Growth of 1-D TiO<sub>2</sub> Nanowires on Ti and Ti Alloys by Oxidation

Lee, Huyong; Dregia, Suliman; Akbar, Sheikh; Alhoshan, Mansour

doi:https://doi.org/10.1155/2010/503186

Journal of Nanomaterials

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Research Article | Open Access

Volume 2010 | Article ID 503186 | https://doi.org/10.1155/2010/503186

Growth of 1-D TiO₂ Nanowires on Ti and Ti Alloys by Oxidation

Huyong Lee,¹Suliman Dregia,¹Sheikh Akbar,¹and Mansour Alhoshan²

Academic Editor: Zhi Li Xiao

Received27 Jul 2010

Accepted11 Nov 2010

Published20 Dec 2010

Abstract

The growth of titania nanowires by a simple metal oxidation process was investigated for both commercially pure α-Ti and Ti alloys including Ti64 and β-Ti under a limited supply of oxygen. The effects of processing variables including heat treatment temperature, gas flow rate, and process duration on the growth of nanowires were explored. Similarities and differences in the growth of nanowires on pure Ti versus Ti alloys were observed. While the growth window in terms of temperature and flow rate is narrow in pure Ti, the window is much wider in the alloys. However, the trend towards high temperature is similar in all the samples promoting faceted oxide crystal growth rather than nanowires.

1. Introduction

Titanium dioxide (TiO₂) is an important inorganic compound that is widely used as a representative white pigment for plastics, paints, rubbers, cosmetics, man-made fibers, papers, and ceramics. TiO₂ has the highest refractive index which is even greater than diamond. With unique ability to reflect light, TiO₂ is used to impart whiteness, brightness, and opacity to various end-use products.

Recently, new products utilizing photocatalytic properties [1–6] of TiO₂ are being developed around the world, and the relevant market size is projected to grow significantly. TiO₂ has also received considerable attention for chemical sensing applications, especially high temperature gas sensors [7]. Dye-sensitized solar cells [8, 9], anodes of Li-based batteries [10–12], biosensors [13, 14], and biocompatible materials for bone implants [15–17] are also important applications for TiO₂. For these applications, surface area is very important to enhance the chemical and electrical properties, and nanomaterials and nanostructures offer an opportunity to enhance these properties.

To date, chemically synthesized nanoparticles have been generally used to enhance the surface area of TiO₂. More recently, one dimensional (1-D) TiO₂ nanostructures such as nanowires and nanotubes have been developed that provide high surface area, which would guarantee a high density of active sites available for surface reactions. To be able to grow 1-D structures such as nanowires, it is necessary to confine the growth direction to one dimension. This can be accomplished by either physical confinement, such as a template or by chemical adsorption confinements [18]. Literature reports TiO₂ nanostructures produced by template-directed method [19–26], electrospinning [27, 28], photoelectrochemical etching [29, 30], anodization [31–33], and hydrothermal techniques [34, 35].

Widespread utilization of nanostructured TiO₂ is often hindered by the conflicting demands for (i) precise control of fine, well-ordered surface features and (ii) low-cost, rapid mass production. Most wet chemical processes like template-directed synthesis of nanostructure require many chemical steps which increase production costs. In addition, variables such as temperature and pH should be well controlled in each chemical step. Moreover, nanostructured TiO₂ has to possess high crystallinity for most applications. TiO₂ nanotubes/nanowires produced by anodization and electrospinning are amorphous after synthesis. For photocatalytic application, crystallinity is very important since amorphous state provides lots of trap sites at which photogenerated charge carriers recombine. Additional heat treatment required for crystallization of the amorphous phase may lead to collapse of the nanostructure due to sintering and grain growth.

Growth of 1-D nanostructures can occur in many ways. One of the more popular methods is to introduce a constituent species in the gas phase. This gaseous specie then reacts with a material in the solid form, a second constituent specie in the vapor phase, or simply condenses on a surface to create nanostructures. Vapor-phase-assisted growth is one of the most common means for producing nanostructures, often nanowires, on a desired substrate. The vapor phase constituent is a metal as is the case with vapor-solid (VS) and vapor-liquid-solid (VLS) methods.

