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1Mechanosynthesis Group, Department of Mechanical Engineering, University of Michigan, 2IMEC, Belgium
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We present methods for fabrication of patterned microstructures of vertically aligned carbon nanotubes (CNTs), and their use as master molds for production of polymer microstructures with organized nanoscale surface texture. The CNT forests are densified by condensation of solvent onto the substrate, which significantly increases their packing density and enables self-directed formation of 3D shapes.
Copic, D., Park, S. J., Tawfick, S., De Volder, M., Hart, A. J. Fabrication, Densification, and Replica Molding of 3D Carbon Nanotube Microstructures. J. Vis. Exp. (65), e3980, doi:10.3791/3980 (2012).
The introduction of new materials and processes to microfabrication has, in large part, enabled many important advances in microsystems, lab-on-a-chip devices, and their applications. In particular, capabilities for cost-effective fabrication of polymer microstructures were transformed by the advent of soft lithography and other micromolding techniques 1, 2, and this led a revolution in applications of microfabrication to biomedical engineering and biology. Nevertheless, it remains challenging to fabricate microstructures with well-defined nanoscale surface textures, and to fabricate arbitrary 3D shapes at the micro-scale. Robustness of master molds and maintenance of shape integrity is especially important to achieve high fidelity replication of complex structures and preserving their nanoscale surface texture. The combination of hierarchical textures, and heterogeneous shapes, is a profound challenge to existing microfabrication methods that largely rely upon top-down etching using fixed mask templates. On the other hand, the bottom-up synthesis of nanostructures such as nanotubes and nanowires can offer new capabilities to microfabrication, in particular by taking advantage of the collective self-organization of nanostructures, and local control of their growth behavior with respect to microfabricated patterns.
Our goal is to introduce vertically aligned carbon nanotubes (CNTs), which we refer to as CNT "forests", as a new microfabrication material. We present details of a suite of related methods recently developed by our group: fabrication of CNT forest microstructures by thermal CVD from lithographically patterned catalyst thin films; self-directed elastocapillary densification of CNT microstructures; and replica molding of polymer microstructures using CNT composite master molds. In particular, our work shows that self-directed capillary densification ("capillary forming"), which is performed by condensation of a solvent onto the substrate with CNT microstructures, significantly increases the packing density of CNTs. This process enables directed transformation of vertical CNT microstructures into straight, inclined, and twisted shapes, which have robust mechanical properties exceeding those of typical microfabrication polymers. This in turn enables formation of nanocomposite CNT master molds by capillary-driven infiltration of polymers. The replica structures exhibit the anisotropic nanoscale texture of the aligned CNTs, and can have walls with sub-micron thickness and aspect ratios exceeding 50:1. Integration of CNT microstructures in fabrication offers further opportunity to exploit the electrical and thermal properties of CNTs, and diverse capabilities for chemical and biochemical functionalization 3.
1. Catalyst Patterning
2. CNT Growth
3. CNT Densification
4. CNT Master Mold Fabrication
5. Replica Molding
6. Representative Results
Representative as-grown CNT pillar arrays along with their densified shapes are shown in Figure 4 (image modified from De Volder et al. 4). HAR pillars with thicknesses of 10μm or smaller have progressively reduced straightness, which is further reduced during densification. Densification of semicircular pillars has been shown to result in uniform bent pillars over large areas (Fig. 4c). SU-8 infiltration occurs in between and inside CNT microstructures, for structures with spacing of 30μm or below a thin film of SU-8 may remain between structures. Photographs of critical steps in the replication process are shown in Figure 5, while SEM images comparing the replicated microstructures to their replicas on various scales are shown in Figure 6 (image modified from Copic et al. 5). Current limits, in terms of structure formation, including twisted structures (image modified from De Volder et al. 4), high aspect ratio walls, and re-entrant structures are shown in Figure 7 (image modified from Copic et al. 5).
Figure 1. Tube furnace setup for growth CNT growth. (a) System schematic. (b) Tube furnace (Thermo-Fisher Minimite), with cover open to show silicon boat inside sealed quartz tube. (c) Silicon boat with samples, shown before and after growth. Click here to view larger figure.
Figure 2. (a) Schematic of beaker setup for controlled condensation of solvent vapor onto CNT microstructures (image modified from De Volder et al. 6). (b) CNT sample substrate attached to aluminum mesh over boiling acetone.
Figure 3. Process flow for replica molding of CNT microstructures, and image of representative replicated microstructure array compared to U.S. quarter dollar coin.
