Journal of Nanomaterials

Journal of Nanomaterials / 2012 / Article

Research Article | Open Access

Volume 2012 |Article ID 483093 | 5 pages |

A Simple Effective Flaw Model on Analyzing the Nanofiller Agglomeration Effect of Nanocomposite Materials

Academic Editor: John Zhanhu Guo
Received16 Oct 2011
Revised06 Nov 2011
Accepted06 Nov 2011
Published23 Jan 2012


A special mechanics/material phenomenon involving nanocomposites is the agglomeration of nanofillers at high volume fractions of nanofillers. Numerous experimental investigations on nanocomposites have indicated a significant decrease in mechanical properties, due to the agglomeration of nanofillers. This paper describes a simple effective flaw model to correlate the local mechanical behavior of agglomerated nanoparticles with the change in global strengths of nanocomposites. The estimated bending strength reduction from our model is shown to be similar to experimental results reported by previous researchers. These results can be used as a guide for future nanocomposite design and development. Future nanomaterial manufacturing should be focused on eliminating the largest agglomerates, rather than limiting the nanofiller volume fraction. Meanwhile, by reducing the nanofiller agglomerate size, we expect that a high critical nanofiller volume fraction could be obtained to delay the mechanical property reduction.

1. Introduction

Nanocomposite materials have extensive applications in the fields of science, engineering, and medicine [1โ€“8]. In general, mechanical properties of nanocomposites have been found to increase with increasing volume fractions of nanofillers. However, many experimental investigations on nanocomposite materials have indicated a significant decrease in mechanical properties (such as bending strength and fracture toughness) after a critical nanofiller volume fraction, as illustrated in Figure 1. This phenomenon has been widely attributed to the agglomeration of nanofillers [9โ€“18], and has been illustrated by using imaging techniques such as transmission electron microscopy (TEM). As shown in Figure 1, agglomeration of carbon nanofibers was severe and had a stark effect on the mechanical properties of nanocomposite materials in addition to their low interfacial load transfer [18].

Agglomeration in nanocomposites is the sticking together of nanofillers inside the matrix during the mixing process [19โ€“22], and it is well known that this phenomenon is certainly detrimental to the strength and fracture toughness of nanocomposites. In recent years, reducing agglomeration has been achieved using ultrasonic irradiation [23], shear mixing [24], or seeded polymerization [25], but it is almost impossible to entirely eliminate this effect. For example, large agglomerates can be filtered, but very small agglomerates of two to three nanoparticles might still exist. Unlike stiffness, which is based on volumetric averaging, strength and fracture toughness are very sensitive to minor local defects like nanoparticle agglomeration.

To ensure reliability in strengths of nanocomposite materials at higher volume fractions, a thorough understanding of the nanofiller agglomeration is essential. However, previous work has mainly focused on changes in nanocomposite stiffness due to agglomeration [16, 26]. Berhan and Sastry have developed a model for a similar problem albeit with different objectives [27] (percolation in nanocomposites). Although many researchers identify the phenomenon of agglomeration, no attempt has thus far been made to model this problem from a failure mechanics point of view. It becomes crucial to connect nanofiller agglomeration with material failure for further development of nanocomposites with high (close to critical) nanofiller volume fractions. Therefore, the current paper provides a simple effective flaw model to explain the global bending strength reduction due to local nanoparticle agglomeration. We attempt to model the reduction in global bending strength of the nanocomposite with increasing the nanofiller volume fraction.

2. Effective Flaw Modeling

This paper deals with a nanoparticle-reinforced composite material system reported by Soh et al. [28]. We consider a square representative volume element (RVE) with a side length of ๐ฟโˆ—2๐‘Ÿ, where ๐‘Ÿ is the radius of each nanoparticle and ๐ฟ is the number of nanoparticles at the RVE edge. For the sake of simplicity, we assume that the square RVE has ๐‘โˆ—๐‘ agglomerated nanoparticles in the form of an ideal square shape (with a side length ๐‘โˆ—2๐‘Ÿ) as shown in Figure 2. Additionally, we assume that there are ๐‘€ nonagglomerated nanoparticles within this RVE, and that no more agglomerates exist inside this RVE. Since the initial flaw or failure always stems from the largest agglomerate, our special RVE is focused on the largest agglomerate, although it is acknowledged that other smaller agglomerates exist outside this RVE. This modeling process is similar to a TEM image recording some severe agglomeration as seen in Figure 1, that is, although other small agglomerates were recorded but they were less important to the strength and fracture toughness of nanocomposite materials so they were not reported. Meanwhile, โ€œlarge or smallโ€ agglomerate is always relative to the single nanofiller; but we do not know the size of the smallest agglomerate which cannot be filtered as mentioned. Therefore, the large agglomerate refers to the one agglomerate whose size is larger than other agglomerates in the same specimen for mechanics modeling purpose and not an absolute size. While the presence of complicated agglomerate shapes is acknowledged, this investigation presents the simplest model to understand the agglomeration effect on the mechanical property reduction.

