Journal of Nanomaterials

Journal of Nanomaterials / 2015 / Article

Research Article | Open Access

Volume 2015 |Article ID 809486 |

D. Scarpellini, C. Leonardi, A. Mattoccia, L. Di Giamberardino, P. G. Medaglia, G. Mantini, F. Gatta, E. Giovine, V. Foglietti, C. Falconi, A. Orsini, R. Pizzoferrato, "Solution-Grown Zn/Al Layered Double Hydroxide Nanoplatelets onto Al Thin Films: Fine Control of Position and Lateral Thickness", Journal of Nanomaterials, vol. 2015, Article ID 809486, 8 pages, 2015.

Solution-Grown Zn/Al Layered Double Hydroxide Nanoplatelets onto Al Thin Films: Fine Control of Position and Lateral Thickness

Academic Editor: Joydeep Dutta
Received17 Dec 2014
Revised05 Apr 2015
Accepted05 Apr 2015
Published27 Apr 2015


We have grown nanostructured films of Zn/Al Layered Double Hydroxide (LDH) on different substrates by combining the deposition of an aluminum micropatterned thin layer with a successive one-step room-temperature wet-chemistry process. The resulting LDH film is made of lamellar-like nanoplatelets mainly oriented perpendicular to the substrate. Since the aluminum layer acts as both reactant and seed for the synthesis of the LDH, the growth can be easily confined with submicrometric-level resolution (about ±0.5 μm) by prepatterning the aluminum layer with conventional photolithographic techniques. Moreover, we demonstrate real-time monitoring of the LDH growth process by simply measuring the resistance of the residual aluminum film. If the aluminum layer is thinner than 250 nm, the morphology of LDH nanoplatelets is less regular and their final thickness linearly depends on the initial amount of aluminum. This peculiarity allows accurately controlling the LDH nanoplatelet thickness (with uncertainty of about ±10%) by varying the thickness of the predeposited aluminum film. Since the proposed growth procedure is fully compatible with MEMS/CMOS technology, our results may be useful for the fabrication of micro-/nanodevices.

1. Introduction

Layered Double Hydroxides (LDHs), also known as hydrotalcite-like compounds, are a class of ionic lamellar materials belonging to the group of the anionic clays [14]. As shown in Figure 1, LDHs have a lattice structure composed by the stacking of positively charged brucite-shaped layers, consisting of a divalent metal ion M2+ (e.g., Ca2+, Zn2+, Mg2+, and Ni2+), octahedrally surrounded by six OH hydroxyl groups. The substitution of the M2+ metal with a trivalent M3+ cation gives rise to the periodic repetition of positively charged sheets (lamellas) alternating with charge-counterbalancing ions. Furthermore, depending on the synthesis technique and the used precursors, the net positive charge is compensated by the intercalation of anions (such as hydroxyl groups, nitrates, carbonates, and sulfates) placed in the hydrated interlamellar galleries. Due to this large variety of elements and ions allowed in the crystal, LDHs are a very interesting and rich class of ionic lamellar materials whose general formula may be written as [14]

Most importantly, even quite complex molecules (inorganic or organic compounds, drugs, bioactive molecules, etc.) can be accommodated in the interlamellar template, both during the synthesis itself, with the assembling of a functionalized host-guest LDH composite, and afterwards when the material is surrounded by and can exchange specific species with the environment. Such peculiar features make LDHs very suitable for a number of applications in different fields, ranging from physical/chemical sensors [5, 6] to adsorbents in water purification and liquid waste treatment [7] or catalytic removal of soot and in vehicle engine exhausts [8], including smart composite materials for optical switching/storage [9] and NIR-emitting quantum code [10]. In addition, the guest molecules can be released in the environment when certain conditions are met, which is promising for self-healing protective coatings which can release the corrosion inhibitors only in aggressive environments [11, 12] and catalyst layers in metal-air batteries [13]. As a most fascinating example, intercalating biological anions may result in LDHs acting as nanocages for sophisticated drugs or genetic material to be delivered inside the patient’s body [14].