Figure 4. Exemplary CNT microstructures before and after capillary forming. Schematic and SEM images of array of cylindrical CNT pillars (a) before capillary forming, and (b) after capillary forming (image modified from De Volder et al. 6). Insets show alignment and density of CNTs. (c) Semicylindrical CNT pillars densify and tilt during capillary forming, forming inclined beams (image modified from Zhao et al. 7). Click here to view larger figure.
Figure 5. Key steps of CNT negative mold fabrication and replica casting. (a) Casting of PDMS negative mold. (b) Degassing of the negative mold. (c) Manual demolding of the negative, and casting of the SU-8 replica.
Figure 6. Comparison of (a) CNT/SU-8 master and (b) replica micropillar structures showing high fidelity replication of micro-scale shape and nanoscale texture (i.e., sidewalls and top surface), over a large area (image modified from Copic et al. 5). Click here to view larger figure.
Figure 7. High-aspect-ratio (HAR) and re-entrant CNT microstructures and their polymer replicas. (a) Densified CNT honeycomb with corresponding SU8-CNT master and SU8 replica. (b) Master and replica of sloped CNT microwell (image modified from Copic et al. 5). (c) Densified twisted CNT micropillars, with master and replica of individual structure (image modified from De Volder et al. 4). The honeycombs in (a) have wall width of 400 nm and height of 20 μm. Click here to view larger figure.
Lithographic patterning and preparation of the CNT catalyst substrates is straightforward and repeatable; however, achieving consistent CNT growth requires careful attention to how the height and density of CNT forests are impacted by the ambient humidity and the condition of the growth tube. In our experience, patterns larger than 1000 μm2 are less sensitive to small fluctuations in the processing conditions. Further, the density of the patterns plays affects the growth density and height8. The growth density and height are larger for patterns with fill fraction (total area of catalyst divided by total substrate area) greater than approximately 20%. Also, it is important vital to keep the growth tube clean and bake out the tube between consecutive growths to remove accumulated carbon deposits. Tube baking is performed by heating the tube for 30 minutes at 875°C with 100 sccm of air flow. Furthermore, the CNT growth rate depends on the temperature, gas composition, and residence time of the gas in the furnace. Thus, it is often necessary to empirically find the "sweetspot" in any growth system, and the placement of the samples in the procedure noted here is based the sweetspot for our tube furnace and process parameters.
The most important properties of our CNT forests for densification and subsequent master mold formation are their alignment, packing density, and adhesion to the substrate. When CNT microstructures are etched by brief exposure to oxygen plasma, the top "crust" of tangled CNTs is removed. This crust constrains the CNT forest laterally, and therefore removing the crust enables greater densification of the CNTs, and increases the amount of slip that occurs among the CNTs during the densification step. Also, the CNT diameter can be tuned by the catalyst film thickness, and by the annealing conditions that precede injection of the hydrocarbon source to the CVD furnace 9. By tuning the annealing conditions and optionally etching the CNTs, we have tuned to the densification factor from approximately 5X to 30X 6. And, the adhesion of the CNTs to the substrate is enhanced by rapidly cooling the substrates in the growth atmosphere immediately after the conclusion of the programmed growth time. In this case, the furnace is enclosure is opened and the heater power is turned off while the growth gas mixture is still flowing through the furnace tube. These details are discussed thoroughly in our other publications cited herein.
In order to achieve consistent CNT densification, one must avoid excessive solvent condensation on the substrate. Excessive condensation causes the CNT structures to be flooded, which can warp, flatten, or delaminate HAR microstructures. The required amount of condensation to fully densify the CNTs depends on both the height and density of the microstructures. In our practice, the amount of solvent condensation is monitored by counting the number of "waves" of solvent that sweep across the substrate. The colorful waves represent optical interference patterns due to the thin film of condensed liquid on the substrate. For typical microstructures with dimensions 10-100 μm, between 1 and 5 waves are required in our setup. Therefore, the amount of solvent in the beaker may be chosen accordingly, or the sample may be removed from the beaker after the desired number of waves has passed.