The nanoparticles inside the agglomerate are weakly bonded to each other by van der Waals forces, whereas the nanoparticles on the boundary of the agglomerate are strongly bonded with the matrix. Therefore, we make an assumption that there is one effective flaw inside the agglomerate, with a flaw length of 2๐‘Že๏ฌ€ expressed as2๐‘Že๏ฌ€=๐‘โ‹…2๐‘Ÿโˆ’2๐‘Ÿ.(1) Even in the presence of other effective flaws, this effective flaw is much longer than other flaws, and hence it will lead to the ultimate failure of nanocomposite materials. Now, the volume fraction ๐‘‰๐‘“ of the nanofillers inside the square RVE (with total area 4๐ฟ2โˆ—๐‘Ÿ2) is determined by the total area of agglomerated nanoparticles (number ๐‘โˆ—๐‘), and the total area of nonagglomerated nanoparticles (number ๐‘€):๐‘‰๐‘“=๐‘‰๐ด๐‘“+๐‘‰๐‘“๐‘๐ด=๐‘2๐œ‹๐‘Ÿ24๐ฟ2๐‘Ÿ2+๐‘€๐œ‹๐‘Ÿ24๐ฟ2๐‘Ÿ2.(2) However, final fracture is controlled by the longest flaw inside the largest agglomerate. In this RVE, the non-agglomerated nanoparticles (๐‘€) tend to be much lesser than the agglomerated nanoparticles (๐‘โˆ—๐‘). Therefore, the nanoparticle volume fraction inside this RVE can be approximated as๐‘‰๐‘“=๐‘‰๐ด๐‘“+๐‘‰๐‘“๐‘๐ดโ‰ˆ๐‘2๐œ‹๐‘Ÿ24๐ฟ2๐‘Ÿ2๎ƒŽโŸน๐‘โ‰ˆ2๐ฟ๐‘‰๐‘“๐œ‹.(3) This relationship between the side length of the square agglomerate (๐‘) and the volume fraction of nanoparticles (๐‘‰๐‘“) is expressed for an RVE with a size of 9โˆ—9(๐ฟ=9) nanoparticles as shown in Figure 3. As expected, the agglomerate number increases with the nanofiller volume fraction. But it should be noted that this relation is an approximation rather than an accurate prediction.

When the RVE is subjected to a critical tensile stress, the effective flaw will propagate as a mode ๐ผ crack and cause the final failure of the nanocomposite specimen. The detailed process of interaction among mode ๐ผ cracks, mixed-mode interface cracks, and final failure has been reported in references [29, 30]. For bending experiments, the final failure occurs when the normal stress inside the bending specimen exceeds a critical level for leading to the effective flaw propagation. Therefore, the bending strength ๐œŽ๐ต is related to the mode ๐ผ fracture toughness of the agglomerated nanoparticle ๐ถ๐‘˜๐พ๐ผ๐ถ as [31]:๐ถ๐‘˜๐พ๐ผ๐ถ=๐œŽ๐ตโˆš๐œ‹๐‘Že๏ฌ€๐‘“๎‚€๐‘Že๏ฌ€๐‘Š๎‚,๐ธ,โ€ฆ,(4) where ๐พ๐ผ๐ถ is the mode ๐ผ fracture toughness of the matrix, ๐ถ๐‘˜ is a reduction factor for the fracture toughness of the agglomerated nanoparticles, and ๐‘“ is a function of the flaw length ๐‘Že๏ฌ€, width of the specimen ๐‘Š, effective elastic modulus ๐ธ, and other parameters. The reduction factor ๐ถ๐‘˜ is introduced due to the inability in direct measurement of the mode ๐ผ fracture toughness of agglomerated nanoparticles. The bending strength ๐œŽ๐ต is related to the effective flaw size by๐œŽ๐ต=๐ถ๐‘˜๐พ๐ผ๐ถ๐‘“โˆš๐œ‹๐‘Že๏ฌ€.(5) To illustrate our model, we choose a ๐ถ๐‘˜ value of 1 to match the experimental data point with the critical volume fraction. Substituting (3) into (5), we arrive at this formula for the bending strength:๐œŽ๐ต=๐ถ๐‘˜๐พ๐ผ๐ถ๐‘“๎”๎€ทโˆš๐œ‹๐‘Ÿ2๐ฟ๐‘‰๐‘“๎€ธ/๐œ‹โˆ’1.(6) The variation of bending strengths with the nanoparticle volume fraction, obtained by using different values of ๐ถ๐‘˜, is presented in Figure 4.

