Conductive mechanism of antistatic poly(ethylene terephthalate)/ZnOw composites
Transcript of Conductive mechanism of antistatic poly(ethylene terephthalate)/ZnOw composites
Conductive Mechanism of AntistaticPoly(ethylene terephthalate)/ZnOw Composites
Ke Chen, Chuanxi Xiong, Liubin Li, Liu Zhou, Youan Lei, Lijie DongSchool of Materials Science and Engineering, Wuhan University of Technology,Wuhan 430070, People’s Republic of China
Antistatic composites of poly(ethylene terephthalate)(PET) and tetrapod-shaped ZnO whisker (ZnOw), thesurface of which was treated with a coupling agent,were prepared by melt-mixing using a twin screw ex-truder. The structure and morphology of the blendswere examined by FTIR and SEM. Antistatic perform-ance and the effect of ZnOw loading levels were inves-tigated. The conductive mechanism of PET/ZnOw com-posites is presented, which can be classified into tun-nel effect, discharging effect at the pinpoint andconductive network. The simple formula of critical vol-ume fraction (vc) for ZnOw forming conductive networkis proposed, based on the actual processing conduc-tion. Comparison of the theory value to the experimen-tal data showed a close agreement. POLYM. COMPOS.,30:226–231, 2009. ª 2008 Society of Plastics Engineers
INTRODUCTION
Poly(ethylene terephthalate) (PET) is widely used in
various fields such as packaging materials, electrical and
electronic parts, and automotive components because of
its good mechanical and thermal properties. PET is inher-
ently an electrical insulator, exhibiting the surface resis-
tivity of 1015–1016 O. The static charge that easily builds
up on such molded parts by contact or rubbing may cause
an electrostatic discharge, which becomes a serious prob-
lem because there may be electrostatic damage to sensi-
tive semiconductor devices and interference with circuit
operation. To solve these problems, a lot of antistatic
materials are often incorporated into the polymer at the
molding process or applied to the surface of the products
in a finishing process to control the resistivity [1].
According to the properties of antistatic materials, they
can be divided into the following categories:
(1) Conductive additives, such as carbon black [2–4],
metal powder [5, 6], or conductive fibers [7, 8], can
be blended with polymer matrix to dissipate the elec-
tronic charge.
(2) The substance whose molecular structure is originally
conductive, such as conducting polymer, can be used
to prepare antistatic materials [9–12].
(3) Antistatic agents, such as nonionic surfactants or
hydrophilic substance, can be added to the surface of
products, or blended into raw materials to form anti-
static composites [13–15].
Because of its excellent properties and lower price,
carbon black is blended into polymer materials to provide
the conductivity of materials. Although carbon black can
serve as a good conductive additive, it will darken the
surface of polymer products, a major defect making color-
ing of polymers more difficult.
Many studies have indicated that polymer composites,
prepared as a mixture of a conjugated conductive polymer
and a classical nonconductive polymer, can show quite a
good electrical conductivity at a relatively low content of
the conducting phase. However, there have been some
problems in the application of the commercial production
of antistatic composites and films because conductive poly-
mers are not cost effective.
The antistatic effect of surfactants or hydrophilic sub-
stance is realized by the equilibrium moisture adsorbed
on the surfactant, so excellent antistatic effect is not
achieved under low humidity. Also, the surfactant can be
removed by rubbing or washing back and forth, so the
antistatic effect disappears easily.
ZnO, a compound semiconductor with a wide direct-
band gap of 3.3 eV, is a good candidate in some applica-
tion fields, especially, tetra-shaped ZnO whisker (ZnOw).
It is a new kind of micro-fiber consisting of a single crys-
tal and possesses good properties such as high strength,
good wear resistance, microwave absorption, and antibac-
terial properties. It can be widely used as both functional
and structural materials [16]. Research indicates that
ZnOw is an effective agent for antistatic of resin materi-
als. In this study, ZnOw fillers are dispersed into PET ma-
trix, the structure and morphology of these composites are
discussed. The antistatic performance and electronic con-
duction mechanism are studied in detail.
