This document provides an introduction to elastic-plastic fracture mechanics (EPFM). It discusses the key concepts of EPFM including crack tip opening displacement (CTOD) and the J-integral. CTOD and J-integral are used to characterize fracture toughness in large-scale plastic deformation, unlike linear elastic fracture mechanics (LEFM) which is only valid for small plastic zones. Measurement methods and applications of CTOD and J-integral are also covered along with background on plasticity theory and LEFM concepts.

1. Elastic-Plastic Fracture Mechanics
Introduction
•When does one need to use LEFM and EPFM?
•What is the concept of small-scale and large-scale yielding?
Contents of this Chapter
•The basics of the two criteria used in EPFM: COD (CTOD), and J-Integral (with H-R-R)
•Concept of K- and J-dominated regions, plastic zones
•Measurement methods of COD and J-integral
•Effect of Geometry
Background Knowledge
•Theory of Plasticity (Yield criteria, Hardening rules)
•Concept of K, G and K-dominated regions
•Plastic zone size due to Irwin and Dugdal

2. LEFM and EPFM
LEFM
•In LEFM, the crack tip stress and displacement field can be uniquely characterized by K, the
stress intensity factor. It is neither the magnitude of stress or strain, but a unique parameter that
describes the effect of loading at the crack tip region and the resistance of the material. K filed is
valid for a small region around the crack tip. It depends on both the values of stress and crack size.
We noted that when a far field stress acts on an edge crack of width “a” then
for mode I, plane strain case
σ
σ
τ
π
θ
θ θ
θ θ
θ θ
xx
yy
xy
IK
r
R
S|
T|
U
V|
W|
=
−
+
L
N
MMMMMMM
O
Q
PPPPPPP
2 2
1
2
3
2
1
2
3
2
2
3
2
cos
sin( ) sin( )
sin( ) sin( )
sin( ) sin( )
σ σ ν σ σzz zz xx yy= = +0 for plane stress; for plane strain( )
u
u
K r
k
k
x
y
I
RST
UVW
=
− +
+ −
L
N
MMMM
O
Q
PPPP
2
2
1 2
2
2
1 2
2
2
2µ π
θ θ
θ θ2
cos ( sin ( ))
sin ( cos ( ))

3. LEFM concepts are valid if the plastic zone is much smaller than the singularity zones.
Irwin estimates
Dugdale strip yield model:
r
K
p
I
ys
=
1
2
2
π σ
( )
r
K
p
I
ys
=
1
8
2
( )
σ
ASTM: a,B, W-a 2.5 , i.e. of specimen dimension.≥ ( )
KI
ysσ
2
rp ≤
1
50
LEFM cont.
Singularity dominated region
σ
σ
τ
π
xx
yy
xy
IK
r
R
S|
T|
U
V|
W|
=
L
N
MMM
O
Q
PPP2
1
1
0
For =0θ
For =
2
all ijθ
θ
σ, =0

4. EPFM
•In EPFM, the crack tip undergoes significant plasticity as seen in the following diagram.
s h a r p t i p
Ideal elastic brittle behavior
cleavage fracture
P: Applied load
P : Yield loady Displacement, u
Loadratio,P/Py
1.0
Fracture
Blunt tip
Limited plasticity at crack
tip, still cleavage fracture
Displacement, u
Loadratio,P/Py
1.0
Fracture

5. Blunt tip
Void formation & coalescence
failure due to fibrous tearing
Displacement, u
Loadratio,P/Py
1.0
Fracture
large scale
blunting
Large scale plasticity
fibrous rapture/ductile
failure Displacement, u
Loadratio,P/Py
1.0 Fracture

6. EPFM cont.
•EPFM applies to elastoc-rate-independent materials, generally in the large-scale plastic
deformation.
• Two parameters are generally used:
(a)Crack opening displacement (COD) or crack tip opening displacement (CTOD).
(b) J-integral.
•Both these parameters give geometry independent measure of fracture toughness.
δSharp crack
Blunting crack
y
x
Γ
ds

