V. K. Sachdev*,
S. K. Sharma,
Monika Tomar†
,
Vinay Gupta and
R. P. Tandon
Department of Physics and Astrophysics, University of Delhi, Delhi, India. E-mail: vk_sachdev@yahoo.com
First published on 29th April 2016
Acrylonitrile–butadiene–styrene (ABS) nanocomposites filled with multiwall carbon nanotubes (MWCNTs) are prepared through localized conductive patterning, using dry powder tumble mixing succeeded by hot compression technique. Electrical conductivity and complex permittivity together with electromagnetic interference shielding effectiveness (SE) are investigated in 8–12 GHz frequency range. Abrupt increase in dc conductivity by number of orders of magnitude on addition of 5 × 10−4 volume fractions of MWCNTs marked as percolation threshold, has adequately described the conductivity behavior with statistical parameters of percolation and GEM models. The SE of these nanocomposites increases with increase of MWCNTs content. SE ∼ 1 dB at 12 GHz produced with 0.05 wt% MWCNTs grows to ∼40 dB on addition of 5 wt% MWCNTs. SE exhibit marginal dependence or even independence on frequency for most of the compositions with 0–5 wt% MWCNTs. SE reflection (SEref) and absorption (SEabs) both are increasing with the rise of MWCNTs content. However increase in SEabs is faster than SEref in addition to its dominance. Complex dielectric constants in 8–12 GHz frequency range have been calculated by means of S11/S12 parameters using Nicolson Ross Weir algorithm. The variation of the SE as a function of dc conductivity which has rarely been examined in literature, investigated and compared with other polymer composites here.
Presently lightweight and effective EMI shielding materials are sought to screen workspaces, equipment on board, computers, telecommunication paraphernalia besides circuits of defense installation and diagnostic equipment in hospitals. Polymer-based conducting systems are considered to be versatile EMI shielding materials because of easy synthesis, lower mass, cost effective in large-scale production and simple processing.2,3 Conducting composites with polymer matrix surpass their metallic counter parts due to added range of mechanical properties like strength, flexibility, and environmental resistance. For making of conductive polymer composites, thermoplastic and thermoset matrices filled with carbon or metallic fillers (powder/fiber) have normally been used. Electrical and dielectric properties of these composites determined by the filler amount, particles size, shape, material defects, connectivity and the processing techniques.4–7 An intrinsically conducting polymer8–10 can be used as material for EMI shielding, but disadvantageous because of poor processability, environmental instability, high cost, and lack of mechanical properties. Extrinsically conducting polymer composites are lighter in weight, easy to develop, cost effective and seams can either be reduced or completely eliminated by molding.11 For an efficient shielding, the conducting filler in polymer composites should have large aspect ratio in addition to small size and high conductivity.12 A special skill is needed for appropriate control of EM behavior of such composites, since these cannot be made efficiently or easily into the requisite forms with a minimum amount of filler. For a convincing SE, extremely low amount of nanosize fillers have been identified.13–15 With the advent of nanotechnology radar absorbing materials are gaining importance due to prospective increase of shielding and microwave absorbing properties besides decrease in mass and volume of structures. In defense and space applications low mass materials are significant because of high costs of launch and launcher payload mass. Among nanosize fillers, carbon nanotube (CNT) has offered to improve the properties of the host polymer matrix due to distinctive features inclusive high strength and low density.16 The percolation threshold is noticeable with a very small content of nanofiller which is produced as a result of creation of network of conductive paths. The threshold is recognized as inverse relation to the aspect ratio of CNT.17 Several researchers18–20 described very low percolation threshold which depends on dispersal of conducting filler in the polymer matrix21,22 besides processing technique.6 For realization of lower percolation threshold good dispersion of CNT is essential23 for reason of CNTs agglomeration tendency.24,25 Functionalized CNT shows higher conductivity of composites equated with the un-functionalized. Studies revealed the functionalization made improvement in dispersion of CNT in natural rubber [NR] matrix leading to decrease in electrical resistivity of CNT–NR composites,26 attributed to preferential dispersion of filler in composites.