In such applications, a reliable adhesion of LDH films to different substrates is the first requirement. In addition, tuning of the lamellar and nanostructure dimensions would be most advantageous, in order to control the intercalation and release of guest molecules as well as the real interaction with the environments. Finally, the practical fabrication of functional microdevices would require the control of growth localization at a microscopic level on specific areas, that is, according to predetermined micropatterns. The abovementioned conditions are not met with the usual hydrothermal coprecipitation method [14] for preparation of LDHs. In fact, the addition of a base to a water solution containing the salts of two different metals, M2+ and M3+ of formula (2), causes the precipitation of the metal hydroxides and the formation of LDH anywhere in the solution. Though the nanoscale precipitates can eventually be collected and then deposited on any substrates, achieving a specific pattern and a good adhesion of the precipitated nanostructures is not simple, which is detrimental for practical applications [15].

By using an alternative, simple, one-step technique, two groups [16, 17] first demonstrated the possibility of growing very stable films of LDH well-formed nanoplatelets, in particular Zn/Al LDHs, onto aluminum surfaces by immersing aluminum thick foils in a water solution of zinc nitrate or acetate. Unlike the usual hydrothermal growth, only a single salt is dissolved in the growth solution to provide the divalent metal Zn2+, while the trivalent one (Al3+) is provided by the aluminum foil that thus acts as both reactant and substrate, in this way greatly improving the adhesion. This method was successively extended to LDHs with various compositions, namely, Mg/Al [18], Ni/Al [19], and Cu/Al [20], on different metals such as Al, Zn, Cu, and even Zn-Al alloy [21], thus demonstrating that the growth of LDH nanoplatelets can be achieved on any material that can be coated with Al, Zn, or Cu. Within this framework, we recently achieved [22] the growth of regular LDH nanoplatelets on Al-coated silicon and investigated how the thickness of the reacting aluminum layer influences the morphology, dimensions, and composition of the LDH nanostructures. The sacrificing role of the metal layer was pointed out and we found a lower limit of the coating thickness below which the growth of LDH nanoplatelets is not regular while ZnO nanorods take place due to the stoichiometric unbalance [22].

In this work we take advantage of a predeposited aluminum layer for demonstrating the submicrometric control of both the position (about ±0.5 μm) and the thickness (about ±10%) of the nanoplatelets in a LDH film with a reasonably good adhesion to the substrate by combining the online monitoring of the residual aluminum layer resistance, conventional photolithographic techniques, and wet-chemical growth; the proposed method is general and, as a proof of concept, we show the accurate control of LDH nanoplatelets grown on patterned tracks on different substrates, namely, glass and silicon .

2. Experimental Details

LDH films were grown on different aluminum-coated substrates, namely, BK-7 glass plates obtained from microscope slides, single-crystal silicon of size 10 × 10 mm2 cut from 2′′ wafers (purchased by Siltronix, thickness 500 microns). The aluminum coatings were deposited by using an e-gun evaporator for tilted evaporation (Balzers 510 system) with different values of thickness for each type of substrate: 10, 25, 50, 100, 250, and 300 nm. For the implementation of the aluminum microresistors, the aluminum film was patterned by conventional photolithographic techniques in order to create aluminum microtracks with different aluminum thickness on insulating glass plates of size 20 × 20 mm2. In order to provide an ideally infinite source of aluminum, we directly used as growth substrates aluminum SEM stubs (Agar Scientific G301). After the aluminum layer deposition, as shown in Figure 2, the hydrothermal growth of LDH was carried out by using a nutrient solution composed of a 1 : 1 ratio of zinc nitrate hexahydrate (Zn(NO3)26H2O) and hexamethylenetetramine (C6H12N4) at 5 mM concentration.