Correspondence to: Chuanxi Xiong; e-mail: [email protected]
DOI 10.1002/pc.20679
Published online in Wiley InterScience (www.interscience.wiley.com).
VVC 2008 Society of Plastics Engineers
POLYMER COMPOSITES—-2009
EXPERIMENTAL
Materials
Poly(ethylene terephthalate) pellets (0.8 dl/g with
intrinsic viscosity and 1.3 g/m3 with density) used in this
work were commercial polymers manufactured by Far
Eastern Industries (Shanghai). ZnOw, in the form of a
white fluffy powder in appearance and with a tetrapod-
shaped structure in microimage (as shown in Fig. 1) was
purchased from Advanced Technologies and Crystal-wide.
The surface resistivity is 103–104 O, with the length of
the whisker needle of about 5–200 lm, the diameter at
the base of the whisker needle of 0.1–10 lm, real density
and apparent density of 5.8 and 0.01–0.5 g/cm3, respec-
tively. Spherical ZnO (s-ZnO) powders were purchased
from Tianjin Tianda Purified Materials Fine Chemical.
APTMS (c-aminopropyltrimethoxysilane) was supplied by
Wuhan University Silicone New Materials. The other
materials were used without any purification.
Modifying the Surface With Coupling Agents
Two kinds of ZnO powders were dried at 608C for 10 h
and put into to a glass flask with a mechanical agitator,
water bath, condenser, and thermometer. The coupling
agents APTMS was used with 1 wt% ZnO and mixed with
acetone. The mixture was stirred and refluxed at 588C for
2 h. Then the suspension solution was deposited for 1 h at
room temperature and then filtered. The treated ZnO was
dried to constant weight in a vacuum drying oven.
Preparation of PET/ZnO Composites
Binary blends of PET pellets and ZnO were melt
mixed by using a SJJ-06 twin screw extruder (Ruiming
Plastics Machine Company) with a screw diameter of
11.5 mm and L/D (length–diameter ratio) of 10. The bar-
rel was set with temperature of 2608C and a screw speed
of 60 rpm. The mixture was stirred about 10 min and
then the extruded strand was cut into pellets for injection
molding. The extruded pellets were molded into the
standard specimens using a WZM-1 micro injection mold-
ing machine (Jilin University Science & Teaching Instru-
ment Plant). Characterization.
FTIR spectra of the samples were recorded between
4,000 and 500 cm21 on a Nicolet Nexus Fourier Trans-
form Infrared Spectrometer (Thermo Nicolet Corporation,
USA). Thin films were prepared, by mixing the finely
ground solid sample with powdered potassium bromide,
and the mixture was pressed under high pressure. The
morphology of the fractured surface was examined by a
JSM-5610LV SEM (Japan Electron Optics Laboratory).
Before observation the samples were gold-coated in a
vacuum chamber to make the surfaces conductive.
The resistivities of the composites were tested on a
ZC-36 model super high resistance meter (Shanghai Cany
Precision Instrument) according to the Chinese standard
of GB/T 1410-2006. The test was conducted with a volt-
age of 500 V, charging of 15 s, temperature of 238C, andrelative humidity of 65%.
RESULTS AND DISCUSSION
FTIR Analysis and Morphology
The FTIR spectra of PET/ZnOw composites and pure
PET are presented in Fig. 2. There was a little difference
between the two spectra pictures, and the new peak in the
PET/ZnOw at 3,300 and 1,080 cm21 corresponded to the
N��H and Si��O vibration of APTMS silane coupling
agent, respectively. This indicated that the silane coupling
agent was grafted onto the surface of ZnOw and inter-
acted well with PET matrix.
Figure 3 presents the morphologies of the PET/ZnO
composites. From the micrographs of bulk samples, it can
be seen that the distribution of ZnOw is basically uniform
in the PET matrix although they are randomly distributed.