7. EPFM cont.
•Wells discovered that Kic measurements in structural steels required very large thicknesses for
LEFM condition.
--- Crack face moved away prior to fracture.
--- Plastic deformation blunted the sharp crack.
δ
Sharp crack
Blunting crack
• Irwin showed that crack tip plasticity makes the crack behave as if it were longer, say from size a to a + rp
-----plane stress
From Table 2.2,
Set ,
r
K
p
I
ys
=
1
2
2
πσ( )
u
K r
ky
I
= + −
2 2 2
1 2
2
2
µ π
θ θ
sin( )[ cos ( )]
θ π= u
k
K
r
y I
y
=
+1
2 2µ π
a ry+
θ π=
δ
πσ
= =2
4 2
2
u
K
E
y
I
ys
Note:
since
k E=
−
+
= +
3
1
2 1
ν
ν
µ νand ( )
δ
π σ
= =CTOD
4 G
ys
G
K
E
I
=
2

8. CTOD and strain-energy release rate
• Equation relates CTOD ( ) to G for small-scale yielding. Wells proved that
Can valid even for large scale yielding, and is later shown to be related to J.
• can also be analyzed using Dugdales strip yield model. If “ ” is the opening at the end of the strip.
δ
π σ
= =CTOD
4 G
ys
δ δ
δ δ
δ
σ ys
Consider an infinite plate with a image crack subject to a
Expanding in an infinite series,
σ σ∞ =
δ
σ
π
π σ
σ
= = ⋅2
8
u
a
E
y
ys
ys
lin sec(
2
)
δ
σ
π
π σ
σ
π σ
σ
= ⋅ + ⋅ +
8 1
12
2 4ys
ys ys
a
E
[
1
2
(
2
(
2
) ) ...]
If , and can be given as:
In general,
δ
σ
π σ
σ
= + ⋅
K
E
I
ys ys
2
2
[1
1
6
(
2
) ]
σ
σ
σ σ δ
σ σys
ys
ysE
G
≈ << =0 ( then =
KI
2
ys
), δ
δ
σ
=
G
m ys
, m = 1.0 for plane stress; m = 2.0 for plane strain

9. Alternative definition of CTOD
δSharp crack
Blunting crack
δBlunting crack
Displacement at the original crack tip Displacement at 900 line intersection, suggested by Rice
CTOD measurement using three-point bend specimen
W
P
a
rp(W-a)
z
Vp
δ p
'
'
'δpl
p p
p
r W a V
r W a a z
=
−
− + +
( )
( )
displacement
expandingδ

10. Elastic-plastic analysis of three-point bend specimen
δ δ δ
σ
= + = +
−
− + +
el pl
I
ys
p p
p
K
m E
r W a V
r W a a z
2
( )
( )
Where is rotational factor, which equates 0.44 for SENT specimen.δ pl
• Specified by ASTM E1290-89
--- can be done by both compact tension, and SENT specimen
• Cross section can be rectangular or W=2B; square W=B
KI is given by
δ
ν
σel
I
ys
K
E
=
−2 2
1
2
( )
K
P
B W
f
a
W
I = ⋅ ( )
δpl
p p
p
r W a V
r W a a z
=
−
− + +
( )
( )
load
Mouth opening
υ p υe
V,P

11. CTOD analysis using ASTM standards
Figure (a). Fracture mechanism is purely cleavage, and critical CTOD <0.2mm, stable crack growth,
(lower transition).
Figure (b). --- CTOD corresponding to initiation of stable crack growth.
--- Stable crack growth prior to fracture.(upper transition of fracture steels).
Figure (c) and then ---CTOD at the maximum load plateau (case of raising R-curve).
δ c
δ i
δ i δ m
δ u
load
Mouth opening
Pc
fracture
(a) (b) (c)
Pi
Pu Pm
fracture
Pi