Hexamethylenetetramine was used as a pH regulator to control the solution [23] basicity through the hydrolyzation and release of ammonia at high temperature. During the growth, the samples were kept in the middle of the solution bottle, anchored to a 45° tilted Teflon substrate by means of Teflon screws in order to avoid any possible contamination. The growth temperature was fixed at 75°C, while the growth time was varied from 20 minutes to 12 hours. The sample was cooled down both inside the nutrient solution and in ambient atmosphere (without appreciable differences of results) and then washed with acetone and ethanol at room temperature to remove the residuals on the top of the LDH surface.

The crystallinity of deposited LDH was evaluated by X-ray diffraction (XRD) carried out by using a RIGAKU diffractometer equipped with a Cu anode to generate Cu Kα radiation (λ = 1.5406 Å). Each diffraction pattern was collected in the 2θ range of 10–50°, with a step size of 0.05° and a count time of 2.0 s/step. FE-SEM (LEO SUPRA 1250, Oberkochen, Germany) and energy dispersion X-ray spectroscopy (EDS, INCA Energy 300, Oxford Inc., Abingdon, UK) were used to investigate the morphology and elemental composition, respectively.

The resistance measurements were performed by laterally attaching two insulated copper wires to the aluminum thin film with a conductive adhesive silver paste and then covering the contact area with a silicone paste. For the resistance measure, we used an Agilent 34410A multimeter remotely controlled by MATLAB software and USB cable.

3. Results and Discussion

First, we present and discuss our results about the dynamics of formation of the LDH film onto the aluminum thin film by considering the SEM images of Figure 2, taken with different growth times. At an early stage of growth, LDH hexagonal nanoplatelets lay horizontally on the aluminum layer, as shown in Figure 2(a), forming a compact layer of LDH over the substrate surface. It is possible to see the borders between the different already-formed LDH crystals (lighter areas) which are separated by darker channels, possibly corresponding to thinner LDH regions with a greater absorption of electrons. In the top left area of Figure 2(a) one of the LDH hexagonal plates has partially left its horizontal position to rise above the substrate. In the same sample, an area with a more advanced stage of growth can be identified (Figure 2(b)) where many platelets stand completely perpendicular to the surface. This indicates that the nanoplatelets, after detaching from the surface as partial hexagons, begin to grow perpendicular to the surface, likely because of balance of electrostatic forces. The detached LDH platelets are whiter because of their insulating properties and the greater distance from the aluminum layer. Figures 2(c) and 2(d) demonstrate that the LDH thin film takes around 1 hour to reach the typical “cabbage-like” morphology [16, 22, 24, 25], with well-defined lamellar-like nanoplatelets (see Figure 2(c)), and remains substantially unchanged for longer times (Figure 2(d)).

We have also real-time monitored the progressive consumption of the aluminum film, due to the reaction with the nutrient solution and the growth of LDH nanoplatelets, by measuring the electrical resistance of an aluminum microtrack deposited on an insulating glass substrate as a function of the immersion time (see Figure 3). In fact, in contrast with most solution-growth processes, whose real-time monitoring is very challenging [2629], we suggest that the online monitoring of our process is extremely simple and can give a direct insight into the aluminum migration into the LDH film. In fact, the electrical resistivity of the LDH film and of the ions in solutions is much larger than the extremely low resistivity of aluminum; as a result, the value of the total resistance is largely dominated by the residual aluminum layer: .

Therefore, if we consider a constant rate of aluminum-ion migration from the metal thin film to the forming LDH nanoplatelets, it is possible to model the aluminum track resistance according to the following formulas:where is the contact resistance due to the interface between the connecting wires and the aluminum thin film and to the intrinsic resistance of the micron-sized nickel wires entering the growth glass bottle; is the aluminum resistivity; is the initial length of the aluminum track; is its initial width; is its initial thickness; is the assumed constant rate of aluminum depletion; and is the time when the aluminum-ion migration starts. In the last two steps of (2), the lateral consumption of the track is considered negligible compared to the thickness reduction. Furthermore, we supposed that the aluminum resistivity is independent of temperature.

