a) semicrystalline, (b) amorphous, and (c) liquid crystal polymers.
(a) (b) (c)

Melting vs. Glass Transition Temperature
What factors affect Tm
and Tg?
• Both Tm and Tg increase with
increasing chain stiffness
• Chain stiffness increased by
1. Bulky sidegroups
2. Polar groups or
sidegroups
3. Double bonds or aromatic
chain groups
• Regularity (tacticity) – affects
Tm only

Elasticity of Polymers
Random arrangement = High Entropy Stretched = Low Entropy
Entropy is a measure of randomness: The more ordered the chains are, the lower
is the entropy. Spontaneous processes always tend to increase the entropy, which
means that after stretching, the chains will tend to return to a high-entropy state

Viscosity of Polymers
Elastic Deformation
creep
Cross-linking stops the sliding of chains
random
Slow Deformation
Low entropy state

Stress – Strain Behavior of Polymers
Polymers can be brittle (A), plastic (B), or highly elastic (C). Deformation shown by curve C is
totally elastic (rubber-like elasticity, large recoverable strain at low stress levels). This class of
polymers – elastomers.
The description of
stress-strain
behavior is
(somewhat) similar
to that of metals
Strains – deformations
> 1000% possible
(for metals, maximum
strain ~ 100% or less)
brittle polymer
plastic
elastomer
FS of polymer ~ 10% that of metals
elastic modulus
– less than metal
A
B
C

Stress – Strain Behavior of Polymers
Characteristics of stress-strain
behavior:
Modulus of elasticity – defined
as for metals
Ductility (%EL) – defined as for
metals
Yield strength - For plastic
polymers (B), yield strength is
defined by the maximum on curve
just after the elastic region
(different from metals)
Tensile strength is defined at the
fracture point and can be lower
than the yield strength (different
from metals)
• Moduli of elasticity for polymers are ~ 10 MPa –
4 GPa (compare to metals ~ 50 - 400 GPa)
• Tensile strengths are ~ 10 - 100 MPa (compare to
metals, hundreds of MPa to several GPa)
• Elongation can be up to 1000 % in some cases
(< 100% for metals)

YOUNG’S MODULI: COMPARISON
0.2
8
0.6
1
Magnesium,
Aluminum
Platinum
Silver, Gold
Tantalum
Zinc, Ti
Steel, Ni
Molybdenum
Graphite
Si crystal
Glass-soda
Concrete
Si nitride
Al oxide
PC
Wood( grain)
AFRE( fibers)*
CFRE*
GFRE*
Glass fibers only
Carbon fibers only
Aramid fibers only
Epoxy only
0.4
0.8
2
4
6
10
20
40
60
80
100
200
600
800
1000
1200
400
Tin
Cu alloys
Tungsten
<100>
<111>
Si carbide
Diamond
PTFE
HDPE
LDPE
PP
Polyester
PS
PET
CFRE( fibers)*
GFRE( fibers)*
GFRE(|| fibers)*
AFRE(|| fibers)*
CFRE(|| fibers)*
Metals
Alloys
Graphite
Ceramics
Semicond
Polymers
Composites
/fibers
E(GPa)
109 Pa
Based on data in Table B2,
Callister 6e.
Composite data based on
reinforced epoxy with 60 vol%
of aligned
carbon (CFRE),
aramid (AFRE), or
glass (GFRE)
fibers.

YIELD STRENGTH: COMPARISON
Room T values
y(ceramics)
>>y(metals)
>> y(polymers)
Based on data in Table B4,
Callister 6e.
a = annealed
hr = hot rolled
ag = aged
cd = cold drawn
cw = cold worked
qt = quenched & tempered

Stress – Strain Temperature Dependence
Temperature increase leads to:
• Decrease in elastic modulus
• Reduction in tensile strength
• Increase in ductility
polymethyl methacrylate
(PMMA) - Plexiglas
The glass transition
temperature (Tg) of PMMA
ranges from 85 to 165 °C –
all of the above curves are
for temperatures below Tg.
• Mechanical properties of polymers change dramatically with temperature, going from glass-
like brittle behavior at low temperatures to a rubber-like behavior at high temperatures.
• Polymers are also very sensitive to the rate of deformation (strain rate). Decreasing rate of
deformation has the same effect as increasing temperature (T).