Two methods are typically used to produce the vaporized metal. The simplest method utilizes the substrate, upon which the nanostructure grows, as the source for the vapor phase. This requires a temperature high enough to produce a sufficient vapor pressure of the material. The vapor phase then condenses onto the substrate on preferential sites allowing for growth to occur. An alternative way to produce the required vapor phase is to utilize a metal source upstream from the substrate. Again, a high temperature is necessary to produce the sufficient vapor pressure to allow for downstream condensation. This method requires a rather large temperature gradient between the vapor source and the target substrate to allow for both vaporization and condensation in the same reaction vessel. While this method has been successfully used to produce nanostructures of SnO₂ and ZnO, this has not been successful for TiO₂ because of low vapor pressure of Ti.

Recent work in the authors’ laboratory has led to the development of a novel and inexpensive technique that creates oriented nanofiber arrays of single-crystal TiO₂ by gas phase reaction with hydrogen [36]. While most 1-D nanostructures are created by deposition or growth [37–39], the TiO₂ nanofibers are created by etching TiO₂ grains by hydrogen-containing species (H₂/N₂ heat treatment). As oxygen from TiO₂ is taken out as H₂O (g), Ti diffuses from the surface to the bulk [40]. We have also developed a method involving H₂/N₂ heat treatment to grow nanofibers of SnO₂ in parts of the sample coated with gold, showing directional growth on grains with crystal facets [41]. The top end of each growing SnO₂ nanofiber contained a gold nanoparticle, with a distinct orientation relation detected at the Au/SnO₂ interface. Solid-state and/or gas phase diffusion paths provided possible mechanisms of mass transport of tin and oxygen from the substrate to the ends of the nanofibers for sustained nanofiber growth. Unlike previous vapor-solid or vapor-liquid-solid processes for forming single crystal SnO₂ nanofibers, this hydrogen-induced surface rearrangement process did not require a separate Sn-O vapor source located upstream of the substrate. More recently, we have developed a process to create nanofibers of TiO₂ on Ti and Ti alloys via the oxidation process under a limited supply of oxygen in an Ar environment. The fiber diameters are in the range of 50–80 nm (controlled by the temperature) and of the length of ~1–10 μm (controlled by the reaction time) [42].

What is common to these structures is that they are created without the use of lithography and involve a gas-phase reaction. Thus, these methods provide an economical way to mass-produce high-surface area ceramic nanostructures that are attached to a substrate. This makes them ideal platforms with catalytic, gas-sensing, electronic, and antimicrobial functions for a variety of chemical manufacturing, environmental, transportation, and biomedical applications. The focus of this paper is on the synthesis of 1-D nano-structured TiO₂ on Ti and Ti alloys using the oxidation process under a limited supply of oxygen (10 s to 100 s of ppm level) similar to that reported in [42]. Ar gas was flown into the furnace from a laboratory grade Ar cylinder. Oxidation-driven nanowire growth of TiO₂ and their applications in electroemission and cell repellence have recently been reported in literature [43–45]. While in these reported cases the oxidation was carried out in an acetone saturated Ar environment, what we report here is a simpler process since it is done in Ar alone.

2. Experimental

Commercially pure Ti (grade 2), Ti64 (grade 5, Ti-6 wt% Al-4 wt% V; Onlinemetals, Seattle, WA), and β-Ti (Ti-5 wt% Al-5 wt% V-5 wt% Mo-3.5 wt% Cr-0.5 wt% Fe; referred to as β-Ti(5-5-5)) bars were used for the experiments. Samples from bars were cut using a diamond cutter (LECO, part number 801-136) and mechanically polished using SiC sand paper. The samples were ultrasonicated for 5 minutes in acetone and methanol and rinsed in DI (deionized) water. The samples were then immersed into a bath of 30 wt% of HCl in DI water for 10 minutes at 80°C to gently remove native oxide layers, and then residual water droplets were blown away by an air gun and dried out for 1 day.

