an internal damping in epoxy composite...
TRANSCRIPT
An internal damping in epoxy composite systems
D. Kroisová
Technical University of Liberec, Department of Material Science,
Studentská 2, 461 17, Liberec, Czech Republic
email: [email protected]
Abstract This work is focused on an internal damping in epoxy composite materials. Composite systems designed
for experiments were created by two-component epoxy resin and selected types of fillers (lead particles
and chippings, alloy hollow tubes, ferrous-ferric oxide particles, titanium dioxide particles, cork particles,
carbon chopped fibres) differ in their composition, particle size and shape and the weight fraction in the
polymer matrix. The damping tests of casted and cured epoxy composite systems were performed at a
temperature of approximately 22oC, an atmospheric pressure and a low frequency at a range of 50 Hz to
100 Hz as a common condition of a dynamic stress of structures. The photo-electric equipment was used
to measure the deflection of samples the lost coefficient tan δ was calculated by the common method. A
scanning electron microscopy was used to observe filler shape, size and surface as well as fracture
surfaces of composites and the evaluation of their interfaces.
1 Introduction
An internal damping of composite materials is a very important parameter related to the dynamic
behaviour of materials and can be used as a source of interesting knowledge about their structure, state and
behaviour. A lot of composites are built up from polymer materials as a matrix and a different type of
reinforcement. The viscoelasticity of polymers is the main reason of their using as materials for vibration
damping. The damping mechanisms of composite systems include not only behaviour of viscoelastic
polymer but intrinsic damping of fillers, the boundary sliding of fillers, the interfacial sliding between
matrix and fillers or the damage of composite systems too [1, 2, 3]. The particle type, the size, the shape,
the surface and the volume fraction of filler can contribute to damping capacity of composite systems.
Material parameters as a hardness or as a stiffness can influence an internal damping of systems too. In
addition, the testing conditions including the temperature, the frequency and the oscillation amplitude can
affect the damping behaviour of composite systems as well [4]. The aim of this work is to study the effect
of selected types of fillers and their weight fraction in epoxy matrix composite samples during common
working conditions.
2 Experimental
2.1 Materials
Two-component epoxy resin (ChS-Epoxy 371, diethylentrimine hardener P11 - Spolek pro chemickou a
hutní výrobu, a. s. Czech Republic) was used as the matrix having a good adhesion to many substrates,
chemical, moisture and heat resistance and, therefore having wide application. Lead particles, lead
chippings, Pb-Sn hollow tubes (Spolek pro chemickou a hutní výrobu, a. s. Czech Republic), ferrous-ferric
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oxide particles (Sigma-Aldrich, spol. s r. o., Czech Republic ), cork particles (different particle size
fractions were prepared by grinding and sieving of common cork compact material), titanium dioxide
particles (Precheza, a. s. Přerov, Czech Republic), carbon fibres (Havel Composites CZ s. r. o., Czech
Republic) were used as fillers of epoxy composite systems. Their basic parameters are presented in table
1.
Designation of Fillers Components Specific Gravity
[g/cm3]
Shape and Size
of Fillers
[μm]
Lead spherical
particles 99.9% Pb
11.3
Particles
Diameter of particles
100 μm
Lead chippings 99.9% Pb
11.3
Chippings
Diameter of chippings
1 – 1.5 mm
Length of chippings
3 – 7 mm
Pb-Sn hollow tubes 60% Pb
40% Sn 8.9
Tubes
Diameter of tubes
500 – 600 μm
Length of tubes
5 – 6 mm
Tubes wall thickness
50 μm
Cork tiny particles
45% suberin
27% lignin
12% cellulose
0.25 – 0.5
Particles
Diameter of particles
20 – 50 μm
Cork particles
45% suberin
27% lignin
12% cellulose
0.25 – 0.5
Particles
Diameter of particles
300 – 500 μm
Ferrous-ferric oxide
particles
99.9% Fe3O4
4.9 – 5.1
Aggregates from spherical particles
Diameter of aggregates
20 – 100 μm
Diameter of particles
< 1 μm
Ferrous-ferric oxide
particles in own
polymer phase
99.9% Fe3O4 4.9 – 5.1
Aggregates from spherical particles
Diameter of aggregates
10 – 20 μm
Diameter of particles
< 1 μm
Titanium dioxide
particles
92% TiO2
4% Al2O3
3% SiO2
1% ZrO2
4.2
Aggregates from spherical particles
Diameter of aggregates
20 – 100 μm
Diameter of particles
< 1 μm
Carbon fibres 99.9% C 1.6
Fibres
Diameter of fibres 8 μm
Length of chopped fibres
2 – 5 mm
Table 1: Basic parameters of used fillers
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2.2 Composite materials preparation
The desired amount (weight fraction phr – part per hundred of resin – g per 100 g epoxy resin) of all types
of filler was added to fluid epoxy resin and mixed together. The mixtures were cured in a three-part
aluminium mould at a temperature 22oC for 24 hours under pressure 0.8 MPa to get homogeneous
materials. To standardize the samples, they were tested after 21 days because of slow post-curing of the
epoxy resin at laboratory temperature - figure 1.
Figure 1: The curve of tan δ dependence on post-curing time of pure epoxy resin
2.3 Characterization
A damping capacity of epoxy composite samples was determined by the photoelectric equipment at a
laboratory temperature (22 ± 2)oC and a low frequency at a range of 50 Hz to 100 Hz. These parameters
were selected as common conditions of dynamic stress of structures although a lot of scientists are
interested in a damping capacity at the glass transition temperature of viscoelastic polymer matrix. The
composite samples (length 100 mm, width 10 mm, thickness 2 mm) were used as cantilever beams. The
standard initial deflection of the cantilever beam from the equilibrium state was specified by the pinpoint
of the measuring apparatus. The photoelectric equipment was used to measure the damped oscillation of
samples. The numerical values of these oscillations were read from a memory oscilloscope. The damping
ratio was found using the logarithmic decrement method. The loss factor tan δ was determined from the
vibration curve decay.
