Patent Application
20110160346
The present invention relates in general to composite materials, and in particular, to composite materials that include carbon nanotubes.
All boats whether they are constructed from ferro-cement, steel, glass fiber, or wood, require good protection from the harsh environment in which they reside, e.g., salt water. A coating system is a selection of adhesives and the order in which they are applied to the boat hull to offer this protection. Typically, this consists of a sealing coat to seal and prime the natural hull surface, followed by several barrier coats to keep the water out, and topped off with an antifouling coating designed to keep the hull free of weeds and barnacles. Most hull types have problems with their coating systems of one sort or other; ferro-cement hulls are no exception. Epoxy coatings are extremely tough, durable, and highly resistant to chemicals, abrasion, moisture, and alcohol. Epoxy coatings are widely used as antifouling coating for marine vessels, such as boats, ships, yachts, etc. They can be applied to different marine surfaces such as wood, metal (e.g., aluminum) or alloy, or glass fiber composite, with good adhesion.
However, current adhesive systems, including epoxy adhesions for coating of marine vessels, have serious short and long term problems for protection purposes. Sooner or later, the adhesion of the antifouling paint with the marine hull is weakened, as well as a performance downturn from a rough, uneven surface. For example, the marine hull will expand or shrink at different temperatures in water, which will cause it to crack or blister. As long as a crack initiates, it can easily propagate and grow, eventually damaging the coatings. New antifouling coatings need to be applied after the damaged coating is removed and cleaned. Not only is it expensive to remove and clean the antifouling coating, but the process is very complicated, expensive, and time consuming. Furthermore, the antifouling coating is not strong enough to prevent damage when it is removed using a cleaning process, such as brushing.
Nanocomposites are composite materials that contain particles in the size range of 1-100 nm. These materials bring into play the submicron structural properties of molecules. These particles such as clay and carbon nanotubes (CNTs) generally have excellent properties, a high aspect ratio and a layered structure that maximizes bonding between the polymer and particles.
Adding a small quantity of these additives (0.5-5%) can increase many of the properties of polymer materials, including higher strength, greater rigidity, high heat resistance, higher ultraviolet (UV) resistance, lower water absorption rate, lower gas permeation rate, and other improved properties (see, T. D. Forties, D. L. Hunter, and D. R. Paul, “Nylon-6 nanocomposites from Alkylammonium-modified clay: The role of Alkyl tails on exfoliation,” Macromolecules 37, 1793-1798 (2004)).
However, dispersion of the nanoparticles is very important to reinforce polymer matrix nanocomposites. Up to now, dispersion of those nanoparticles in a polymer matrix has been a problem. Conventional dispersion methods such as ball milling, ultrasonication, and monogenization are not effective ways to disperse the particles. For example, a ball milling process takes a very long time to disperse the particles. Moreover, the particles are broken rather than dispersed. The energy of the ultrasonication process is not enough to disperse carbon nanotube ropes or layered clay particles. That is why those nanoparticle-reinforced nanocomposites do not achieve excellent properties as expected (see, Shamal K. Mhetre, Yong K. Kim, Steven B. Warner, Prabir Phaneshwar Katangur, and Autumn Dhanote, “Nanocomposites with functionalized carbon nanotubes,” Mat. Res. Soc. Symp. Proc. Vol. 788, L11.17.1-6 (2004); Chun-ki Lam, Kin-tak Lau, Hoi-yan Cheung, Hang-yin Ling, “Effect of ultrasound sonication in nanoclay clusters of nanoclay/epoxy composites,” Materials Letters 59, 1369-13722005)).
However, dispersion of the nanoparticles is very important to reinforce polymer matrix nanocomposites. Up to now, dispersion of those nanoparticles has been a problem in the polymer matrix. Conventional dispersion methods such as ball milling, ultrasonication, and monogenization are not effective ways to disperse the particles. For example, ball milling processes have been using for a century, but it takes a very long time to disperse the particles. Moreover, the particles are rather more broken than dispersed. The energy of the ultrasonication process is not enough to disperse the carbon nanotube ropes or layered clay particles. That is why those nanoparticle-reinforced nanocomposites do not achieve excellent properties as expected (see, Shamal K. Mhetre, Yong K. Kim, Steven B. Warner, Prabir Phaneshwar Katangur, and Autumn Dhanote, “Nanocomposites with functionalized carbon nanotubes,” Mat. Res. Soc. Symp. Proc. Vol. 788, L11.17.1-6 (2004); Chun-ki Lam, Kin-tak Lau, Hoi-yan Cheung, Hang-yin Ling, “Effect of ultrasound sonication in nanoclay clusters of nanoclay/epoxy composites,” Materials Letters 59, 1369-1372 (2005)). Researches also studied the ways to reduce the crack propagation and growth of the polymer matrix using CNT reinforcement. It showed that the crack growth rate can be significantly reduced by (1) reducing the nanotube diameter, (2) increasing the nanotube length, and (3) improving the nanotube dispersion (see, W. Zhang, R. C. Picu, and N. Koratkar, “The effect of carbon nanotube dimensions and dispersion on the fatigue behavior of epoxy nanocomposites,” Nanotechnology 19, 285709 (2008).