The samples were then inserted into a quartz tube which was placed in a horizontal tube furnace (Lindberg, TF55035A) for gas heat treatments. The tube was first purged with 5% H₂ balanced with Ar gas flown at a rate of 1000 mL/min for 1 hr. Then the temperature of the furnace was raised at 30°C/min and maintained at the target temperature (700–900°C) for a certain time period (6–10 hr) with three different Ar gas flow rates: 200, 500, and 1000 mL/min. The flow rate of Ar was maintained by a manual gas flowmeter, and the oxygen partial pressure in the gas was monitored by an oxygen sensor (CG-1000, AMTEK). The humidity was also monitored by a humidity sensor (HMP234, Vaisala), and the level of the humidity was maintained at approximately 0.5% relative humidity. The value of the oxygen concentration in the Ar gas ranged from 10 s to 100 s of ppm throughout the heat treatment process. The sample was cooled down to room temperature rapidly by air quenching to enhance cooling of the sample and to minimize unnecessary oxidation during cooling.

Field emission scanning electron microscope (FEG-SEM, Model XL-30, Philips) was used to characterize the surface morphology of the metal specimens before and after exposure to the Ar gas treatment. A Sirion SEM (FEG-SEM, Model Sirion, FEI, Oregon) was used for high-resolution observation to detect changes in the surface morphology of the specimens at submicron scales. For the SEM observation, a thin layer of gold was deposited on the heat-treated samples to avoid charging effect.

3. Results and Discussions

3.1. Pure α-Ti

Exposure of pure Ti to Ar gas containing ~ppm of oxygen at a flow rate of 200 mL/min for 8 hours at 600°C resulted in the growth of TiO₂ nanowires. The length of nanowires is in the range of 50 nm to 400 nm as represented in Figure 1. The flow rate was changed to observe its effect on the growth of nanowires. An increase in the flow rate from 200 mL/min to 1000 mL/min caused the disappearance of the nanowires. The effect of the flow rate was more obvious as the temperature for the heat treatment was increased. Higher flow rate and higher temperature promoted growth of faceted oxide crystals and platelets. Hence, the window of high aspect ratio nanowire growth was found to be very narrow in pure Ti, as illustrated in Figure 2. The phase of nanowire in this case as well as all those reported in this paper was confirmed to be rutile by electron diffraction in a TEM.

(a)

(b)

Even though the relationship between the flow rate and the change of morphology on the surface has been reported in literature, there is no clear understanding of the effect in these reports [46–48]. By combining experiments of nanostructure growth by oxidation of Cu foil in combination with computer simulation of the gas flux, Xu et al. [46] showed that in an area of higher flux, a higher oxygen concentration was present which promoted nanowire growth only in these areas. According to Peng and Chen [47], the use of a gas environment containing a lower concentration of oxygen was required for the growth of titania nanowires from pure Ti, which is contradictory to the results of the growth of nanowires from Cu oxidation, but consistent with our observation.

To understand the effect of the flow rate, it is useful to determine the gas flow pattern across the sample. The Reynolds number was calculated to determine the pattern of the gas flow with a reference value of 2100 [49]. Values above 2100 indicate turbulent gas flow while numbers less than 2100 indicate laminar or viscous flow. The calculated Reynolds number for our experiments was ~20 indicating that the gas flow in the quartz tube was laminar. When the flow rate is changed in a laminar flow, the convection layer thickness defined by the following equation also changes: where is the kinematic viscosity of the gas, is the velocity of the gas, and is the distance from the leading edge of the sample. Based on (1), the reaction boundary layer thickness decreases as the flow rate increases. The gas reaction boundary layer thicknesses at flow rates of 200 mL/min and 1000 mL/min, with the center of the sample being 2.5 × 10⁻³ m from the edge, are calculated to be 0.02 m and 0.0089 m, respectively. At a lower flow rate of 200 mL/min, the increased gas reaction layer thickness causes oxygen to transfer slowly to the surface of the substrate, and this slowed oxygen supply preferentially promotes the formation of nanowires over a continuous oxide layer.