Master mold formation is highly dependent on SU-8 infiltration and the formation of the SU-8-CNT nanocomposite. SU-8 infiltration is easily achievable due to the wetting of the CNTs by the SU-8. Selection of the SU-8 viscosity and spin speeds determines the SU-8 volume fraction and the smoothness of the sidewalls of the master structure. SU-8 wicks into the individual CNT structures and, depending on the spacing between the structures, may also wick in the spaces between the CNT structures. This may result in a thin film of SU-8 remaining in between closely spaced structures, and the thickness of this film can be tuned by selecting SU-8 viscosity and spin speed. The stated spin speeds result in fully infiltrated structures with heights ranging from 10 to 300μm and with aspect ratios from 0.2 to 20. These process conditions preserve the surface texture of the CNT structures, i.e., the sidewalls and top surfaces do not bulge outward with excess SU-8.
Vacuum casting of the PDMS negative is a robust process and depends on the initial monomer to cross-linker ratio and the curing conditions. A ratio of 10:1 monomer:cross-linker is used for most castings; however, casting HAR structures (AR>10) with high yield or reentrant structures remains challenging. HAR structures require a mix ratio of 8:1 due to the increased stiffness and reduced adhesion of the negative. A demolding agent, such as fluorinated silane 10, may be used to further reduce the separation force required, minimizing the stress on the master microstructures during demolding and greatly increasing yield. When casting replicas, degassing is not necessary due to the prolonged baking. Degassing was found to lead to inconsistent replication, due to non-uniform evaporation of SU-8 solvent.
The main advantage of the CNT master technology is the ability to form robust master features with hierarchical textures, high aspect ratios, and sloped or curved shapes. However, this requires careful tuning of the CNT growth conditions to achieve uniform and consistent starting patterns, practical mastery of the capillary forming step, and implementation of the SU-8 infiltration and replication steps to give high-fidelity copies of the master shapes. The exact parameters may vary depending on the geometry of the desired structures, and may not be understood until many iterative trials are performed. In addition, because the amount of densification due to capillary forming depends on the density and straightness of the CNTs, prediction of the exact dimensions of the densified CNT structures will require calibration experiments to determine the densification factor. Nevertheless, our method may have important advantages if hierarchically textured and/or 3D polymer features are desired, and/or if the enhanced properties of the CNT structures (at any endpoint in the process) are desired. These enhanced properties could include the mechanical robustness, thermal or electrical conductivity of the master structures, or any like properties of the CNT features themselves.
In conclusion, we have shown a versatile process to precisely form heterogeneous CNT microstructures using capillary forming, infiltrate them, and subsequently replicate them in SU-8. In our previous work we have shown a 25-fold replication sequence is possible without any damage to the negative or fidelity reduction in the replicas 5. Because our process is based on replica molding to cast replicas a variety of materials could be used in the future instead of SU-8 including PU, PMMA, PDMS, and even low temperature metals. Other CNT growth procedures and structures made from other nanoscale filaments (e.g., inorganic nanowires, biofilaments) could potentially serve as the framework of novel master mold architectures as well.
No conflicts of interest declared.
This research was supported by the Nanomanufacturing program of the National Science Foundation (CMMI-0927634). Davor Copic was supported in part by the Rackham Merit Fellowship Program at the University of Michigan. Sameh Tawfick acknowledges partial support from the Rackham Predoctoral Fellowship. Michael De Volder was supported by the Belgian Fund for Scientific Research - Flanders (FWO). Microfabrication was performed at the Lurie Nanofabrication Facility (LNF), which is a member of the National Nanotechnology Infrastructure Network; and electron microscopy was performed at the Michigan Electron Microbeam Analysis Laboratory (EMAL).
|4" diameter <100> silicon wafers coated with SiO2 (300 nm)||Silicon Quest||Custom|
|Positive photoresist||MicroChem||SPR 220-3.0|
|Developer||AZ Electronic Materials USA Corp.||AZ 300 MIF|
|Sputtering system||Kurt J. Lesker||Lab 18||Sputtering system for catalyst deposition|
|Thermo-Fisher Minimite||Fisher Scientific||TF55030A||Tube furnace for CNT growth|
|Quartz tube||Technical Glass Products||Custom||22 mm ID × 25 mm OD 30" length|
|Helium gas||PurityPlus||He (PrePurified 300)|
|Hydrogen gas||PurityPlus||H2 (PrePurified 300)||UHP|
|Ethylene gas||PurityPlus||C2H4 (PrePurified 300)||UHP|
|Perforated aluminum sheet||McMaster-Carr||9232T221||For holding sample above densification beaker|
|UV flood lamp||Dymax||Model 2000|
|SU-8 2002||MicroChem||SU-8 2002|
|Polydimethylsiloxane (PDMS)||Dow Corning||Sylgard 184 Silicone Elastomer Kit|
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