Scanning electron microscope (VEGA/TESCAN, Czech Republic) was used at an accelerating voltage of
30 kV to evaluate the character of sample interfacial surface and the homogeneity of the systems. The
fracture surfaces were coated with a thin layer of gold – palladium alloy.
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3 Results and discussion
3.1 The effect of material type and volume fraction on internal damping
The addition of fillers to viscoelastic polymer matrix can make a contribution to increase the internal
damping of composites. The contribution to the internal damping can come from the intrinsic damping of
fillers, the boundary sliding of fillers, the interfacial sliding between matrix and fillers or from the damage
of composite systems [4, 5]. Part of vibration energy is dissipated due to shear forces that are formed at
the interfaces of loaded system if the Young modulus of used compound is different [6]. Another part of
the vibration energy is dissipated due to viscoelastic behaviour of polymer matrix [7].
As we can see from figure 2, the highest contribution to the internal damping comes from the Pb-Sn
hollow tubes. The part of the vibration energy can be dissipated by the deformation of alloy tubes due to
their low stiffness. An adhesion between tubes and an epoxy resin matrix is low – figure 3c). The
difference in the contribution to the internal damping between lead chippings and lead particles can be
explained by the shape of fillers. Lead chippings with low Young modulus can be deformed during the
loading whilst spherical particles cannot. An adhesion in these both examples is low too – figure 3a), 3b).
Figure 2: The curves of tan δ fraction dependence of the selected particles
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a) b) c)
Figure 3: The fracture surfaces of the selected composite systems
a) lead particles – epoxy resin matrix
b) lead chippings – epoxy resin matrix
c) alloy (Pb-Sn) hollow tubes – epoxy resin matrix
As we can see from figure 4, higher contribution to the internal damping comes from the bigger cork
particles. The part of the vibration energy can be dissipated by the deformation of cork particles consisting
from hollow cells. An adhesion between cork particles and an epoxy resin matrix is good – figure 5d). The
difference in the contribution to the internal damping between small and big cork particles can be
explained by the different size of the filler – figure 5a), b), c).
Figure 4: The curves of tan δ fraction dependence of the cork particles
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a) b)
c) d)
Figure 5: The shape and the size of two different size cork particles
a) tiny cork particles
b) bigger cork particles
c) bigger cork particles – hollow cells
d) cork particles in epoxy resin matrix
As we can see from figure 6, the higher contribution to the internal damping comes from ferrous-ferric
oxide particles deposited in the own polymer phase. The part of the vibration energy can be dissipated by
the movement of the tiny particles in the own polymer phase – figure 7a). Ferrous-ferric oxide particles
without polymer phase – figure 7b) do not contribute to the internal damping. An adhesion between both
types of fillers and the epoxy resin matrix is good – figure 7c), d). The difference in the contribution to the
internal damping between two types of ferrous-ferric oxide particles can be explained by the presence of
the secondary viscoelastic polymer phase and the possibility of tiny ferrous-ferric oxide particles to move
in this polymer phase during loading.
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Figure 6: The curves of tan δ fraction dependence of two different ferrous-ferric oxide particles
a) b)
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c) d)
Figure 7: The character of two different ferrous-ferric oxide particles
a) ferrous-ferric oxide particles in the own polymer phase
b) ferrous-ferric oxide particles without own polymer phase
c) the fracture surface of ferrous-ferric oxide particles in the own polymer phase – epoxy resin
matrix
d) the fracture surface of ferrous-ferric oxide particles without polymer phase – epoxy resin matrix
As we can see from figure 8, particles of titanium dioxide do not contribute to the internal damping of
composite system. An adhesion between this type of filler and the epoxy resin matrix is good – figure 9b).
There is no intrinsic damping of filler particles and no interfacial sliding between matrix and particles of
filler.
Figure 8: The curves of tan δ fraction dependence of titanium dioxide particles
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a) b)
Figure 9: Titanium dioxide particles
a) aggregates of titanium dioxide particles
b) the fracture surface of titanium dioxide particles – epoxy resin matrix
As we can see from figure 10, the chopped carbon fibres do not contribute to the internal damping of this
composite system. An adhesion between used carbon fibres and the epoxy resin matrix is quite good –
figure 11b). The energy cannot be dissipated by the deformation of the high-modulus carbon fibres.
Figure 10: The curves of tan δ fraction dependence of chopped carbon fibres
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a) b)
Figure 11: Carbon fibres
a) a surface of carbon fibres
b) the fracture surface of chopped carbon fibres - epoxy resin matrix
4 Conclusion
The fillers type, the fraction of the filler particles in the matrix, their size and shape and basic mechanical
parameters can influence the internal damping of composite systems.
Low modulus particles of filler with a nonspherical shape have an influence on the internal damping as a
result of their deformation during the vibration of the matrix.
Spherical and high modulus particles and fibres practically do not deform themselves and do not increase
the internal damping of composite systems.
The samples were tested at the low frequency at a range of 50 Hz to 100 Hz and the temperature 22oC.
Data dispersion is to 2 %.
Acknowledgements
The author gratefully acknowledges MSM number 4674788501, Czech Republic for the financial support.
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