12. More on CTOD
The derivative is based on Dugdale’s strip yield model. For
Strain hardening materials, based on HRR singular field.
By setting =0 and n the strain hardening index based on
*Definition of COD is arbitrary since
A function as the tip is approached
*Based on another definition, COD is the distance between upper
and lower crack faces between two 45o
lines from the tip. With this
Definition
2
orI
COD
y y
K J
E
δ
σ σ
= =
( )
11
1
,
n
n
n
i y i
y y n
J
u r u n
I
αε θ
ασ ε
+
+
 
=  ÷
 
1
3
2
n
y ije
y y y
ε σσα
ε σ σ
−
 
=  ÷
 
( ) ( ),0 ,0y yu x u xδ + −
= −
( )
1
1nx +−
COD n
y
J
dδ
σ
=

13. Where ranging from 0.3 to 0.8 as n is varied from
3 to 13 (Shih, 1981)
*Condition of quasi-static fracture can be stated as the
Reaches a critical value . The major advantage is that this
provides the missing length scale in relating microscopic failure
processes to macroscopic fracture toughness.
*In fatigue loading, continues to vary with load and is a
function of:
(a) Load variation
(b) Roughness of fracture surface (mechanisms related)
(c) Corrosion
(d) Failure of nearby zones altering the local stiffness response
( ), ,n n yd d nα ε=
tipδ
CODδ
2
2
I
y
k
δ
σ ε
∆
∆ =

14. 3.2 J-contour Integral
• By idealizing elastic-plastic deformation as non-linear elastic, Rice proposed J-integral, for regions
beyond LEFM.
• In loading path elastic-plastic can be modeled as non-linear elastic but not in unloading part.
• Also J-integral uses deformation plasticity. It states that the stress state can be determined knowing
the initial and final configuration. The plastic strain is loading-path independent. True in proportional
load, i.e.
• under the above conditions, J-integral characterizes the crack tip stress and crack tip strain and
energy release rate uniquely.
• J-integral is numerically equivalent to G for linear elastic material. It is a path-independent integral.
• When the above conditions are not satisfied, J becomes path dependent and does not relates to any
physical quantities
d d d d d d
k
σ
σ
σ
σ
σ
σ
σ
σ
σ
σ
σ
σ
1
1
2
2
3
3
4
4
5
5
6
6
= = = = = =

15. 3.2 J-contour Integral, cont.
y
x
Γ
ds
Consider an arbitrary path ( ) around the crack tip. J-integral is defined asΓ
J wdy T
u
x
ds w di
i
i
ij ij
ij
= −
∂
∂
= zz( ), σ ε
ε
0
Γ
It can be shown that J is path independent and represents energy release rate for a material where
is a monotonically increasing with
σ ij
εij
Proof: Consider a closed contour:
Using divergence theorem:
J wdy T
u
x
dsi
i
i
*
( )
*
= −
∂
∂zΓ
J
w
x x
u
x
dxdy
i
ij
i
A
*
( )
*
=
∂
∂
−
∂
∂
∂
∂z σ
where w is strain energy density, Ti is component of traction vector normal to contour.
A*
Γ*

16. *
*
( )i
ij
j
A
uw
J dxdy
x x x
σ
 ∂∂ ∂
= − 
∂ ∂ ∂  
∫
Evaluate
∂
∂
=
∂
∂
⋅
∂
∂
=
∂
∂
w
x
w
x xij
ij
ij
ij
ε
ε
σ
ε
Note is only valid if such a potential function exists
Again,
σ
ε
ij
ij
w
=
∂
∂
∂
∂
=
∂
∂
+
∂
∂
=
∂
∂
∂
∂
+
∂
∂
∂
∂
w
x x
u
x
u
x
u
x x
u
x
ij i j i j
ij
j
i
i
j
1
2
1
2
σ
σ
[ ( ) ( )]
[ ( ) ( )]
, ,
Since σ σ
σ
ij ji
ij
j
i
x
u
x
=
=
∂
∂
∂
∂
( )
Recall
∂
∂
=
∂
∂
∂
∂
=
∂
∂
∂
∂
σ
σ σ
ij
j
j
i
j
ij
i
x
x
u
x x
u
x
0 (equilibrium) leads to
ij ( ) ( )
Evaluation of J Integral ---1
w
(equilibrium) leads to
,j i