In this research work focus is on analysis of acrylonitrile butadiene styrene (ABS) composites filled with minimum amount of conducting filler with a good-sized EMI shielding capability. ABS offers a comfortable processability besides low cost, and dependable notch impact resistance. Generally, ABS plastics are employed for mechanical works in addition to several combinations with other materials for varied range of features and uses. Recently, the EMI shielding capabilities of polymeric materials filled with multiwall carbon nanotubes (MWCNTs)27–35 have been investigated using solution processing technique together with sonication and compression molding. MWCNTs possess tubular geometry offers huge surface area besides high aspect ratio is expected to allow property enhancement at lower concentration compared to conventional fillers. SE obtained was ∼30 dB with 5 wt% MWCNTs in ABS matrix,27 whereas in the present work 40 dB of SE is achieved by addition of 5 wt% MWCNTs to ABS, using simpler method of tumble mixing of dry powders followed by hot compression.1,7,15 Earlier this group has produced graphite-filled ABS composites7 through the same method of tumble mixing of dry powders followed by compression molding at 90 °C. The shape of graphite particles is essentially flake. During mixing graphite flakes coat on to the surface of ABS particles. Gaps are obvious in coats among graphite flakes due to their planer geometry. These gaps are filler depleted areas containing ABS only which is transparent to EM waves and serve as windows for EM waves escape. The dimension of gaps would be larger for lower packing of graphite, decreases with higher loading. The SE was <30 dB for 5 wt% graphite in ABS in the X-band frequency range. Thus besides fabrication method and processing conditions the shape of filler is also important to achieve better results.
Composites with pre-localized networked of MWCNT are acknowledged better to dispersed MWCNTs (solution polymer mixing) in relation to lower electrical conductivity and higher compressive strength.15 The locations of conductive MWCNTs in the insulating ABS matrix would obviously add toward improvement of electrical and dielectric properties of the composites. Thus the consideration of complex permittivity (ε*) would be of great importance and relevance.
ε* = ε′ − jε′′ | (1) |
Fig. 2(a)–(c) are displaying ε′, tanδ and ε′′ variations with frequency for various ABS nanocomposites pellets with 0.0–5.0 wt% MWCNTs. Up to 1.0 wt% MWCNTs in ABS, ε′ increases with increasing MWCNTs, yet close to matrix ABS and almost independent of frequency. The value of ε′ is primarily based upon the effects of interfacial orientation, atomic and electronic polarizations in the nanocomposite. The orientation and interfacial polarizations depend on the content of filler. Probably, the MWCNTs have brought about an increment in ε′ value by increasing the MWCNTs loading. It is observed that for >1 wt% MWCNTs loading, the value of ε′ gives maximum values at higher frequencies which can be explained by bearing in mind that MWCNT/ABS nanocomposites are made of number of micro-capacitors formed by nanofillers/aggregates and the polarization centers created from the defects in the nanofiller structure27 contribute towards rise in ε′ with increasing frequency. This is anticipated to be as a result of effect of orientation and polarization in network pattern of conductive paths.
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Fig. 2 Frequency dependencies for the MWCNT/ABS nanocomposites with different MWNT content for dielectric constant (ε′); (b) dissipation factor (tan δ); (c) loss factor (ε′′). |
The dissipation factor tanδ as a function of frequency at various MWCNTs loadings is shown in Fig. 2(c), tan
δ registers decrease by increasing the frequency for >1 wt% MWCNTs loading. It has been noticed that increasing the MWCNTs in the low frequency region represents a significant variation, it is minimum for ABS and maximum for 5 wt% MWCNTs nanocomposite. In the higher frequency range, tan
δ curves come nearer even crossover the lower value curve. Increasing MWCNTs content produce an increase in orientation polarization that results in an improvement in the dissipater. Dissipation factor tan
δ is described as tan
δ = ε′′/ε, where ε′′ is the dielectric loss. Loss factor ε′′ is the average power factor over a given period of time describes the losses in transmission and distribution. The variation of ε′′ for the composites is shown in Fig. 2(c). It can be observed that ε′′ is low in lower frequency region and is found maximum for the composite with MWCNTs 5 wt%. By increasing frequency, the value of ε′′ decreases.
It is interesting to note, ac conductivity (σac) for all MWCNTs/ABS nanocomposites is almost independent of frequency. σac as function of frequency for these nanocomposites have been calculated through ε′′ using relation.
σac = ωε0ε′′ | (2) |
At a certain frequency σac rises with the increase of MWCNTs content. Variation of σac with frequency for pristine ABS and other MWCNT/ABS nanocomposites have displayed curves similarities.
