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326

needed to create new crack surfaces. The calculation applied by Griffith is complicated,

but the same result is obtained by simplification using concept of stress-lines, Fig. 5

/10/.

Figure 4. Griffith’s crack: geometrical

configuration

Figure 5. Simplified model for approximate

calculation of strain energy release rate /10/

Two half-crack lengths

a

and

(a +

δ

a)

are considered under fixed-grip conditions,

exposed to applied stress

σ

. The stress-free regions above and below the crack can be

roughly triangular in shape and extended to a height

π

. Then, for a length

a

, the strain

energy release

U

per unit thickness (

B

= 1) is given in plane stress by

½

×

stress (

σ

)

×

strain (

σ

/

E

)

×

area (

π

a

2

), i.e.

2

1

2

U

a

E

σ

σ

π

= − ⋅ ⋅

(1)

thus, for a length increase

da

, the decrease of the strain energy is

2

dU

a da

E

σ

π

= − ⋅

(2)

In plane strain, the tensile strain is given as

σ

(1 – v

2

)/E

(

v

is Poisson’s ratio) instead

σ

/E

, and the change in energy with crack length,

U/

a

, is:

2

U

a

a E

σ π

= −

(for plane stress)

2

2

1

U (

) a

a

E

σ

ν

π

= −

(for plane strain) (3)

In order to verify the results of Griffith, crack is modelled in an ideal crystalline body

by increased atom distance at the tip under applied remote stress

σ

(Fig. 6), considering

the change in crack-driving force

F

with the crack extension at atomic level /10/.

The strength is taken as a tensile stress

σ

, which must be applied to cause the fracture

across a particular crystallographic plane of cubic lattice with initial atomic spacing

b

o

.

Stress

σ

is simply the sum of the forces,

F

, acting between successive pairs of atoms. To

a first approximation, the value of

F

required to cause fracture corresponds to that

needed to separate an isolated pair of atoms such as AB. For a pair of atoms, such as AB,

CD,...PQ it is possible to draw a curve to represent their energy of interaction as a

function of distance of separation

b

(Fig. 7). The resultant energy,

U

, exhibits a mini-

mum at the equilibrium lattice spacing

b

o

. Some energy must be spent to increase the