Consistently with the previous results shown in Figure 2, in less than one hour (from minute 21 to about minute 73) the aluminum is exhausted. The final value of 73 minutes is extrapolated by taking the intersection of the blue line with the -axis. The very good fit with a hyperbolic function confirms that the aluminum film is depleted at a constant rate, from the surface down to the substrate, with a regular ion flux from the aluminum track into the LDH nanoplatelets. Interestingly, the dynamics of the depletion process did not change significantly, that is, with variations of parameters within 10%, when monitoring was repeated by doubling the zinc equimolar concentration at 10 mM. As discussed in [29], the ZnO nanorods growth may occur, with the same recipe as the one presently used, only for bath temperatures higher than about 60°C. On the other hand, as previously reported in [30], the LDH nanosheets can already be well formed at temperatures as low as 50°C, thus suggesting that the LDH formation is energetically more favorable. Furthermore, in presence of aluminum, our results consistently show that the LDH growth greatly overcomes the ZnO formation. We also observed that, after about one hour of growth, when the aluminum track has already been consumed, the solution is still almost transparent (i.e., the ZnO formation in solution is also negligible); however, after some more time, the solution starts becoming milky colored because of the formation of ZnO nanostructures.

Next we consider the completely formed LDH which is shown in Figure 4 by SEM microphotographs (at different magnifications) of LDH samples grown for 12 hours onto predeposited aluminum layers with different initial thickness. It is evident that a nanostructured film has grown on the aluminum layer, with the nanoplatelets mostly oriented perpendicular to the surface, so that it exhibits a “cabbage-like” shape very similar to that reported in the literature [16, 24], by using comparable methods on thick aluminum foils, and to that obtained by our group [6, 22] on Al-coated silicon with a coating thickness higher than 25 nm. However, even though in this case enough time is allowed, the limiting factor for the LDH growth is the aluminum content available over the substrate surface even in a low molarity zinc solution. In fact, the nanoplatelets exhibit a planar and well-formed lamellar-like shape, with a thickness greater than 100 nm, only when the original aluminum layer is 300 nm thick at least (see Figure 4(c)). This effect is consistent with previous results [22] showing that the morphological quality of LDH nanostructures increases with the thickness of the aluminum film in the range from 10 to 100 nm. The process can be attributed to the achievement of the zinc/aluminum stoichiometric balance for the whole growth process, so that the LDH nanoplatelets can form with a more regular shape provided that enough aluminum is available.

The present data demonstrate that the nanoplatelet regularity and flatness keep improving with the aluminum thickness beyond 100 nm and very planar nanostructures are formed at thicknesses around 300 nm or higher. Moreover, by statistically measuring the dimensions of the deposited nanostructures we have found that the nanoplatelet thickness shows a strong positive linear correlation with the aluminum thickness in the range from 10 nm to 250 nm, as reported in Figure 4(d). If the aluminum thickness is higher than 300 nm, as in the case of bulk aluminum, the nanoplatelet thickness saturates to a value near 170 nm. This indicates that the depletion of an aluminum layer down to a depth of 250 nm, approximately, is sufficient to complete the growth of LDH flat nanoplatelets through the reaction with a 5 mM Zn-nitrate solution. In presence of a thinner aluminum coating, the LDH growth will stop at an earlier stage of formation, thus resulting in less flat and thinner LDH nanoplatelets. Therefore, this effect allows having a certain control on the nanoplatelet morphology.