At 10 GHz representative frequency, behavior of σac for MWCNTs/ABS nanocomposites is made known in Fig. 4. Qualitative variation σac is similar to σdc.1 However σac values are all the way higher than σdc. This can be explained yet again by above consideration that MWCNTs/ABS nanocomposites are made of number of micro-capacitors formed by nanofillers/aggregates and the polarization centers created from the defects in the nanofiller structure.27 Thus, MWCNTs/ABS nanocomposite is a heterogeneous system consists of microstructure resistor-capacitor networks that contain both dielectric (capacitor) and conductive (resistor) regions. At higher frequency (10 GHz) the σac of the micro-capacitors admittance would be more than the resistors conductivity for all compositions of MWCNT/ABS. For ABS nanocomposites with small content of MWCNTs, hopping/tunneling of electrons contributes towards the σdc. Nevertheless, at higher contents of MWCNTs, some extra conductive networks are put up within the ABS matrix and the σdc proceeds to σac with increasing MWCNTs.
EM radiations can pass through neat ABS. Its total SE is almost zero. SE increases with increase of MWCNTs content in ABS nanocomposites. Nanocomposite containing a 0.05 wt% of MWCNTs produces SE ∼ 1 dB at 12 GHz which raises to ∼40 dB on addition 5 wt% MWCNTs. Most of the compositions showed minimal dependency of SE on frequency. For nanocomposite with 5 wt% MWCNTs the highest and smallest SE values are 40.2 dB at 12 GHz and 38.2 dB at 8.5 GHz respectively. The uncertainties in SE measurements are ±0.07 to 1 dB using VNA uncertainty calculator. The RL values are observed to be cumulative with frequency for all compositions of MWCNT/ABS. It is noticeable that the nanocomposites having a high value of SE showed lower value of RL. This implies that lower the value of RL higher is the reflection owing to larger value of conductivity. For higher loading of MWCNTs, RL is smaller. For MWCNT/ABS nanocomposites with 5 wt% and 0.05 wt% MWCNTs the RL values are ∼1 dB and ∼6 dB respectively at 12 GHz.
Evaluated values for R, and A (absorbance) for various compositions of MWCNT/ABS nanocomposites in X-band frequency range using above known relations are summarized in Table 1. R is rising with the increase of MWCNTs since more EM waves meet with more number of MWCNTs. The increase in R with MWCNTs is due to the increase in dielectric constant.40 The positions of MWCNTs within the ABS matrix are thought to be responsible for the magnitude of R and A. Reflectance R takes place before absorbance A. Thus there is a lower amount of the radiation left for A. The proportion of the power truly absorbed by the materials reaches a maximum before decreasing at high electrical conductivity. It actually never surpasses 45.7% for sample with a thickness of 1.28 mm at 12 GHz. Although the absorption capability is improved, there is a lesser part of the radiation left for absorption after the extensive reflection linked to the high conductivity.
MWCNT wt% | 0.1% | 0.2% | 0.5% | 1% | 3% | 5% | ||||||||||||
---|---|---|---|---|---|---|---|---|---|---|---|---|---|---|---|---|---|---|