Quiz: Stress – Strain Temperature Dependence
polymethyl methacrylate
(PMMA) - Plexiglas
From the stress–strain data for
poly(methyl methacrylate) shown
in Figure estimate the modulus of
elasticity and tensile strength at
room temperature 20C.

Stress – Strain Temperature and Rate Dependence
Temperature increase leads to:
• Decrease in elastic modulus
• Reduction in tensile strength
• Increase in ductility
• Mechanical properties of polymers change dramatically with temperature, going from glass-
like brittle behavior at low temperatures to a rubber-like behavior at high temperatures.
• Polymers are also very sensitive to the rate of deformation (strain rate). Decreasing rate of
deformation has the same effect as increasing temperature (T).
Temperature is fixed
Time dependence of viscoelastic
(polymeric) materials showing the
changes in stress-strain with strain
rate
Strain rate is fixed

Viscoelasticity
Amorphous polymer: glass at low temperatures, rubber at intermediate
temperatures, viscous liquid at high T.
• Low temperatures: elastic deformation at small strains (σ = Eε).
Deformation is instantaneous when load is applied. Deformation is
reversible.
• High temperatures: viscous behavior. Deformation is time dependent
and not reversible.
• Intermediate temperatures: viscoelastic behavior. Instantaneous elastic
strain followed by viscous time dependent strain.
Viscoelastic behavior is determined by rate of strain (elastic for rapidly
applied stress, viscous for slowly applied stress).
Rate dependence of viscoelastic properties in a silicone polymer (Silly Putty).

Viscoelasticity
Load is applied at ta and released at tr

Definition of the Relaxation Modulus
time
Stress,
10 s
10
DL
 fixed 
DL
Lo
Er(0) = E, Young’s Modulus
Er( ) = 0
Glass-like elasticity
Rubber-like
elasticity
Fluid-like
viscous
fixed
r sE

 )10(
)10( 
Viscoelastic Modulus
Modulus of Elasticity
Relaxation Modulus
• Stress relaxation test:
-- strain to o and hold.
-- observe decrease in
stress with time.

Viscoelasticity: Relaxation Modulus
Viscoelasticity can be characterized by the viscoelastic relaxation modulus:
Log time, t
• Sample is strained rapidly to pre-
determined strain.
• Stress required to maintain this strain ε0
over time is measured at constant T.
• Stress decreases with time due to molecular
relaxation processes.
• Relaxation modulus can be defined as:
• Er(t) is also a function of temperature.
Er (t) 
(t)
o

Viscoelasticity: Relaxation Modulus
To show the influence of temperature, the relaxation modulus can be plotted at a fixed time for different T:
Log time, t

Time-Dependent Deformation
• Stress relaxation test:
-- strain to o and hold.
-- observe decrease in
stress with time.
o
r
t
tE



)(
)(
• Relaxation modulus:
• Sample Tg(C) values:
PE (low density)
PE (high density)
PVC
PS
PC
- 110
- 90
+ 87
+100
+150
Selected values from
Table 15.2, Callister
7e.
time
strain
tensile test
o
(t)
• Data: Large drop in Er
for T > Tg.
(amorphous
polystyrene)
103
101
10-1
10-3
105
60 100 140 180
rigid solid
(small relax)
transition
region
T(°C)
Tg
Er (10s)
in MPa
viscous liquid
(large relax)