At the same time, it can be observed that a small quantity
of ZnOw agglomeration phenomena occurred in the
blends system. The length of some ZnOw particles is
more than 30 lm. When the composites were in the proc-FIG. 1. SEM image of ZnOw.
FIG. 2. FTIR spectra of PET/ZnOw and pure PET.
DOI 10.1002/pc POLYMER COMPOSITES—-2009 227
essing of the melting extrusion, some amounts of ZnOw
needles were broken away from the matrix and some
small cavities formed that could be seen on the fracture
surfaces. Most of the ZnOw remained in situ in the PET,
an interface between the dispersion phase (ZnOw) and the
continuous phase (PET) could be observed. These results
suggest that PET is compatible with ZnOw modified by
the coupling agents to some degree.
Mechanism Analysis of Electric Conduction
Figures 4 and 5 illustrate the surface resistivity (qs) andvolume resistivity (qv) of two kinds of PET/ZnO compo-
sites plotted against the weight content of ZnO. It can be
found that the resistivity of PET/ZnOw composites
decreased slowly before 8 wt% of ZnOw content in the
PET matrix. When the content of ZnOw reached between 8
and 12 wt%, qs and qv had decreased rapidly from 2.8 31013 O to 3.6 3 108 O and 4.3 3 1014 O � cm to 4.2 3 109
O � cm, respectively. The blends of PET/ZnOw show the re-
sistivity low enough for achieving better antistatic perform-
ance. With addition of the ZnOw amount above 12 wt%,
there was not an obvious decrease for two kinds of resistiv-
ities value. For the PET composites filled with s-ZnO, the
magnitude of qs and qv were about 1012 even 20% of s-
ZnO content, which had no obvious influence on the PET
resistivities compared with ZnOw.
ZnOw plays a significant role in reducing the resitivity
of polymer composites and is an effective antistatic agent
for resin materials. The mechanism of electric conduction
in the composites containing ZnOw can be described as
the following reason:
Tunnel Effect [17]
When addition of only a small quantity of ZnOw is
available, there is not a continuous conductive network
formed in the polymer composites. Nevertheless, the
resistivities of the composites decrease by several orders
comparing with the matrix. Tunneling theory must be
taken into account. In the electron tunneling theory, the
electrical conduction is believed to take place by electrons
FIG. 3. SEM image of PET/ZnOw composites with various content: (a) 4 wt% ZnOw, (b) 8 wt% ZnOw, (c) 12 wt% ZnOw, and (d) 16 wt% ZnOw.
FIG. 4. Volume and surface resistivity vs. ZnOw content in PET.
228 POLYMER COMPOSITES—-2009 DOI 10.1002/pc
jumping across a gap or tunnel through energy barriers
between conducting elements in the polymer matrix. The
tunnel effect phenomenon can be described by Fig. 6.
The following equation regarding the charge carrier
and penetrating probability explains this phenomenon:
g ¼ exp�4pah
ffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi2mðu0 � EÞ
p� �ð1Þ
where g is the penetrating probability, h equals 6.63 310234 J � s and is Planck’s constant, a is the distance
between the charge carriers.
It can be found that the tunnel effect decreases expo-
nentially with the increase of the potential barrier. When
charge carriers are electron and (u0 2 E) ¼ 1.6 3 10219
J in the electron system, according to (1), the relation of
between g and a is shown in Table 1.
It can be seen from Table 1 that leakage current gener-
ating from the tunnel effect has become obvious only
when the distance between the needles of the whiskers is
less than 0.2 nm. In actual composites, the related situa-
tion certainly exists, so the tunnel effect appears in the
PET/ZnOw composites. This explains that although the
content of ZnOw is relatively low not to form a continu-
ous conductive network, polymer/ZnOw composites ex-
hibit certain electric conductivity.
Discharging Effect at the Pinpoint [18]
When the composites are loaded by an electric field,
there exists high charge density on the pinpoint of the
needle because the pinpoint of the needles of whiskers is
very sharp, exciting strong electric fields on the vicinity
and resulting in the breakdown of polymer medium
locally. The appearance of those local breakdown areas
can be also regarded as decreasing the width of potential
barrier, thereby causing the discharging effect become
obvious.