Freq (GHz) | R% | A% | Aeff% | R% | A% | Aeff% | R% | A% | Aeff% | R% | A% | Aeff% | R% | A% | Aeff% | R% | A% | Aeff% |
8.0 | 27.0 | 2.3 | 3.2 | 27.9 | 11.2 | 15.5 | 28.2 | 29.5 | 41.0 | 45.6 | 41.5 | 76.3 | 75.0 | 24.7 | 98.84 | 81.3 | 18.7 | 99.92 |
8.5 | 25.1 | 2.1 | 2.9 | 25.8 | 10.6 | 14.3 | 26.6 | 28.7 | 39.0 | 43.1 | 42.4 | 74.7 | 72.1 | 27.5 | 98.87 | 79.4 | 20.6 | 99.93 |
9.0 | 23.9 | 2.1 | 2.7 | 24.5 | 10.3 | 13.6 | 25.5 | 28.1 | 37.7 | 41.3 | 43.2 | 73.5 | 69.6 | 30.0 | 98.92 | 77.7 | 22.3 | 99.93 |
9.5 | 23.0 | 2.1 | 2.9 | 23.4 | 10.1 | 13.2 | 24.8 | 27.5 | 36.6 | 39.7 | 43.8 | 72.7 | 67.5 | 32.2 | 98.98 | 76.3 | 23.7 | 99.94 |
10.0 | 22.3 | 2.3 | 2.9 | 22.5 | 10.0 | 12.9 | 24.3 | 27.1 | 35.8 | 38.5 | 44.3 | 72.0 | 65.7 | 34.0 | 99.03 | 75.1 | 24.9 | 99.95 |
10.5 | 21.9 | 2.1 | 2.7 | 21.8 | 9.6 | 12.3 | 24.0 | 26.6 | 35.0 | 37.6 | 44.6 | 71.4 | 64.3 | 35.4 | 99.09 | 74.2 | 25.7 | 99.95 |
11.0 | 21.4 | 2.1 | 2.7 | 21.1 | 9.7 | 12.3 | 23.7 | 26.4 | 34.7 | 36.7 | 44.9 | 71.0 | 63.0 | 36.7 | 99.14 | 73.3 | 26.6 | 99.96 |
11.5 | 20.8 | 2.2 | 2.8 | 20.1 | 9.7 | 12.1 | 23.4 | 26.3 | 34.3 | 35.9 | 45.4 | 70.8 | 61.7 | 38.0 | 99.20 | 72.6 | 27.4 | 99.96 |
12.0 | 20.3 | 2.3 | 2.9 | 19.1 | 9.3 | 11.5 | 23.2 | 25.8 | 33.6 | 35.1 | 45.7 | 70.5 | 60.7 | 39.0 | 99.24 | 71.8 | 28.2 | 99.97 |
Thickness (mm) | 2.57 | 2.09 | 2.38 | 1.28 | 2.52 | 2.80 |
SEabs can be expressed39 by a relation, SEabs = −10log10(1 − Aeff) = −10
log10{T/(1 − R)}. Aeff and T are the effective absorption and transmittance respectively. Aeff can be evaluated using this relation. Table 2 displays the values of Aeff at 9 GHz demonstrative frequency for MWCNT/ABS (this work) which rises with increasing content of MWCNT together with dominance in contrast to R. This trend is identical to behavior reported earlier for MWCNT/polystyrene (PS)15 (Table 2). Aeff is 99.9% compared to 77.7% of R on 5 wt% of MWCNTs in ABS. MWCNT/ABS is more absorptive than the MWCNT/PS for all equivalent contents of MWCNTs, comparison of Aeff reveals.
MWCNT wt% | MWCNT/ABS | MWCNT/PS (ref. 15) | ||||||
---|---|---|---|---|---|---|---|---|
R% | A% | Aeff% | T% | R% | A% | Aeff% | T% | |
0 | 21.6 | 0.5 | 0.68 | 77.9 | — | — | — | — |
0.05 | 23.1 | 1.2 | 1.6 | 75.6 | — | — | — | — |
0.1 | 23.9 | 2.1 | 2.7 | 74.0 | 22.9 | 18.1 | 23.4 | 59 |
0.2 | 24.5 | 10.3 | 13.6 | 65.2 | 29.9 | 26.4 | 37.6 | 43.7 |
0.5 | 25.5 | 28.1 | 37.7 | 46.4 | 47.0 | 30.7 | 57.9 | 22.3 |
0.8 | 39.0 | 41.6 | 68.3 | 19.3 | — | — | — | — |
1 | 41.2 | 43.2 | 73.5 | 15.5 | 39.1 | 31.9 | 52.3 | 29.0 |
1.2 | 47.2 | 39.2 | 74.3 | 13.6 | — | — | — | — |
2 | 63.9 | 34.0 | 94.2 | 2.1 | — | — | — | — |
3 | 69.6 | 30.0 | 98.9 | 0.3 | 70.8 | 26.5 | 90.6 | 2.8 |
5 | 77.7 | 22.3 | 99.9 | 0.01 | 78.1 | 21.3 | 97.4 | 0.6 |
At lower contents of MWCNTs, SE of PS nanocomposites are more than the ABS nanocomposites. With more addition of MWCNTs, there is a net rise of SE in both. MWCNT/ABS demonstrates progressively improved SE and excels over the MWCNT/PS. At 5 wt% MWCNTs, SE for ABS nanocomposite grows up to ∼38 dB compared 22 dB of PS nanocomposite. Effect of use of filler Gr in place of MWCNT7 on SE can also be noticed in Gr/ABS composites; SE is all the way less than PS and ABS nanocomposites.