Time-Temperature Superposition
Construction of the viscoelastic master curve for PIB (Polyisobutylene) at 25 °C reference
temperature by shifting stress relaxation curves obtained at different temperatures horizontally
along the time axis. The shift factor, aT varies with temperature as shown in the inset.
G(t,T) = G(aTt, Tref)

Viscoelasticity
Temperature dependence of the relaxation modulus for different polymer structures
A : Largely crystalline
isotactic polystyrene. Glass
transition region limited –
small amount of amorphous
material
B: Lightly cross-linked
atactic polystyrene –
leathery region extends to
decomposition temperature:
no melting
C: Amorphous polystyrene

Viscoelasticity: Structure Dependence
Crosslinked Branched
Effect of crosslinking
Thermoset
Heavy Crosslinking
Elastomer
Light crosslinking
Effect of crystallinity
Tg Tm
LogMod.OfElasticity
amorphous
50 % Crystalline
100 % crystalline
Tm
LogMod.OfElasticity
Thermoplastic
No crosslinking
Tg
Branched polymer
Crystals act like crosslinks
Strain Induced Crystallization in NR

Viscoelasticity: Structure Dependence
Make two schematic plots of the logarithm of relaxation modulus versus temperature
for an amorphous polymer (a) how the behavior changes with increasing molecular
weight and (b) change in behavior with increasing crosslinking.
Increasing molecular weight increases
both glass-transition and melting
temperatures.
Increasing the degree of crosslinking
will increase the modulus in both
glassy and rubbery regions.

TENSILE RESPONSE: ELASTOMER (ex: rubberband)
• Compare to responses of other polymers:
-- brittle response (aligned, cross-linked & networked case)
-- plastic response (semi-crystalline case)

TENSILE RESPONSE: BRITTLE & PLASTIC
brittle failure
plastic failure
(MPa)

x
x
crystalline
regions
slide
fibrillar
structure
near
failure
crystalline
regions align
onset of
necking
Initial
Near Failure
semi-
crystalline
case
aligned,
cross-
linked
case
networked
case
amorphous
regions
elongate
Stress-strain curves adapted from Fig. 15.1, Callister 7e. Inset figures along plastic response curve adapted from Figs. 15.12 &
15.13, Callister 7e. (Figs. 15.12 & 15.13 are from J.M. Schultz, Polymer Materials Science, Prentice-Hall, Inc., 1974, pp. 500-501.)

Predeformation by Drawing
• Drawing…(ex: monofilament fishline)
-- stretches the polymer prior to use
-- aligns chains in the stretching direction
• Results of drawing:
-- increases the elastic modulus (E) in the
stretching direction
-- increases the tensile strength (TS) in the
stretching direction
-- decreases ductility (%EL)
• Annealing after drawing ...
-- decreases alignment
-- reverses effects of drawing.
• Comparable to cold working in metals (change of defects,
metal becomes more resistant to further deformation)!
Adapted from Fig. 15.13, Callister
7e. (Fig. 15.13 is from J.M.
Schultz, Polymer Materials
Science, Prentice-Hall, Inc.,
1974, pp. 500-501.)

Viscoelastic properties in polymers
A stress σ0 is applied at time t=0
and held constant. The strain (t)
is followed over time. The creep
compliance J(t) is given by:
(t) = σ0 J(t)
A strain 0 is applied at t=0 and held
constant. The stress σ(t) is followed
over time. The stress relaxation
modulus G(t) is given by:
σ(t) = 0G(t)

The complex modulus G*
If a sinusoidal strain is applied: (t) = 0cos(ωt)
the resulting stress is given by:
σ(t) = 0 [G’(ω) cos(ωt) – G’’(ω) sin(ωt)]
The complex modulus, G*= G’(ω) + iG’’(ω) is
given by a Fourier transform of G(t).
G’ gives the elastic response, G’’ the viscous
response

Viscoelastic Creep
• Many polymers susceptible to time-dependent deformation under
constant load – viscoelastic creep.
• Creep may be significant even at room temperature and under
moderately low stresses (below yield strength).
• Results of creep tests are described by time dependent creep modulus:
• Amount of creep decreases as
crystallinity increases.
Crystals act like crosslinks