3. Results and Discussion

The relationship in (6) is valid only for these bending strengths after the critical nanofiller volume fraction, which is obtained from experimental data shown in Figure 4 [28]. It should be noted that this paper only attempts to model the decrease in bending strength beyond the critical volume fraction. The initial increase in bending strength can be explained using a rule of mixtures type relation. Agglomeration of nanofillers does not affect this initial increase in bending strength. The bending strength is shown to decrease with the nanoparticle volume fraction as predicted by our simple effective flaw model. Also, a higher value of ๐ถ๐‘˜, which represents a higher fracture toughness of nanocomposite materials with agglomeration, leads to higher bending strengths after the critical nanofiller volume fraction. Therefore, this simple effective flaw model illustrates the correlation between the bending strengths with nanoparticle agglomeration. There is a lack of experimental data for the fracture toughness in nanocomposites with nanofiller agglomerates. This absence of data has restricted us to choosing a matchup of bending strength and fracture toughness values.

The above results can be used as a guide for future nanocomposite designs and development. For example, in case of two nanocomposite systems with the same volume fraction of agglomerated particles, the nanocomposite with one large agglomerate of 100 nanoparticles will fail first in bending before a nanocomposite with 50 small agglomerates of two nanoparticles inside each agglomerate. Therefore, future material processing should be focused on eliminating the largest agglomerates, rather than limiting the nanofiller volume fraction. Meanwhile, small nanofiller agglomerates will lead to high critical nanofiller volume fractions to show mechanical property reduction. In summary, this is an original attempt in understanding the relationship between the nanoparticle agglomeration at a local scale and the corresponding decrease in strengths at a global scale. Sophisticated models considering agglomerate geometries, nanofiller shapes should be developed after this issue receives greater attention.


The authors are grateful to Professors C. M. Lukehart and W. K. Zhong for valuable discussions and collaboration. The authors acknowledge financial support from the National Science Foundation and the Office of Naval Research.