Using CNTs as a reinforcing component in polymer composites also requires the ability to tailor the nature of the CNT walls in order to control the interfacial interactions between the CNTs and the polymer chains to improve the mechanical properties (see, A. Romov, S. Dittmer, J. Svensson, O. A. Nerushev, S. A. Perez-Garcia, L. Licea-Jimenez, R. Rychwalshi, and E. E. B. Campbell, Journal of Materials Chemistry 15, 3334 (2005)). These interactions govern the load-transfer efficiency from the polymer to the CNTs and hence the reinforcement efficiency. Studies showed that strong interfacial bonding is critical to improve stiffness and strength of the CNT-reinforced composites (see, Erik T. Thostenson, Zhifeng Ren, Tsu-Wei Chou, “Advances in the science and technology of carbon nanotubes and their composites: a review,” Composites Science and Technology 61, 1899-1912 (2000)).
Therefore, it is very important to improve the mechanical properties of the epoxy adhesive as an antifouling coating to improve the crack propagation resistance, so that it will not be easily damaged, the lifetime of the coating will be extended, and the maintenance cost will be lowered. Embodiments of the present invention improve mechanical properties of CNT-reinforced polymer matrix nanocomposites by utilizing the following steps, significantly improving the crack propagation resistance:
The following examples are described.
DWNTs were obtained from Nanocyl, Inc., Namur, Belgium (Nanocyl-2100 product series). The DWNTs had an average outer diameter of 3.5 nm and lengths of 1-10 μm. The DWNTs were produced via a catalytic carbon vapor deposition (CCVD) process, though other processes could be utilized. CNTs collected from the reactor were then purified to greater than 90% carbon by the manufacturer. MWNTs were obtained from Mitsui Co., Japan and other vendors. The MWNTs were highly purified (>95% purity). Epon 828 epoxy resin and hardener (dicyandiamide) used to cure the epoxy were obtained from Mitsubishi Corporation, Japan.
The purified DWNTs and MWNTs were first put through an oxidation process by placing them in a 3:1 HNO3/H2SO4 solution. The DWNTs and MWNTs in the solution were sonicated in an ultrasonic bath flow. The oxidation process resulted in functionalization of the DWNTs and MWNTs with a carboxylic functional group (—COOH) on the CNT surfaces. The CNTs were cleaned using de-ionized water and filtered using a 2 μM mesh Teflon thin film filter under a vacuum. The CNTs collected from the Teflon thin film were dried under vacuum in preparation for epoxy nanocomposite fabrication. The COOH-functionalized DWNTs were further functionalized with a NH2-group utilizing a wet chemical process (see, Z. Konya, I. Vesselenyi. K. Niesz, A. Kukovesz, A. Demortier, A. Fonseca, J. Delhalle, Z. Mekalif, J. B. Nagy, A. A. Koos, Z. Osvath, A. Kocsonya, L. P. Biro, I. Kiricsi, Chemical Physics Letters 360, 429 (2002)).
Referring to
Epon 828 resin was then added in step 304 in the CNT/acetone gel at ratios needed for sample preparation (305). In step 306, the mixing process may use a stirrer at 70° C. for half an hour at a speed of 1000 rev/min to produce a suspension on 307 followed by an ultrasonication process in step 308 to evaporate the acetone and disperse the DWNTs in the epoxy matrix (309). The hardener (dicyandiamide) was then added in step 310 into the mixture at a ratio of 4.5 wt. % and mixed by stirring at 70° C. for 1 hour to produce an epoxy/CNT/hardener gel (311). The mixture was degassed in step 312 in a vacuum oven at 70° C. for 2-48 hours. In step 313, the mixture was then poured into a release agent-coated Teflon mold and cured at 160° C. for 2 hours in step 314. The specimens were polished in step 315 using fine sandpaper to create flat and smooth surfaces for ASTM evaluation.