Viscoelastic Creep
Increasing creep (strain)
with higher applied load

Fracture of Polymers
• Fracture strengths of polymers are low compared to metals and ceramics.
• Brittle fracture occurs in thermosetting polymers. Fracture is initiated at stress
concentrators (scratches, notches, etc). Covalent bonds are severed during fracture.
• In thermoplastic polymers, both ductile and brittle fracture are possible. Brittle
fracture is favored at lower temperatures, higher strain rates, and at stress
concentrators (sharp notches).
• Brittle to ductile transition often occurs with increasing temperature.

Crazing During Fracture of Thermoplastic Polymers
• Fracture of glassy thermoplastic polymers often proceeds through crazing.
Crazing occurs when localized regions yield, forming an interconnected array of
microvoids. Fibrillar bridges of oriented molecular chains form between voids.
• At high enough tensile loads, these bridges elongate and break, enabling crack
propagation.
• Crazing absorbs fracture energy and increases fracture toughness.
fibrillar bridges microvoids crack
alligned chains

Deformation and Failure in Glassy Polymers
Jörg Rottler and Mark O. Robbins, Johns Hopkins University

Craze Formation and Fracture in Glassy Polymers
Courtesy of E. Kramer et al., UCSB
constant stress S
d
dense polymer
craze
Experiment: Simulation:
Experimental
craze growth
parameters:
• extension ratio
l= ri/rf  2-6
• drawing stress
S  40-70MPa
• fibril diameter
D  5-30 nm
• craze width
d  3-20mm

cm crack  mm craze  10nm fibril  nm polymer
time
z
broken bonds are
marker by red
Chains that
carry maximum
load indicated
by blue color

 80nm
L3/L
N=512
N=256
Stress-strain curves
II. Growth
III. Failure
• Growth (fibril drawing) in II at
constant stress S
• I and II independent of N,
not so III
• Two phases coexist at
constant normal stress S

Plastic Deformation of Semicrystalline Polymers
Plastic deformation is defined by the interaction between crystalline and
amorphous regions and is partially reversible.
Stages of plastic deformation:
1. elongation of
amorphous tie chains
2. tilting of lamellar
crystallites towards
the tensile axis
3. separation of
crystalline
block segments
4. stretching
of crystallites
and amorphous
regions along
tensile axis

Plastic Deformation of Semicrystalline Polymers
Different from ductile metals where the deformation is confined in the initial neck region.
The macroscopic deformation involves necking. Neck gets stronger
since the deformation aligns the chains and increases local strength in the
neck region (up to 2-5 times) ⇒ neck is expanding along the specimen.

Factors that Influence Mechanical Properties
Temperature and strain rate (already discussed)
Chain entanglement, strong intermolecular bonding
(van der Waals, cross-links) increase strength
Drawing, analog of work hardening in metals, corresponds to the neck
extension. Is used in production of fibers and films. Molecular chains become
highly oriented ⇒ properties of drawn material are anisotropic (perpendicular
to the chain alignment direction strength is reduced)
Heat treatment - changes in crystallite size and order
• undrawn material: Increasing annealing temperature leads to
• increase in elastic modulus
• increase in yield/tensile strength
• decrease in ductility
Note that these changes are opposite from metals
• drawn material: opposite changes (due to recrystallization and loss of chain
orientation)

Equilibrium Toughness (long deformation times)
• The total area under the true stress-strain curve which measures the
energy absorbed by the specimen in the process of breaking.
Toughness  dToughness is not Strength:
 Tough: High elongation, low modulus.
 High MW
 Low Intermolecular strength
 Rubber, slight cross linking
 Brittle: Low elongation, high modulus
 Crystalline
 High degree of Xlinked rigid
 High Intermolecular strength
Strong Tough
To be tough, a material should withstand both high
stresses and high strains. Strength indicates how
much force the material can support, while toughness
indicates how much energy a material can absorb
before rupturing. Brittle materials (like ceramics) that
are strong but with limited ductility are not tough.