If a ball-like particle is considered, the surface density
of electric charge is expressed as:
rs ¼ Q
4pR2ð2Þ
where Q is the electric charge on the surface and R is the
radius of the ball-like particle.
A common ZnOw is composed of two components: an
octahedron of the central nucleus and four hexagonal pyr-
amids of the cross section [19]. Here, a needle of the
whisker can be approximately regarded as half an ellip-
soid, and the surface electric density of a rotating ellip-
soid is introduced to simulate the needle of whiskers.
r ¼ Q
4pab2� 1ffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffiffi
x2
a4 þ y2þz2
b4
q ð3Þ
where a is the length of the ellipsoid’s longer axis, b is
the length of the ellipsoid’s shorter axis and a/b is the as-
pect ratio of the ellipsoid. The surface density of electric
charge at the needle tip (x ¼ a, y ¼ z ¼ 0) can be
obtained as:
rw ¼ Q
4pb2ð4Þ
The volume of a rotating ellipsoid is 83pab2. If a tetra-
pod-shaped whisker occupies the same volume as a ball-
like particle, and the aspect ratio is 40, we obtain
R ¼ 4:3b ð5Þrw=rs ¼ 18:5 ð6Þ
The results of the above analysis demonstrate that the
density of electric charge at the pinpoint of a whisker
needle(whose aspect ratio is 40) is about 20 times higher
than that of general spherical particle at the same volume
fraction, which indicates an obvious charge concentration
at the tips of whisker. The effect of the related charge
concentration at the tips is so obvious that the charge con-
FIG. 5. Volume and surface resistivity vs. s-ZnO content in PET.
FIG. 6. Tunnel effect phenomenon.
TABLE 1. The relation of between g and a.
a/nm g a/nm g
0.1 0.36 0.5 0.006
0.2 0.13 0.6 3.9 3 1025
0.3 0.047 2.0 1.0 3 1029
0.4 0.017
DOI 10.1002/pc POLYMER COMPOSITES—-2009 229
centrating effect may have caused the polymer matrix
between the trips of the whiskers to be broken down,
therefore lowering the resistivity of the composites.
Conductive Network
When a sufficient amount of filler is loaded, the filler
particles get closer to each other and form linkages,
which result in continuous chains (conductive network) in
the polymer matrix. There is a critical content at which
the system experiences the transition from an insulator to
conductor. At the critical content, the conductive network
in the matrix will form and a large increase in conductiv-
ity results from a minor increase of the fillers in the ma-
trix. The corresponding filler content is called the percola-
tion threshold. When the content of conductive fillers
overpasses this critical value, the conductivity of the sys-
tem is mainly determined by the conductive network
formed by the fillers. Since the conductive network al-
ready exists, the conductivity will increase marginally
against the increase of filler content.
This phenomenon can be explained by percolation
theory [20] which has been successfully used for describ-
ing the electrical conductivity of mixtures of conductors
and insulators in the following form:
r ¼ r0ðv� vcÞt ð7Þwhere r is the conductivity of the mixture, r0 is the con-
ductivity of the filler particles, vc is the critical volume
fraction (percolation threshold) of formation of conductive
network, v is the volume fraction of conductive phase
above vc. The critical exponent t expresses the rate of
conductivity change depending on the conductive compo-
nent concentration. From the Fig. 4, it can be observed
that at about 10 wt% of ZnOw which corresponds to 2.4
vol% in the composites, the resistivity value decreases
drastically by several orders of magnitude.
It is understandable that the content to obtain the con-
ductive network is much lower for ZnOw than for s-ZnO.
This can be ascribed to the tetrapod-shaped needle struc-
ture of ZnOw, which will lead to the formation of the
conductive network more easily.