  1. F. T. Fisher, R. D. Bradshaw, and L. C. Brinson, โ€œEffects of nanotube waviness on the modulus of nanotube-reinforced polymers,โ€ Applied Physics Letters, vol. 80, no. 24, p. 4647, 2002. View at: Publisher Site | Google Scholar
  2. G. M. Odegard, T. C. Clancy, and T. S. Gates, โ€œModeling of the mechanical properties of nanoparticle/polymer composites,โ€ Polymer, vol. 46, no. 2, pp. 553โ€“562, 2005. View at: Publisher Site | Google Scholar
  3. L. R. Xu and S. Sengupta, โ€œInterfacial stress transfer and property mismatch in discontinuous nanofiber/nanotube composite materials,โ€ Journal of Nanoscience and Nanotechnology, vol. 5, no. 4, pp. 620โ€“626, 2005. View at: Publisher Site | Google Scholar
  4. M. P. Manoharan, A. Sharma, A. V. Desai, M. A. Haque, C. E. Bakis, and K. W. Wang, โ€œThe interfacial strength of carbon nanofiber epoxy composite using single fiber pullout experiments,โ€ Nanotechnology, vol. 20, no. 29, Article ID 295701, 2009. View at: Publisher Site | Google Scholar
  5. L. R. Xu, L. Li, C. M. Lukehart, and H. Kuai, โ€œMechanical characterization of nanofiber-reinforced composite adhesives,โ€ Journal of Nanoscience and Nanotechnology, vol. 7, no. 7, pp. 2546โ€“2548, 2007. View at: Publisher Site | Google Scholar
  6. E. T. Thostenson, S. Ziaee, and T. W. Chou, โ€œProcessing and electrical properties of carbon nanotube/vinyl ester nanocomposites,โ€ Composites Science and Technology, vol. 69, no. 6, pp. 801โ€“804, 2009. View at: Publisher Site | Google Scholar
  7. R. P. Singh, M. Khait, S. C. Zunjarrao, C. S. Korach, and G. Pandey, โ€œEnvironmental degradation and durability of epoxy-clay nanocomposites,โ€ Journal of Nanomaterials, vol. 2010, Article ID 352746, 13 pages, 2010. View at: Publisher Site | Google Scholar
  8. P. Cortes, I. Sevostianov, and D. J. Valles-Rosales, โ€œMechanical properties of carbon nanotubes reinforced composites: experiment and analytical modeling,โ€ International Journal of Fracture, vol. 161, no. 2, pp. 213โ€“220, 2010. View at: Publisher Site | Google Scholar
  9. M. Avella, M. E. Errico, and E. Martuscelli, โ€œNovel PMMA/CaCO3 nanocomposites abrasion resistant prepared by an in situ polymerization process,โ€ Nano Letters, vol. 1, no. 4, pp. 213โ€“217, 2001. View at: Publisher Site | Google Scholar
  10. X. Li, H. Gao, W. A. Scrivens et al., โ€œStructural and mechanical characterization of nanoclay-reinforced agarose nanocomposites,โ€ Nanotechnology, vol. 16, no. 10, pp. 2020โ€“2029, 2005. View at: Publisher Site | Google Scholar
  11. Y. Zhou, F. Pervin, and S. Jeelani, โ€œEffect vapor grown carbon nanofiber on thermal and mechanical properties of epoxy,โ€ Journal of Materials Science, vol. 42, no. 17, pp. 7544โ€“7553, 2007. View at: Publisher Site | Google Scholar
  12. J. Cho, I. M. Daniel, and D. A. Dikin, โ€œEffects of block copolymer dispersant and nanotube length on reinforcement of carbon/epoxy composites,โ€ Composites Part A, vol. 39, no. 12, pp. 1844โ€“1850, 2008. View at: Publisher Site | Google Scholar
  13. K. A. Narh, L. Jallo, and K. Y. Rhee, โ€œThe effect of carbon nanotube agglomeration on the thermal and mechanical properties of polyethylene oxide,โ€ Polymer Composites, vol. 29, no. 7, pp. 809โ€“817, 2008. View at: Publisher Site | Google Scholar
  14. M. Q. Tran, J. T. Cabral, M. S. P. Shaffer, and A. Bismarck, โ€œDirect measurement of the wetting behavior of individual carbon nanotubes by polymer melts: the key to carbon nanotubeโ€”polymer composites,โ€ Nano Letters, vol. 8, no. 9, pp. 2744โ€“2750, 2008. View at: Publisher Site | Google Scholar
  15. W. Ma, L. Liu, Z. Zhang et al., โ€œHigh-strength composite fibers: realizing true potential of carbon nanotubes in polymer matrix through continuous reticulate architecture and molecular level couplings,โ€ Nano Letters, vol. 9, no. 8, pp. 2855โ€“2861, 2009. View at: Publisher Site | Google Scholar
  16. A. L. Gershon, D. P. Cole, A. K. Kota, and H. A. Bruck, โ€œNanomechanical characterization of dispersion and its effects in nano-enhanced polymers and polymer composites,โ€ Journal of Materials Science, vol. 45, no. 23, pp. 6353โ€“6364, 2010. View at: Publisher Site | Google Scholar
