Micromechanics- Shear Lag Theory 2 Flashcards
Load balance do a segment of an aligned short fibre composite under longitudinal stress
σ1=ffσbarf+(1-ff)σbarm
Where σ1 is the applied longitudinal stress
σbarf is volume averaged stress in the fibre
σbarm is volume averages stress in the matrix
Can multiply both sides by CSA of composite (A) for force balance
Assumption for strain in the matrix of short fibre composites
Assume the strain in the strip is uniform and equal to that on the composite (ε1)
Means σbarm is about Emε1
Less uniform for long fibre composites
Formula for composite modulus in 1 direction for aligned short fibre composites in databook
E1=ffEf(1-(tanh(ns)/ns)+(1-ff)Em
Where n is dimensionless constant with formula in databook
Ef and Em are stiffness of fibre and matrix
s is fibre aspect ratio L/r
In databook there is η at start but this is 1 in this case (aligned)
Modified shear lag version of formula for composite modulus in 1 direction for aligned short fibre composites not in databook
E1’=ffEf(1-(Ef-E’m(tanh(ns))/Efns)+(1-ff)Em
The difference is the Ef-E’m over Ef stuff
E’m has formula in databook
Takes into account stress transfer across fibre ends
How does composite modulus vary with ff for different aspect ratios (unmodified shear lag theory)?
For carbon fibre in epoxy: start nearly 0, curve up to high modulus when ff=1. Lower aspect ratio means E1 stays lower for longer and more curvy. Higher aspect ratio more linear like long fibre composites.
For SiC in glass: start higher E1 then same trend to higher E1 at ff=1. Same effect of aspect ratio but not as noticeable and each aspect ratio more linear than for C fibre in epoxy (less mismatch in properties between fibres and matrix)
How does composite modulus vary with ff for different aspect ratios (modified shear lag theory)?
Even lower effect of aspect ratio and all lines more linear than for unmodified theory. Still same start and end points
What happens to E1 formula for increasing aspect ratio?
At high aspect ratios fibres are effectively continuous. Equation reverts to simple longitudinal rule of mixtures because
tanh(ns)/ns tends to 0
Formula for minimum aspect ratio for effective stress transfer
This is the aspect ratio which maximises stiffness (where rule of mixtures is observed).
Estimated by s sub RM = 10/n
sRM is about 100 for polymer composites
sRM is about 25 for metal matrix composites
How does sRM vary with fibre volume fraction (still aligned fibres)?
Starts high, curves down with decreasing stiffness, then nearly straight line until curves downwards near end. Highest curve for C fibre in epoxy, lowest for SiC in glass, middle for glass fibre in unsaturated polyester.
How does formula for composite modulus change when short fibres are not aligned?
This is the formula in the databook with η in front. This is the Krenchel factor which is the efficiency of reinforcement.
For randomly oriented short fibres in a 2D plane it is 3/8 (e.g for chopped strand mat).
For randomly oriented short fibres in 3D it is 1/5
How does being randomly aligned in 2D or 3D affect composite modulus vs ff graph?
For every aspect ratio the curve starts at same point but remains lower and finishes at lower value when ff=1. Lowest for random in 3D. Even when fibres effectively continuous the near linear line is just less steep
Where is interfacial shear stress τi the highest?
At the fibre ends
What happens when interfacial shear stress exceeds a critical value τic?
Either get local plasticity in the matrix
Or interfacial sliding between the matrix and fibre
Formula for interfacial shear stress
τi=(n/2)Efε1sinh(nx/r)sech(ns)
In databook
x is distance from centre of fibre so is equal to L at fibre ends
When looking at fibre ends get nL/r which is ns
Formula for critical interfacial shear stress
τic=(n/2)Efε1cTanh(ns)
In databook
ε1c is critical strain
Tanh(ns) comes from simplification of sinh(nL/r)sech(ns)