The effect of ethylene glycol on pore arrangement of anodic aluminium oxide prepared by hard anodization.

The influence of the addition of ethylene glycol (EG) on the pore self-ordering process in anodic aluminium oxide (AAO) membranes prepared by hard anodization (HA) was investigated. It was illustrated that EG has a substantial effect on the pore arrangement of AAO, and it was found that a smaller pore size can be obtained with an EG concentration reaching 20 wt% in aqueous electrolyte. The number of estimated defects of AAO increases significantly with an increase in EG concentration to 50 wt%. Excellent ordering of pores was realized when the samples were anodized in the 30 wt%-EG-containing aqueous electrolyte.

Introduction

Anodic aluminium oxide (AAO) has drawn widespread attention due to its well-defined pore architecture and suitable corrosion resistance, thermal stability, hardness, abrasion resistance and insulation properties [1-4]. Meanwhile, as a nano-template or host material, AAO plays an essential role for various surface engineering applications, e.g. molecular separation, catalysis, energy storage, electronics, sensors, drug delivery and template synthesis [5,6], and is a component in a diverse range of nanostructured materials in the form of nanodots, nanowires and nanotubes [7,8].

AAO can be fabricated by hard anodization (HA) in various aqueous electrolytes [8]. The HA process has an advantage of high-speed growth ascribed to the high current density (j) with increased anodizing potential (U). Nevertheless, however, AAO made by the HA process demonstrated severely buckled surfaces with numerous cracks and distorted pores [9-11]. Moreover, the controllability of pore diameter (Dp) and the aspect ratio of nanopores of AAO was also very low.

To solve the problems in the process of HA, organic compounds were added to the aqueous electrolyte, which aimed at prompting the ordered arrangement of AAO [12-15]. Zaraska et al. [12] have reported the results of fabrication of AAO with electrolyte containing different n-alcohols, and showed that alcohol can boost parameter regularity and pore circularity. Besides, Chen et al. [13] used polyethylene glycol (PEG) as a modulator to manipulate pore sizes of AAO. The phenomenon of the presence of PEG in the electrolyte restrained chemical dissolution of alumina (Al) and resulted in smaller pores. Meanwhile, AAO could be fabricated by a non-lithographic approach as reported by Martin et al. [14], which illustrated that EG had the ability to improve parameter regularity and lower the pore diameter of AAO. Recently, the addition of organic compounds in the formation of AAO has received much attention. Vega et al. [4] commented on the preparation of AAO by HA in a renewed electrolyte with different oxalic acid and ethanol concentrations and explained the role of oxalate ions and their limited diffusion through alumina nano-channels from a bulk electrolyte on the basis of a phenomenological model. Furthermore, Norek et al. [15] have also reported a systematic study on the effect of addition of EG to oxalic acid electrolytes for the HA process of Al.

In this paper, the effect of EG concentration on the pore arrangement of AAO produced by HA in oxalic acids is analysed. The results demonstrate that the presence of EG has a significant effect on pore ordering and pore size during the HA process. Simultaneously, the results shed new light on the pore-ordering phenomena during HA.

Experiment

Electro-polished ultrapure aluminium foils (greater than 99.999% Al) were cut into square samples of size 3.3 cm × 3.3 cm. The Al samples were embedded in an insulated loader and served as the anode. The back and edges of the loader were sealed with plastic. Graphite was used as the cathode and the distance between both electrodes was kept constant (approx. 4.5 cm). A 0.3 M oxalic acid solution was used as the electrolyte for all samples. A calculated amount of EG was also added to the solutions with the final EG concentrations being 0, 10, 20, 30, 40 and 50 wt% and labelled as S0, S1, S2, S3, S4 and S5, respectively. The applied starting voltage (Vs) was 60 V and this was increased to the target voltage (Vt) of 120 V at a rate of 0.1 Vs−1 [8]. The reaction temperature was fixed at 0°C. The samples were first anodized at Vs for 10 min. Then, the voltage was raised to Vt and the samples were anodized for another 3 min. The morphology of AAOs was characterized by field-emission scanning electron microscopy (SEM) with images collected from the bottom part of the produced AAOs after wiping and subsequently etching the Al for 55 min in 5 wt% H3PO4 solution at 45°C. The fast Fourier transforms (FFTs) of the SEM images were carried out by WSxM 5.0 [16].

Results and discussion

Figure 1 presents the time-dependent current density (ja) of S0–5 samples. As shown in figure 1a, the changes in ja are divided into three stages. Stage I: the ja decays fast and reaches a minimum in a short time. Subsequently, it increases to a peak in the peak time followed by a slight decrease and then arrives at a stable value (js). This phenomenon can be explained by Liu's current theory on the pore-growth model of AAO [17]. Stage II: firstly, the j elevates due to the increasing voltage with a rise in the transport of ions passing through the barrier layer. Next, it decreases slowly with a large amount of fluctuation. This is because a high voltage creates a thicker barrier [16], and a slight decline in the number of ions passing through the barrier layer results in a smaller current. Stage III: The ja decreases gradually. This is because the level of oxygen ions mostly coming from water decreases in the electrolyte according to the reaction (H2O(l) → O + 2H+(aq) + 2e−) [14]. In the meantime, there is greater volatility, possibly because the heat exchange enhances the velocity of the ions in the local electrolyte.