17. Hence, Thus for any closed contourJ*
.= 0 J*
.= 0
Now consider
Γ1
Γ2
Γ3
Γ4
1 2 3 4
0J J J J J= + + + =
Recall J wdy
w
x
dsi
*
( )= −
∂
∂z τ
Γ
On crack face, (no traction and y-displacement), thus
, leaving behind
Thus any counter-clockwise path around the crack tip will yield
J; J is path independent.
τ i dy= =0 0,
J J3 4 0= = J J1 2= −
Evaluation of J Integral ---2
1 2 3 4
ti
ti

18. Γ'
a
y
x
2D body bounded by Γ'
In the absence of body force, potential energyΠ
Π
Γ
= −z zwdA u ds
A
i i
' ''
τ
Suppose the crack has a vertical extension, then
d
da
dw
da
dA
du
da
ds
A
i
iΠ
Γ
= −z z' '
τ (1)
Note the integration is now over Γ'
Evaluation of J Integral ---3
ti
ti

19. Noting that
d
da a
x
a x a x
x
a
=
∂
∂
+
∂
∂
∂
∂
=
∂
∂
−
∂
∂
∂
∂
= −since 1
d
da
w
a
w
x
dA
w
a
u
x
ds
A
i
iΠ
Γ
=
∂
∂
−
∂
∂
−
∂
∂
−
∂
∂z z( ) ( )
' '
τ (2)
∂
∂
=
∂
∂
∂
∂
=
∂
∂
∂
∂
w
a
w
a x
u
aij
i
ij
j
i
ε
ε
σ ( )
Using principle of virtual work, for equilibrium, then from
eq.(1), we have
d
da
Π
= 0
σ τij
j
A
i
i
i
x
u
a
dA
u
a
ds
∂
∂
∂
∂
=
∂
∂z z( )
' '
Γ
Thus,
d
da
du
dx
ds
dw
dx
dAi
i
A
Π
Γ
= −z zτ
' '
Using divergence theorem and multiplying by -1
− = − = −
∂
∂z zd
da
wn
du
dx
ds wdy
w
x
dsx i
i
i
Π
Γ Γ
( )
' '
τ τ
Evaluation of J Integral ---4
j
titi
ti
ti
ti
⋅⋅

20. Therefore, J is energy release rate , for linear or non-linear
elastic material
d
da
Π
In general
Potential energy; U=strain energy stored; F=work done by
external force and A is the crack area.
Π = − = −
∂Π
∂
U F J
A
and
Π =
a
u
p
Evaluation of J Integral ---5
-dP
*dU dU= − d∆
Displacement
*U P UΠ = − ∆ = = Complementary strain energy = dP∆∫0
p
Load

21. For Load Control
For Displacement Control
The Difference in the two cases is and hence J for
both load Displacement controls are same
*
p
dU
J
da
=
dU
J
da ∆
= −
0 0
0
. .
.
pD
p p
J dp dp
a a
or
p
J pd d
a a
∆
∆ ∆
∂ ∂∆
= ∆ =
∂ ∂
∂ ∂
= − ∆ = − ∆
∂ ∂
∫ ∫
∫ ∫
J=G and is more general description of energy release rate
2
'
IK
J
E
=
Evaluation of J-Integral