X-ray diffraction and EDS provide further confirmations of a (Zn, Al) LDH structure similar to that reported in the literature [16, 24, 3133]. Figure 5(a) shows the XRD spectrum of LDH nanoplatelets completely formed after a one-hour growth time (the same sample as in Figure 2(c)). Two basal reflections, (003) and (006), give evidence of parallel-oriented LDH nanoplatelets (not visible in the SEM image because of being covered by the vertical-oriented nanoplatelets). The (00) reflections, in particular, allow directly determining the lattice parameter , which gives the total thickness of the brucite-like layer plus an interlamellar space. The average value obtained for this sample is close to 22.64 Å, in good agreement with the values reported in literature [1, 16, 24, 3032], also in consideration of the large variability of the interlamellar space, due to the different intercalated anions.

Moreover, the XRD pattern also shows the presence of some () nonbasal reflections (i.e., having ), coming from almost perpendicular-oriented nanoplatelets, which are visible in the SEM images, having the -axis being almost parallel to the substrate (and parallel to the normal versor of Figure 1). By using the -parameter experimentally obtained from symmetrical (00l) reflections, we could calculate the lattice parameter, corresponding to the distance between two metal cations.

Specifically, the peak positions of the nonbasal reflections give a value of lattice parameter with an average value close to 3.062 Å and a very small variance, in excellent agreement with the results reported in the literature for (Zn, Al) LDH [1, 16, 24, 3133]. Figure 5(b) reports the EDS spectrum of a sample at the initial stage of the growth (similar to the one as in Figure 2(a)). The chemical composition gives evidence of a great presence of aluminum (relative to zinc), coming from the underlying aluminum coating. Figure 5(c) shows the EDS of a well-formed sample, that is, with a growth time of 1 hour, with almost perpendicular-oriented nanoplatelets (similar to the one as in Figure 2(c)). In this case, the compositional analysis reveals a Zn : Al ratio close to 3 : 2. An adhesion test was performed using ASTM D3359. The adhesion of the coating obtained was reasonably good, 3B, as rated by the standard.

Finally, we report on the precise spatial localization of the LDH growth allowed by the predeposited aluminum method, since this can be of great importance to engineer micro/nanodevices. As explained in the experimental section, we fabricated a pattern of 16 aluminum microresistors, shown in Figure 6(a), with each microresistor consisting in a serpentine of 16 lines with a 5 μm width and spaced of the same distance (see Figure 6(b)). In this way, we found that, for higher resolution patterning, the initial Al film should be thinner. In fact, Figure 6(c) shows that when LDH grows onto a 300 nm thick aluminum layer, the growth is not restricted within the patterned tracks and the different LDH lines of the serpentine merge together, even though the original pattern is still visible. Conversely, if a much lower initial aluminum thickness is used (see Figure 6(d)), this effect does not take place and the growth is localized within the borders of the aluminum tracks with about ± 0.5 μm precision.

4. Conclusions

We have demonstrated that thewet-chemistry synthesis of LDHs by using reacting aluminum thin coatings deposited on silicon surface enables the growth of dense films of LDH nanoplatelets perpendicularly oriented to the substrate. The nanoplatelets start growing parallel to the substrate surface but in a short time begin to rotate and eventually they align perpendicular to it. We have also found that the final morphology takes less than one hour to be achieved. During this time, the required aluminum is depleted at a constant rate. Moreover, the morphology and, specifically, the thickness of nanoplatelets can be locally tuned by varying the thickness of the predeposited aluminum coating in the range 10–300 nm. In fact, if the original aluminum layer thickness is lower than 250 nm the growth stops before the LDH nanostructures are fully formed, so that the nanoplatelet final thickness and shape are quite independent of the growth time and only linearly depend on the available aluminum thickness. Finally, provided that the aluminum initial thickness is low enough, the accurate localization of growth within the bounds of the aluminum layer can be achieved with an excellent spatial resolution (about ±0.5 μm). Since the presented LDH wet-chemistry recipe is fully compatible with the MEMS/CMOS technology, our results could be relevant for applications to integrated physical/chemical micro/nanodevices.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.


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