Impact Toughness or Impact Strength
Impact toughness is the energy adsorbed by material upon sudden impact.
Tough: high elongation and low modulus; Brittle: low elongation and high modulus
Charpy/Izon impact toughness tests
mgh2

HARDNESS
• Resistance to permanently indenting the surface.
• Large hardness means:
--resistance to plastic deformation or cracking in
compression.
--better wear properties.
Adapted from Fig. 6.18, Callister 6e. (Fig. 6.18 is adapted from G.F. Kinney, Engineering Properties
and Applications of Plastics, p. 202, John Wiley and Sons, 1957.)

Factors that Influence Mechanical Properties
Tensile strength increases with molecular weight – effect of entanglement
Higher degree of crystallinity – stronger secondary bonding - stronger and
more brittle material
polyethylene

Elastomers
Elastomers can be deformed to very large strains and then spring back elastically to the
original length, a behavior first observed in natural rubber. To be elastomeric, the polymer
needs to meet several criteria:
• Resistance to crystallization (elastomers are amorphous).
• Relatively free chain rotations (unstressed elastomers have coiled/twisted structure –
uncoil during deformation).
• Certain degree of cross-linking (achieved by vulcanization) that increases resistance to
plastic deformation.
• Temperature is above the glass transition temperature (below Tg elastomer becomes
brittle).

Elastomers: Vulcanization
Because they are cross-linked, elastomeric materials are thermosetting polymers
Elastic modulus, tensile strength, oxidation resistance increased by vulcanization –
magnitude of E is proportional to number of cross-links. Too many cross-links
reduces extensibility.
Crosslinked

Rubber Elasticity
A rubber (or elastomer) can be created by linking together linear
polymer molecules into a 3-D network. n is the number of
strands per unit volume.
To observe “stretchiness”, the temperature should be > Tg for
the polymer.
Chemical bonds between polymer molecules are called
“crosslinks”. Sulphur can crosslink natural rubber.

strand

Elasticity of a Single Ideal Chain
For crystalline solids the
elastic response appears,
because external stress
changes the equilibrium
interatomic distances and
increases the internal
energy of the crystal
(energetic elasticity).
f

lD
Since the energy of ideal polymer chain is
equal to zero, the elastic response appears by
purely entropic reasons (entropic elasticity).
Due to the stretching the chain adopts the less
probable conformation its entropy
decreases.

R

f

R
Ll
kT
R
F
f


 3




L = total unfolded length = l N

Elasticity of a Single Ideal Chain
R

f

R
Ll
kT
R
F
f


 3




L = total unfolded length = l N
• The chain is elongated in the direction
of and (kind of a Hooke law).
• “Elastic modulus”
f

Rf


:
3
Ll
kT
1) is proportional to , i.e. very small
for large values of L. Long polymer chains
are very susceptible to external actions.
2) is proportional to kT which is the
indication to entropic nature of elasticity.
L1

Affine Deformation
With an affine deformation, the macroscopic change in dimension
is mirrored at the molecular level.
We define an extension ratio, l, as the dimension after a
deformation divided by the initial dimension:
o

=l
oo l
l
==


l

o
Bulk:
l
Strand:
lo

Transformation with Affine Deformation
y
x
z
x
z
y yy l
zzl
xxl
z
y
x
R2 = x2+y2+z2
z
y
x
Bulk:
Ro
Single
Strand
Ro = xo+ yo+ zo
R
R = lxxo + lyyo + lzzo
If non-compressible (volume conserved): lxlylz =1