Garboczi et al. [21] investigated an idealized model of
conductive composites built up from freely rotating ellip-
soid particles randomly placed in polymer matrix. This
percolation theory model is that completely permeable fil-
ler objects, whose free interconnecting as more and more
objects uniformly added a matrix, eventually results in a
geometrically continuous conductive network. By means
of theory deduction and simulation study, the critical vol-
ume fraction of ellipsoids of revolution, which is also
called percolation threshold, may be expressed as:
vc ¼0:6
b
aðprolateÞ
1:27a
bðoblateÞ
8><>: ð8Þ
Tetrapod-shaped ZnO whisker can be approximately
expressed as two prolate ellipsoids of revolution, therefore
the critical volume fraction of ZnOw in polymer matrix is
given by vc ¼ 0:3 ba in theoretical distribution.
For the actual processing PET/ZnOw system of the
composites, other important influencing factors must be
taken into accounts [22]:
(a) Covering effect: In the actual composites system, the
shorter whiskers below 12la (la is the average length of
whisker) don’t contribute to the formation of an effec-
tive conductive network. Moreover, those whiskers
above 2la probably overlap the space that other
whiskers have occupied in the composites system.
The covering coefficient a1 is used to express the per-
centage of the shorter (�12la) and longer (‡2la)
whiskers that will lead to the increase of vc value.
vc ¼ 0:3ð1þ a1Þba
ð9Þ
where a1 depends upon the uniformity of ZnOw.
(b) Obstruction effect: In PET/ZnOw composites system,
some amounts of thicker PET insulating layers may
exist between separate ZnOw particles. Thus, the
spaces between noncontacting ZnOw particles are suf-
ficiently large, and the assumption of no continuous
conductive network in some areas is valid. It is diffi-
cult for electrical charges to transport beyond insulat-
ing layers because there is obstruction formation of
PET matrix layer. Therefore, the critical volume frac-
tion is given by
vc ¼ 0:3ð1þ a1Þbð1� a2Þa ð10Þ
where a2 is the obstruction fraction of the PET matrix.
(c) Agglomeration effect: For the case of the process of
the PET/ZnOw composites, a certain amount of aggre-
gates of ZnOw might occur. The agglomeration of
ZnOw particles into clusters permits the ZnOw par-
ticles to conduct at higher weight percentage, resulting
in the appearance of a larger volume fraction. So, the
value of the critical volume fraction has the following
form:
vc ¼ 0:3ð1þ a1Þbð1� a2Þð1� a3Þa ð11Þ
where a3 is the agglomeration coefficient of ZnOw.
(d) Breakage effect: Processing parameters, especially
those involving considerable shear of the PET/ZnOw
mixtures, have a profound effect on the conductive
properties of the ultimate conductive polymer compo-
sites. To ensure the conductive ZnOw dispersed uni-
formly throughout the polymer matrix, the composites
should be stirred sufficiently. On the other hand, how-
ever, this mixing condition will generate greater
shearing forces and lead to heavy breakage of the
whiskers, which will reduce their tendency to form
conductive network in the polymer matrix. The break-
230 POLYMER COMPOSITES—-2009 DOI 10.1002/pc
age coefficient c1 and c2 are introduced to explain the
influence of the breakage effect on the lengths of nee-
dles and the volume fraction, respectively. Consider-
ing the above mentioned factors, the critical volume
fraction should be modified as:
vc ¼ 0:3ð1þ a1Þð1þ c2Þbð1� a2Þð1� a3Þð1� c1Þa
ð12Þ
The critical volume fraction for forming conductive
network in the composites is mainly determined by aspect
ratio, but the influences of covering, obstruction, agglom-
eration, and breakage effects during the processing should
be considered. In the composites of PET/ZnOw, let a/b ¼40, a1 ¼ 0.2, a2 ¼ 0.15, a3 ¼ 0.2, c1 ¼ 0.3, c1 ¼ 0.3 we
get vc ¼ 2.6%, which basically coincides with 2.4% of
the experimental result.