Figure 1.

The current density versus time curves for the studied samples. (b–d) Larger magnifications of the stages in (a) (I, II and III, respectively).

Figure 1b reveals that the higher EG concentrations lead to lower js. The effect can be explained by the formula [18] where j, F, c, ζ, ε, Ε and η represent the current of ions, the Faraday constant, ionic concentration, zeta potential, dielectric coefficient, electric field strength and the viscosity coefficient, respectively. The reduction of the ε and increase of the η of the electrolyte due to the addition of EG results in the lower js. Meanwhile, the phenomenon that ja rises to a peak value in the peak time disappears as EG is increased because the addition of EG blocks ion diffusion. Figure 1c shows that the process for ja reaching the critical value (ja ≈ 30 mA cm−2) takes more time with increase in EG concentration. The increase of the reaction voltage elevates ja. Furthermore, addition of EG lowers the value of ε/η, promoting decrease in ja for the same applied potential (U). It opens up the possibility for synthesis of AAO by MA (mild anodization) over a wider voltage range in an oxalic acid electrolyte containing EG.

SEM images of the bottom part of the analysed AAO along with their FFTs images are exhibited in figure 2. The FFTs of the lattice present the periodicity of AAO in the inverse scale. An FFT pattern consists of six distinct spots for a perfect triangular lattice. Ring-shaped forms could be observed in the FFT image for the worst lattice. It is shown that EG has an obvious effect on AAO quality. The pore ordering gradually decreases with increase in EG concentration to 20 wt%. In the S2 sample, the hexagonal pore ordering almost disappeared. This is probably because the heat exchange rate lags behind the growth rate of the AAO. However, the pore ordering was improved with EG concentration exceeding 20 wt%. It is likely that the local heat exchange accelerates the dissolution of the pore wall. This reveals that it is necessary to mix EG into the aqueous electrolyte during preparation of AAO by HA, which is a completely new perspective. The pore ordering is also well determined by the FFT rings which form distinct points at the corner of a hexagon for the considerably well-ordered AAO.

Figure 2.

SEM images of the bottom part of the AAO samples along with the FFT images. Scale bars = 1 µm.

The pore diameter (Dp) and the number of estimated defects per given area in accordance with stacking faults in hexagonal pore arrangement are shown in figure 3. One can observe that Dp showed a nonlinear relation with EG concentration. The Dp presents a downward trend for the EG concentration under 20 wt%. It can be explained that the EG molecules play an important role in inhibiting the chemical dissolution of alumina during anodization when the EG concentration is less than 20 wt% [19]. However, the Dp shows a sharp rise when the EG concentration exceeds 20 wt%. There could be two reasons for this. First, it is well known that pore distribution and size are determined by many factors including voltage, electrolyte concentration, reaction temperature, solution viscous flow, etc. The solution viscous flow changes after adding EG with a different mass ratio in the range of 10–50 wt% [20]. In our opinion, viscous flow has a great effect on the internal heat exchange between solution and AAO substrate. It is concluded that the addition of EG produces both the positive factors, such as decreasing permittivity of the electrolyte and inhibition of the chemical dissolution of alumina during anodization, and negative factors, such as slowing down of the heat exchange due to relatively higher solution viscous flow. The Dp rapidly increases as the EG concentration exceeds 20 wt%. This is probably because the effect of heat exchange overshadowed the role of EG that inhibits the chemical dissolution of alumina during anodization; Second, extensive incorporation of soluble and COO− ions into the oxide framework probably favours cleavages and enhances the oxide dissolution rate along the cell boundaries [15].

Figure 3.

The pore diameter (Dp) (a), the number of estimated defects (b) and the scheme demonstrating the determination of percentage of estimated defects (c) for the studied samples.

In figure 3b,c, the number of estimated defects increases slowly for the S0, S1 and S2 samples. However, it dramatically increases as the EG concentration reaches 50 wt%. This is probably because 50 wt% EG added to electrolyte would induce drastic heat exchange.

To better characterize the order degree of AAO, semi-quantitative analysis of the regularity parameter (R) from the FFT's intensity profile was performed [13], which could be represented by the following formula: Here the regularity parameter is defined as the ratio of intensity to the full width at half maximum of the FFT's intensity profile. The corresponding R versus EG concentration is presented in figure 4. Significant growth of R is observed as the EG concentration reaches 30 wt%. Perhaps this is because the heat exchange is in balance with the dissolution of the pore wall. Briefly, we can conclude that the pore ordering is related to the presence of EG.

Figure 4.

Plot of the regularity parameter (R) (a) and scheme demonstrating the intensity profile analysis of the FFT (b) against EG concentration for the studied samples.

Conclusion

In this work, the influence of EG on the pore arrangement of AAO fabricated by HA in oxalic acids was investigated. It was demonstrated that EG has a substantial impact on the pore arrangement in AAO. A long-range ordered AAO can be obtained when the sample is anodized in a 30 wt%-EG-containing oxalic acid electrolyte. Moreover, minimum Dp can be gained with an EG concentration of 20 wt%. The number of estimated defects of AAO increases sharply as the concentration of added EG reaches 50 wt%.