Force for Rubber Deformation
At the macro-scale, if the initial length is Lo, then l = L/Lo.
)+)((+~ 3
2
2
2
L
L
L
LnkT
F o
o
bulkD
Substituting in
L/Lo =  + 1:
)
)+(
+)+((+~ 3
1
2
1
2
2


nkT
FbulkD
Tensile stress T = Y. The strain, , for a 1-D tensile deformation is
1===
oo
o
o L
L
L
LL
L
LD

Realising that DFbulk is an energy of deformation (per unit volume),
then dF/dT is the force, F (per unit area, A) for the deformation,
i.e. the tensile stress, T.
]
)1(
2
)1(2[
2 2





-
nkT
d
dF
T
A
F
A

Young’s and Shear Modulus for Rubber








 22
1
]
)1(
1
)1[(
l
l

 nkTnkTT
In the limit of small strain, T  3nkT, and the Young’s modulus is
thus Y = 3nkT.
The Young’s modulus can be related to the shear modulus, G, by a
factor of 3 to find a very simple result: G = nkT
This result tells us something quite fundamental. The elasticity of a
rubber does not depend on the chemical make-up of the polymer nor
on how it is crosslinked.
G does depend on the crosslink density. To make a higher
modulus, more crosslinks should be added so that the lengths of
the segments become shorter.
This is an equation of state, relating together F, L and T.
oL
LD

l = L/Lo

Experiments on Rubber Elasticity
]
1
[ 2
l
l -nkTT 
Treloar, Physics of Rubber
Elasticity (1975)
Rubbers are elastic over a large range of l!
Strain hardening region:
Chain segments are fully
stretched!
l = L/Lo
- very good agreement
- theory slightly over-
estimates stress at a given
strain (chain entanglements)
()()
52.1
2.14.0


l
l

Alternative Equation for a Rubber’s G

We have shown that G = nkT, where n
is the number of strands per unit
volume.
xM
RTr
=
x
A
M
N
n
r
=
For a rubber with a known density, r, in
which the average molecular mass of a
strand is Mx (m.m. between crosslinks),
we can write:
)(
)#)((
=
#
mole
g
mole
strands
m
g
m
strands 3
3
Looking at the units makes this
equation easier to understand:
kT
M
N
nkTG
x
Ar
==Substituting for n:
strand

Polymer Additives
Improve mechanical properties, processability,
durability, etc.
• Fillers
– Added to improve tensile strength & abrasion
resistance, toughness & decrease cost
– ex: carbon black, silica gel, wood flour, glass,
limestone, talc, etc. Size: 10nm-macroscopic
• Plasticizers (liquids, low vapor pressure, low Mw)
– Added to reduce the glass transition
temperature Tg
– commonly added to PVC - otherwise it is brittle

Polymer Additives
• Stabilizers (counteract deterioration, mechanical integrity)
– Antioxidants (consume O2 before it reaches polymer or
block reaction)
– UV protectants (thin adsorbent layer: sunscreen;
material that react with bonds broken by UV)
• Lubricants
– Added to allow easier processing
– “slides” through dies easier – ex: Na stearate
• Colorants
– Dyes (dissolved in polymer) or pigments (separate phase)
• Flame Retardants
– Cl/F & B

Summary
Reading: Chapter 4 of Plastics: Materials and Processing by A. Brent Strong
• Mechanical properties of solids (forces, elastic behavior)
• Mechanical properties of liquids – viscous flows (Newtonian non-
Newtonian regimes, viscosity measurements)
• Viscoelastic materials (definitions, time dependence, short-range, long-
range interactions)
• Plastic stress-strain behavior definitions, mechanical models
• Creep, toughness, impact strength, hardness
• Reinforcements, fillers, toughness modifiers

Lecture: Mechanical Properties: Macro Viewpoint

More Related Content

What's hot (20)

Similar to Lecture: Mechanical Properties: Macro Viewpoint (20)

More from Nikolai Priezjev (20)

Recently uploaded (20)

Lecture: Mechanical Properties: Macro Viewpoint