As shown in Fig. 8, SE increases continually with the dc conductivity for MWCNT/ABS. There are two regimes: first, just lower than the percolation threshold, the SE rises faintly with increase in MWCNTs since in this arrangement a small change in filler concentration abruptly raises the σdc while the influence on the SE rests minimal. On inclusion of 0.2 wt% MWCNTs, the σdc of ABS nanocomposite increases suddenly by ten orders of magnitude in the semiconducting range. The major rise of seven orders in σdc on addition of 0.1 wt% MWCNTs yields 1.3 dB SE only. Further increase of 0.5 wt% MWCNTs to ABS enhances σdc to 0.001 S cm−1, and builds SE to 3.3 dB. In the second regime after the percolation threshold, though σdc does not increase significantly with the addition of MWCNTs, however SE value boosts to 38.3 dB. Additional MWCNTs from 0.5 wt% to 5 wt% flatten the value of σdc from 1 × 10−3 S cm−1 to 44 × 10−3 S cm−1, yet a small change in σdc causing significant increase in SE whereas in first regime a major increase in σdc results a small improvement in the value of SE. Almost similar SE trend has been witnessed for MWCNT/PS nanocomposite15 and graphite/ABS7 composite at 9 GHz shown in Fig. 8. Thus the behavior of σdc is not the only conclusive aspect for controlling the degree of SE. Some additional factors like low percolation threshold conceivably significant. For achievement of filler's low percolation threshold, large aspect ratio is desirable. Development of close packed conductive linkages in the polymer composites8 which increase with the rise in filler content has also been stated for improvement of SE. The conductive network formed owing to adding of conductive filler that interacts with incident radiation likewise be an origin for SE. Addition of filler narrowly packs the conductive network. Therefore their capability to attenuate more EM radiation increases the SE. In this work although the accumulation of MWCNTs from 0.5 to 5 wt% in ABS nanocomposites provide a negligible rise in σdc, but the increase in MWCNTs provide a close packed conductive network. It is recognized earlier1 in such nanocomposites with high MWCNTs content (above percolation) there is making of mesh of conductive network that provide an additional attenuation of EM radiation, like Faraday cage consists of mesh of conducting material which has the capability to stop external electric fields. Meaningful to mention that the conducting mechanism for conductivity needs connectivity between conducting paths, whereas shielding does not.12
SE of metals is because of reflection for the reason of conductivity. Insulating polymers are almost transparent to incident radiation. SE of conductive polymer composite is essentially attribute to reflection and absorption both. Therefore it is necessary to probe the behavior of SEref and SEabs of polymer composites as well to evaluate SEabs overriding contribution to SE.
After SEabs > SEref, Fig. 10(e)–(h) illustrate the shielding performance of MWCNTs (e) 1.0 wt%; (f) 2.0 wt%; (g) 3.0 wt%; (h) 5.0 wt% in ABS nanocomposites. Progress in value of SEabs is much faster than the SEref. In specimen with MWCNTs 0.05 wt%, the value of SEabs and SEref at 12 GHz are 0.11 dB and 0.96 dB improve to 34.69 dB and 5.5 dB at 5 wt% through 1.78 dB and 1.15 dB at 0.5 wt% with crossover (SEabs > SEref).
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Fig. 10 Performance after crossover of SEabs in SE in X band frequency range for MWCNTs (a) 1.0 wt%; (b) 2.0 wt%; (c) 3.0 wt%; (d) 5.0 wt%. |
Studies have discovered that both the contributions increase with the conductivity by way of dominance of SEabs over SEref. The increase in SEabs is larger than SEref, which suggests that the input of absorption to the SE increases with the conductivity, since the reflection increases with the filler content along with increase in dielectric constant.40 Placement of MWCNTs within the interfacial places surrounded by insulating ABS matrix environment is anticipated to induce dielectric property by causing space charge polarization at the interfaces.41 MWCNT/ABS nanocomposites exhibited an increase in the ε′ with rise in MWCNT loading shown in Fig. 2(a). For small content of MWCNTs near to percolation threshold, the ε′ have observant values that are basically nearby to host matrix ABS, do not vary with frequency. ε′ exhibits increase with frequency above 1 wt% of MWCNTs. However these trends are more prominent at higher content of MWCNTs. The ε′ of polymer nanocomposites is stated to be a measurement of number of micro-capacitors formed by nanofillers/aggregates and the polarization centers created from the defects in the nanofiller structure.27 These micro-capacitors created by MWCNTs aggregates are anticipated to work as electrodes filled with insulating polymeric material ABS. Therefore, the rise in MWCNT loading in ABS nanocomposites increases ε′ for the reason of increase in the number of these micro-capacitors and structural defects. Moreover, the decrease of gap owing of increasing MWCNTs content thus increases the polarization of the polymeric material by filling the gap between the nanoparticles, thus enhances the absorption loss. Aeff values obtained at 9 GHz for MWCNT/ABS and MWCNT/PS15 nanocomposites in Table 2 are in accordance to the conjecture.
Footnote |
† Miranda House, University of Delhi, Delhi. |
This journal is © The Royal Society of Chemistry 2016 |