22. More on J Dominance
J integral provides a unique measure of the strength of the singular
fields in nonlinear fracture. However there are a few important
Limitations, (Hutchinson, 1993)
(1) Deformation theory of plasticity should be valid with small strain
behavior with monotonic loading
(2) If finite strain effects dominate and microscopic failures occur, then
this region should be much smaller compared to J dominated
region
Again based on the HRR singularity ( )
1
1
,
n
I
ijij y
y y n
J
n
I r
σ σ σ θ
ασ σ
+ 
=  ÷
 
Based on the condition (2), we would
like to evaluate the inner radius ro of J
dominance. Let R be the radius
where the J solutions are satisfied
within 10% of complete solution.
FEM shows that R
o
r
3o CODr δ;

23. •However we need ro should be greater than the forces zone
(e.g. grain size in intergranular fracture, mean spacing of voids)
•Numerical simulations show that HRR singular solutions hold
good for about 20-25% of plastic zone in mode I under SSY
• Hence we need a large crack size (a/w >0.5) . Then finite strain
region is , minimum ligament size for valis JIC is
• For J Controlled growth elastic unloading/non proportional loading
should be well within the region of J dominance
• Note that near tip strain distribution for a growing crack has a
logarithmic singularity which is weaker then 1/r singularity for a
3 CODδ
25 IC
y
J
b
σ
=
and a R
dJ J
da R
≥ ∆ =

24. Williams solution to fracture problem
Williams in 1957 proposed Airy’s stress function
As a solution to the biharmonic equation
For the crack problem the boundary conditions are
Note will have singularity at the crack tip but is single valued
Note that both p and q satisfy Laplace equations such that
( ) ( )R rψ θ θ=
2 2
4 2
2 2 2
1 1
0 where
r r r r
ψ
θ
∂ ∂ ∂
∇ = ∇ = + +
∂ ∂ ∂
0 forrθθ θσ σ θ π= = = ±
ψ
( ) ( )2
, ,r p r q rψ θ θ= +
2 2
0p q∇ = ∇ =

25. Now, for the present problem.
( ) ( )
( )[ ]
( )[ ]
( )[ ]
( ) ( ) ( )[ ]
1
2 2
1
2
1 1
2
2 2
2
1 1
2
1 12
cos sin
cos 2 sin 2
Then
cos cos 2
sin sin 2
Consider only mode I solution with
cos cos 2
1 2 cos cos 2
z
z
r
p A r A r
q B r A r
r A B
r A B
r A B
r A B
r
r
λ λ
λ λ
λ
λ
λ
λ
θθ
θ
λθ λθ
λ θ λ θ
ψ λθ λ θ
λθ λ θ
ψ λθ λ θ
ψ
σ λ λ λθ λ θ
σ
+ +
+
+
+
= +
= + + +
= + +
+ + +
= + +
∂
= = + + + +
∂
∂
= −
∂
( ) ( ) ( )[ ]1 1
1
1 sin 2 sin 2
r
r A Bλ
ψ
θ
λ λ λθ λ λ θ
∂ 
 ÷
∂ 
= + + + +

26. Williams Singularity…3
Applying boundary conditions,
( )
( )
1 1
1 1
A +B cos 0
2 sin 0A B
λπ
λ λ λπ
=
+ + =  
Case (i) cos 0λπ = 2 1
, Z=0,1,2...
2
Z
λ
+
=
1 1B
2
A
λ
λ
= −
+
or,
sin 0λπ = Zλ = 1 1B A= −
Case (ii)
Since the problem is linear, any linear combination of the above two will also be
acceptable.
Thus
Though all values are mathematically fine, from the physics point of view, since
2
with Z= ... 3, 2, 1,0,1,2,3...Z
λ = − − − −
andij ijr rλ λ
σ ε∝ ∝