3.2. Ti Alloys

Pure Ti (α phase) transforms to β phase at 880°C [50]. There are no pure β-Ti alloys below the transition temperature which do not contain β stabilizers such as V, Mo, and Cr. As a result, separating the impact of stabilizing elements from the β phase in nanofiber formation becomes very complicated. When Ti64 and β-Ti samples were heat treated at 700°C for 8 hr with various flow rates, nanowires were formed all over the surface as shown in Figures 3(a) and 3(b). The difference between Ti64 and β-Ti (5-5-5) is the amount of β phase and chemical compositions. Usually, Ti64 is a mixture of α and β phases with the β phase existing as lamellar structures in the domain of α phase.

(a)

(b)

A change in the flow rate did not show any dramatic effect on the growth of nanowires for both Ti64 and β-Ti (5-5-5). However, the effect of temperature was similar to the general trend observed in α-Ti. While 700°C was found optimum for nanowire growth in the alloys, 800°C produced a mixture of well-faceted crystals and nanowires (Figure 4(a)), and 900°C produced well-faceted equiaxed crystals and platelets (Figure 4(b)) only. This general trend towards high temperature seems to indicate that 1-D growth at low temperature is driven by oxidation reaction anisotropy with preferential growth on certain crystal faces. This anisotropy decreases at higher temperature promoting growth on other surfaces leading to facetted crystals. Details of the growth mechanism will be the focus of another publication.

(a)

(b)

Compared to α-Ti, in Ti alloys the growth window was found to be much wider as illustrated in Figure 5. From these results, it is apparent that samples containing the β phase are much better suited for nanowire formation by the oxidation process.

To identify the dependence of nanowire formation on each phase more clearly, Ti-6.85 wt% Al-1.6 wt% V with a specific microstructure was used for the heat treatment. A schematic diagram of the microstructure of this sample is represented in Figure 6(a). The β phase lies only along the grain boundaries of the α phase. The sample was heat treated at 700°C for 8 hr at a flow rate of 500 mL/min, the results of which are shown in Figures 6(b)-6(c). Nanowire formation was achieved across the sample; however, both the length and density of the nanowires were enhanced at locations containing the β phase.

(a)

(b)

(c)

4. Conclusions

Growth of nanowires was observed on the surfaces of commercially pure α-Ti as well as Ti64 and β-Ti(5-5-5) alloys using a high temperature heat treatment in Ar gas containing ~ppm of oxygen. The growth window in α-Ti was narrow and limited to low temperature (600°C) and low flow rate (200 mL/min). The growth window in Ti64 and β-Ti(5-5-5) alloys was much wider with flow rate having no dramatic effect. In the alloys, while the optimum growth temperature was 700°C, a mixture of nanowires and faceted crystals was produced at 800°C, and 900°C produced faceted equiaxed crystals only. High temperature promoted faceted crystal growth in α-Ti as well. This general trend towards high temperature seems to indicate that 1-D growth at low temperature is driven by oxidation reaction anisotropy with preferential growth on certain crystal faces. This anisotropy decreases at higher temperature promoting growth on other surfaces leading to facetted equiaxed crystals.

Acknowledgment

Publication charges for this paper was paid by King Saud University in Riyadh, Saudi Arabia.

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Copyright © 2010 Huyong Lee et al. 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.

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Journal of Nanomaterials

Growth of 1-D TiO2 Nanowires on Ti and Ti Alloys by Oxidation

Abstract

1. Introduction

2. Experimental

3. Results and Discussions

3.1. Pure α-Ti

3.2. Ti Alloys

4. Conclusions

Acknowledgment

References

Copyright

Growth of 1-D TiO₂ Nanowires on Ti and Ti Alloys by Oxidation