In this study, neat, non-functionalized, COOH-functionalized DWNTs, COOH-functionalized MWNTs, and NH2-functionalized DWNT reinforced epoxy nanocomposites were synthesized for comparison.
An MTS Servo Hydraulic test system (capacity 22 kips) was used for 3-point bending testing for flexural strength and modulus evaluation (based on ASTM D790). It was also used for compression strength testing (ASTM E9). Impact strength was tested based on ASTM D256. Vibration damping was tested based on ASTM E756.
A Hitachi S4800 FEI XL50 High Resolution SEM/STEM system was used for SEM imaging of the fracture surfaces of both reinforced epoxy nanocomposites.
Table 1 shows mechanical properties of the CNT-reinforced (both D T and MWNT) epoxy nanocomposites compared with an epoxy neat sample.
From the results in Table 1, one can conclude that proper functionalization of DWNTs has a great effect on the flexural strength of the epoxy nanocomposites. Compared with the neat epoxy, improvement of flexural strength was 3%, 18%, and 33%, respectively, for the non-functionalized, COOH-functionalized and NH2-functionalized DWNT-reinforced epoxy nanocomposites at 1.2 wt. % loading. At NH2-DWNT loading of 1.80 wt. %, compression strength, flexural strength, modulus, impact strength, and vibration damping factors were improved 39%, 42%, 16%, 31%, and 44%, respectively, compared with the neat epoxy. Further improvement may be seen by increasing the loading of the NH2-DWNTs; however, the viscosity of the epoxy becomes higher with increasing loading of the DWNTs. The heightened viscosity makes higher loading of the CNTs impractical for epoxy nanocomposite fabrication.
The results in Table 1 show that the NH2-DWNT reinforced epoxy nanocomposite is more effective for the improvement of the mechanical properties of the epoxy matrix than COOH-DWNT reinforced epoxy nanocomposites. NH2-functional groups located on the surface of the DWNTs react and form covalent bonds with the epoxy matrix, and as a result, significantly enhance the interfacial adhesion. The NH2-functional groups are terminated at the open end of the DWNTs. As a result, the DWNTs can be integrated easily into the epoxy matrix via a reaction with the epoxy, and consequently become an integral part of the matrix structure (see, J. Zhu, H. Peng, F. Rodriguez-Macias, J. L. Margrave, V. N. Khabashesku, A. M. Imam, K. Lozano, and E. V. Barrera, Advanced Functional Materials 14, 643 (2004)).
As for the COOH-CNT reinforced epoxy nanocomposites, the surface of the DWNTs affects the wettability between the surface of CNTs and the matrix. It is very possible that the COOH-CNTs are hydrophilic to the epoxy matrix after the functionalization, which improves their dispersion in the epoxy matrix (see, J. Zhu, H. Peng, F. Rodriguez-Macias, J. L. Margrave, V. N. Khabashesku, A. M. Imam, K. Lozano, and E. V. Barrera, Advanced Functional Materials 14, 643 (2004)). The COOH-functional groups attached onto the CNTs offer an opportunity for chemical interactions with the epoxy matrix and enhanced mechanical properties.
This application for patent is a continuation-in-part application of U.S. patent application Ser. No. 11/757,272, which claims priority to U.S. Provisional Patent Application Ser. Nos. 60/819,319 and 60/810,394, and which is a continuation-in-part of U.S. patent application Ser. No. 11/693,454, which claims priority to U.S. Provisional Application Ser. Nos. 60/788,234 and 60/810,394, and which is a continuation-in-part of U.S. patent application Ser. No. 11/695,877, which claims priority to U.S. Provisional Application Ser. Nos. 60/789,300 and 60/810,394, all of which are hereby incorporated by reference herein.
| Number | Date | Country | |
|---|---|---|---|
| 60819319 | Jul 2006 | US | |
| 60810394 | Jun 2006 | US | |
| 60788234 | Mar 2006 | US | |
| 60810394 | Jun 2006 | US | |
| 60789300 | Apr 2006 | US | |
| 60810394 | Jun 2006 | US |
| Number | Date | Country | |
|---|---|---|---|
| Parent | 11757272 | Jun 2007 | US |
| Child | 13040085 | US | |
| Parent | 11693454 | Mar 2007 | US |
| Child | 11757272 | US | |
| Parent | 11695877 | Apr 2007 | US |
| Child | 11757272 | US |