27. Williams Singularity…4
( )
0
0
21
2
2
1
20
2A 2 1
0
=
ij ij
R
ij ij
r
R
r
U r
rdrd
r drd
λ
π
λ
σ ε
σ ε θ
θ+
= ∝
∫ ∫
∫ ∫;
Since U should be provided for any annular rising behavior and R ,0r
0 ˆas 0, 1 ( 1 makes 0)ijU r λ σ< ∞ → > − = − =
1
1
31 1 Z
2 2 2 2
1
12 3
, needs > 1. Thus
=- ,0, ,1, ,2... with = Z=-1,0,
positive number.
The most dominant singular form
=- and B
r
i
A
Also u r
where
λ
λ λ
λ
+
∝ −
=

28. ( )
( )
( ) ( ) ( )
( ) ( )
3
2
5
2
1 1
2 2
31
1 2 3 2
2
0
1
Now cos cos
+ ...
...
and
where indicates the order of
I
ij ij ij ij
r A
r
r
A r r r
θ θ
σ σ θ−
Φ = +  
Φ
+ Φ
= + Φ + Φ
Φ
%
Williams Singularity…4
( )
( )
0
1
Note the second term in is a non-singular
and non-vanishing term. However, higher order vanish as r 0
with
2
(no sum on x)
2
ij ij
I
II
ij ij ix jx
r
K
A
K
T
r
σ
π
σ σ θ δ δ
π
= Φ
→
=
= +%

29. ( )
( )
( ) ( ) ( )
( ) ( )
3
2
5
2
1 1
2 2
31
1 2 3 2
2
0
1
Now
cos cos
...
...
and
where indicates the order of
I
ij ij ij ij
r A
r
r
A r r r
θ θφ
φ
φ
σ σ θ φ φ
φ
−
= +  
+
+
= + +%
Williams Singularity…5
( )
( )
0
1
Note the second term in is a non-singular
and non-vanishing term. However, higher order vanish as r 0
with
2
(no sum on x)
2
ij ij
I
II
ij ij ix jx
r
K
A
K
T
r
σ
π
σ σ θ δ δ
π
= Φ
→
=
= +%

30. Williams Singularity…6
( ) ( )
( ) ( )
For in-plane stress components,
0
0 02
I I
xx xy xx xyI
I I
yx yy yx yy
TK
r
σ σ σ θ σ θ
σ σ π σ θ σ θ
    
= +          
% %
% %
I
Second-term is generally termed as "T-stress" or
"T-tensor" with
For brittle crack of length 2a in x-z plane
with & applied
K and
xx
yy xx
yy
T
a
σ
σ σ
σ π
∞ ∞
∞
=
=
T= yy xxσ σ∞ ∞
−
x
y
2a
z

31. HRR Singularity…1
0 0 0
Hutchinson, Rice and Rosenbren have evaluated the character of crack tip
in power-law hardening materials.
Suppose the material is represented by Ramberg-Osgood model,
ε σ σ
α
ε σ σ

= +

0
0
0
Reference value of stress=yield strength
, strain at yield
E
dimensionless constant
strain-hardening exponent
n
n
σ
σ
ε
α

 

−
−
−
−
1
Note if elastic strains are negligible, then
ˆ3 3
ˆ;
2 2
n
y y
n
ij eq ij
eq ij
y ij y
ε σ
α
ε σ
ε σ σα
σ σ
ε σ σ
−
 
=   
 
 
= =  
 

32. HRR Singularity…2
( )
( ) ( )
( )
4
0
1 2
0
Then
, , , ,
(similar to Williams expression)s t
s
f r n
C r r
k r
φ φ σ α
φ θ ρ θ
φ σ φ θ
∇ +
= +
= ⋅ ⋅ %
( )
( )
1
1
0 2
0
1
0
2
0
Applying the appropriate boundary conditions
,
,
Integration const
n
ij ij
n
n
n
ij ij
n
n
EJ
n
I r
EJ
n
E I r
I
σ σ σ θ
ασ
σ
ε ε θ
ασ
+
+
 
=  
⋅ 
 
=  
⋅ 
−
%
%
ant
, Dimensionless functions of n andσ ε θ−%%