  17. N. A. Siddiqui, E. L. Li, M. L. Sham et al., โ€œTensile strength of glass fibres with carbon nanotube-epoxy nanocomposite coating: effects of CNT morphology and dispersion state,โ€ Composites Part A, vol. 41, no. 4, pp. 539โ€“548, 2010. View at: Publisher Site | Google Scholar
  18. L. R. Xu, V. Bhamidipati, W. H. Zhong et al., โ€œMechanical property characterization of a polymeric nanocomposite reinforced by graphitic nanofibers with reactive linkers,โ€ Journal of Composite Materials, vol. 38, no. 18, pp. 1563โ€“1582, 2004. View at: Publisher Site | Google Scholar
  19. Z. Dehouche, J. Goyette, T. K. Bose, J. Huot, and R. Schulz, โ€œSensitivity of nanocrystalline MgH2-V hydride composite to the carbon monoxide during a long-term cycling,โ€ Nano Letters, vol. 1, no. 4, pp. 175โ€“178, 2001. View at: Publisher Site | Google Scholar
  20. E. J. Podlaha, โ€œSelective electrodeposition of nanoparticulates into metal matrices,โ€ Nano Letters, vol. 1, no. 8, pp. 413โ€“416, 2001. View at: Publisher Site | Google Scholar
  21. M. Kester, Y. Heakal, T. Fox et al., โ€œCalcium phosphate nanocomposite particles for in vitro imaging and encapsulated chemotherapeutic drug delivery to cancer Cells,โ€ Nano Letters, vol. 8, no. 12, pp. 4116โ€“4121, 2008. View at: Publisher Site | Google Scholar
  22. D. Konatham and A. Striolo, โ€œMolecular design of stable graphene nanosheets dispersions,โ€ Nano Letters, vol. 8, no. 12, pp. 4630โ€“4641, 2008. View at: Publisher Site | Google Scholar
  23. D. Lee, Y. X. Gan, X. Chen, and J. W. Kysar, โ€œInfluence of ultrasonic irradiation on the microstructure of Cu/Al2O3, CeO2 nanocomposite thin films during electrocodeposition,โ€ Materials Science and Engineering A, vol. 447, no. 1-2, pp. 209โ€“216, 2007. View at: Publisher Site | Google Scholar
  24. A. K. Subramaniyan and C. T. Sun, โ€œEnhancing compressive strength of unidirectional polymeric composites using nanoclay,โ€ Composites Part A: Applied Science and Manufacturing, vol. 37, no. 12, pp. 2257โ€“2268, 2006. View at: Publisher Site | Google Scholar
  25. A. M. El-Toni, S. Yin, and T. Sato, โ€œSynthesis and silica coating of calcia-doped ceria/mica nanocomposite by seeded polymerization technique,โ€ Applied Surface Science, vol. 252, no. 14, pp. 5063โ€“5070, 2006. View at: Publisher Site | Google Scholar
  26. D. L. Shi, X. Q. Feng, Y. Y. Huang, K. C. Hwang, and H. Gao, โ€œThe effect of nanotube waviness and agglomeration on the elastic property of carbon nanotube-reinforced composites,โ€ Journal of Engineering Materials and Technology, Transactions of the ASME, vol. 126, no. 3, pp. 250โ€“257, 2004. View at: Publisher Site | Google Scholar
  27. L. Berhan and A. M. Sastry, โ€œModeling percolation in high-aspect-ratio fiber systems. I. Soft-core versus hard-core models,โ€ Physical Review E, vol. 75, no. 4, Article ID 041120, 2007. View at: Publisher Site | Google Scholar
  28. A. K. Soh, D.-N. Fang, and Z.-X. Dong, โ€œAnalysis of toughening mechanisms of ZrO2/Nano-SiC ceramic composites,โ€ Journal of Composite Materials, vol. 38, no. 3, pp. 227โ€“241, 2004. View at: Google Scholar
  29. L. R. Xu and A. J. Rosakis, โ€œImpact damage visualization of heterogeneous two-layer materials subjected to low-speed impact,โ€ International Journal of Damage Mechanics, vol. 14, no. 3, pp. 215โ€“233, 2005. View at: Publisher Site | Google Scholar
  30. P. Wang and L. R. Xu, โ€œDynamic interfacial debonding initiation induced by an incident crack,โ€ International Journal of Solids and Structures, vol. 43, no. 21, pp. 6535โ€“6550, 2006. View at: Publisher Site | Google Scholar
  31. T. L. Anderson, Fracture Mechanics, CRC Press, Boca Raton, Fla, USA, 2nd edition, 1995.

Copyright ยฉ 2012 Arun Krishnan and L. Roy Xu. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

More related articles

1233ย Views | 782ย Downloads | 4ย Citations
 PDF  Download Citation  Citation
 Download other formatsMore
 Order printed copiesOrder

Related articles

We are committed to sharing findings related to COVID-19 as quickly and safely as possible. Any author submitting a COVID-19 paper should notify us at to ensure their research is fast-tracked and made available on a preprint server as soon as possible. We will be providing unlimited waivers of publication charges for accepted articles related to COVID-19. Sign up here as a reviewer to help fast-track new submissions.