CONCLUSIONS
Silane coupling agent was used to improve the compat-
ibility of PET and ZnOw. The difference in the FTIR
spectra of PET-filled ZnOw suggested that coordination
interaction appeared between the surface of ZnOw and
function group of PET matrix. The morphologies of the
PET/ZnOw showed that the distribution of ZnOw is basi-
cally uniform and random in the PET matrix, which is in
favor of the formation of continuous conductive network.
The conductive mechanism of PET filler ZnOw was
explained by tunnel effect, discharging effect at the pin-
point and conductive network. At the lower loading con-
tent of ZnOw, if the interval distances between whisker
particles may be within 0.2 nm, there exist tunnel effect
phenomena. When the composites are loaded by an elec-
trical field, the charge concentration at the tips of the
whisker is distinct. The thinner layer of polymer matrix
between the tips of the whiskers will be broken down,
resulting in discharging effect at the pinpoint. When suffi-
cient ZnOw fillers are added to PET matrix to cause con-
tinuous conductive network, the resistivity of resultant
composites can be varied by several orders of magnitude
as the ZnOw concentration is increased beyond a certain
critical volume fraction. The critical value is basically
determined by aspect ratio, but the influences of covering,
obstruction, agglomeration, and breakage effects also play
an important role in the actual processing systems.
REFERENCES
1. K. Toshikazu, A.W. Barbara, T. Akio, and O. Hirokuni,
J. Electrostat., 64, 377 (2006).
2. P. Ghosh and A. Chakrabarti, Eur. Polym. J., 36, 1043
(2000).
3. D. Pantea, H. Darmstadt, S. Kaliaguine, L. Summchen, and
C. Roy, Carbon, 39, 1147 (2000).
4. M.K. Schwarz, W. Bauhofer, and K. Schulte, Polymer, 43,3079 (2002).
5. H.G. Busmann, B. Gunther, and U. Meyer, Nanostruct.Mater., 12, 531 (1999).
6. Y.P. Mamunya, V.V. Davydenko, P. Pissis, and E.V. Lebe-
dev, Eur. Polym. J., 38, 1887 (2002).
7. M.H. Choi, B.H. Jeon, and I.J. Chung, Polymer, 41, 3243(2000).
8. W. Thongruang, R.J. Spontak, and C.M. Balik, Polymer, 43,2279 (2002).
9. M. Omastova, S. Kosna, J. Pionteck, A. Janke, and J. Pavli-
nec, Synth. Met., 81, 49 (1996).
10. M. Omastova, J. Pavlinec, J. Pionteck, F. Simon, and S.
Kosina, Polymer, 39, 6559 (1998).
11. M. Omastova, I. Chodak, and J. Pionteck, Synth. Met., 102,1251 (1999).
12. S.K. Dhawan, N. Singh, and D. Rodrigues, Sci. Technol.Adv. Mater., 4, 105 (2003).
13. V. Kale and M. Moukwa, J. Electrostat., 38, 239 (1996).
14. B. Dacre and J.I. Hetherington, J. Electrostat., 45, 53 (1998).
15. V. Dudler, M.C. Grob, and D. Merian, Polym. Degrad.Stab., 68, 373 (2000).
16. Z. Zhou, W. Peng, and S. Ke, J. Mater., 13, 57 (1998).
17. F. Ma and X.J. Zhai, Physics, 29, 552 (2000).
18. S.C. Li, J.Q. Xu, and C.Y. Chen, Electrostatics, 12, 49
(1994).
19. E.F. Chen, Y.J. Tian, Y.J. Cheng, and B.L. Zhou, J. Chin.Ceram. Soc., 29, 151 (2001).
20. H. Scher and R. Zallen, J. Chem. Phys., 53, 3759 (1970).
21. E.J. Garboczi, K.A. Snyder, and J.F. Douglas, Phys. Rev. E.,52, 891 (1995).
22. Z.W. Zhou, L.S. Chu, W.M. Tang, and L.X. Gu, J. Electro-stat., 57, 347 (2003).
DOI 10.1002/pc POLYMER COMPOSITES—-2009 231