Different types of hydrogen fuel cells have been intensively investigated as the effective sources of clean electric energy. Hydrogen is most preferred fuel but direct use of hydrogen in fuel cells meets a number of problems. Hydrogen does not exist naturally and its production, store and transportation meet difficulties. Moreover, hydrogen has a low energy density in comparing with the hydrogen-containing compositions (methanol, ethanol, ammonia etc.). Direct methanol fuel cell (DMFC) with proton conducting polymer membrane (Nafion) is considered as the promising type of fuel cell for small power-supply units. Platinum catalyst on the DMFC anode extracts hydrogen from liquid methanol. This process eliminates the need for fuel reformer for hydrogen production and allows using the methanol solution as a fuel. But DMFC has disadvantage due to moderate operating temperature (about 100˚C) and formation of CO pollutant gas. Moreover, the fabrication of DMFC with organic polymer membrane as proton conductors is not readily integrated with standard micro-fabrication technique that is widely used in production of most electronic devices.

Ammonia (NH₃) containing 17% hydrogen by weight is carbon-free, not explosive, not corrosive, nor highly flammable and it is being considered as a very promising source of hydrogen for fuel cells [1] . Energy density of ammonia (13.6 GJ/m³) is larger than that for hydrogen (3.6 GJ/m³). Ammonia can be produced commercially in large quantities. Ammonia has proven to be problematic for PEM fuel cells with Nafion membrane since both the conductivity of the membrane and the activity of the catalysts are adversely affected by trace ammonia in the fuel cells. Ammonia as hydrogen source was used for solid oxide fuel cells (SOFC). However, direct ammonia solid oxide fuel cell (DASOFC) operating at sufficiently high temperatures (600˚C - 800˚C) has received little attention until now [1] - [5] . It should be noted that the energetic expenses necessary for supporting of high operation temperatures result in a loss in efficiency for the SOFC system as a whole. Possibility of use of nanoporous gold electrode as effective anode catalyst for ammonia borane (AB-NH₃BN₃) oxidation reaction was studied in [5] .

To overcome above disadvantages, we used the nanoporous silicon layer as proton-conducting membrane and TiO₂, Au/TiO₂ or Au films as anode catalyst. Existence of pores with huge surface (up to 800 m²/cm³) determining large ion (proton) conductivity along the pores opens new perspectives for using porous silicon-based structures as hydrogen fuel cells. Porous silicon technology can be integrated into standard silicon micro fabrication processes. Previous studies devoted to fuel cells with the porous silicon membrane have been focused on direct methanol fuel cell [6] [7] sodium borohydride and hydrogen sulphide cells [8] [9] . To best of our knowledge, data on direct ammonia fuel cell with porous silicon electrolyte lack in literature.

This pioneer paper reports on fabrication details, structural and morphological properties of porous silicon and room temperature performance characteristics of new type direct ammonia fuel cell using proton conducting porous silicon membrane and TiO₂, Au/TiO₂ or Au as catalyst.

Porous silicon layers with thickness of 10 - 40 µm and average porosity from 50% to 70% were prepared on n- type monocrystalline (111) Si substrates with resistivity of 1 × 10⁻² Ω∙cm by anodic etching in hydrofluoric- ethanol solution under the white light illumination [9] . For some measurements the PS films were then detached from Si substrate by electro-polishing. The free-standing PS films were characterized by porosity and thickness measurements. The average porosity, i.e. the void fraction in the porous layer was measured by gravimetry technique. Morphological characterizations of the porous silicon surface were performed by scanning electron microscopy (SEM; JSM-5410LV). The crystalline structure of porous silicon layers was studied by X-ray diffraction (XRD) measurements (Pananalitical Diffractometer, Philips, CuK_α1, λ = 0.15406 nm).

The TiO₂/PS/Si cells have been obtained by deposition of thin titanium dioxide film (about of 150 nm) on PS/Si by using Titanium isopropoxide (TTIP)-Ethanol solution and spin coating technique. These structures have been treated at 450˚C for 30 min in air ambient. The Au/PS/Si and Au/TiO₂/PS/Si structures were fabricated by evaporation of a thin Au film onto the PS/Si and TiO₂/PS/Si surface respectively at room temperature by using the electron-beam technique in vacuum of 1.3 × 10⁻³ Pa. The thickness of the deposited Au film was of 150 nm as obtained by the measurements during evaporation with the aid of a deposition controller (Inficon, Leybold). Electrical measurements of fuel cell characteristics were carried out using ammonia solution (NH₃:H₂O) of different concentrations.

The current-voltage characteristics, open-circuit voltage (V_oc) and short-circuit current density (J) of the TiO₂/PS/Si, Au/TiO₂/PS/Si and Au/PS/Si cells were measured at room ambient (300 K, 40% RH) as well as in ammonia solution in measuring cell (300 K). The ammonia-stimulated generation of the open-circuit voltage and short-circuit current between the contacts to Au or TiO₂ film and Si substrate was measured directly by digital multi-meter (Thurlby-1503). The relative humidity of air was measured with hygro-thermometer (Extech- 44470). The photosensitive properties of the investigated cell structures were analyzed by measuring current-voltage characteristics in the dark and in daylight. All the cells exhibited weak photosensitivity and therefore ammonia-stimulated measurements of current-voltage characteristics were performed under daylight conditions.

Figure 1 illustrates the SEM image of the PS, Au/PS and TiO₂/PS surfaces. Here the bright islands and relatively dark regions are the tops of silicon walls and intervals containing no of PS, respectively (Figure 1(a)). The larger dimensions of the bright islands on Au/PS surface than on the PS surface may be caused by 2 - 3 neighboring islands covered by unbroken gold film (Figure 1(b)). SEM image of TiO₂/PS surface is just like to PS surface image (Figure 1(c)). Figure 2 shows the X-ray diffraction patterns of monocrystalline Si substrate and porous silicon layer of 64% porosity. It is seen that the crystalline structure of porous silicon layer is similar to that of nearly perfect monocrystalline Si. Nature of peaks about at 39˚ and 65˚ in silicon can be tentatively attributed to SiC inclusions [10] . Lattice parameter of the porous silicon layer (0.5528 nm) was slightly bigger than that of silicon substrate (0.5456 nm). It can be caused by the lattice deformation of porous silicon.

Figure 3 shows the room temperature current density-voltage characteristics of four different types of structures with ammonia solution (50%) as fuel: 1) Au/TiO₂/Si structure without porous layer; 2) Au/PS/Si and 3) TiO₂/PS/Si cells with porous silicon layer and with single catalyst (Au or TiO₂ respectively) and 4) Au/TiO₂/ PS/Si cell with double catalyst layers. It can be seen clearly from Figure 3 the short circuit current density for (3) TiO₂/PS/Si and (4) Au/TiO₂/PS/Si cells is almost equal. The open circuit voltage for these cells (0.67 and 0.87 V, respectively) is well over than that for Au/PS/Si cell (0.35 V). The Au/TiO₂/Si structure without porous silicon layer (curve 1) is very weakly sensitive to ammonia fuel. Thus the catalytic layer containing TiO₂ plays main role in determining of electrical parameters of cells. Below will be presented mainly results of investigation of electrical characteristics of TiO₂/PS/Si cells with single catalyst layer taking into account theirs nearness to characteristics of Au/TiO₂/PS/Si cells with double catalyst layers and simplicity of technology fabrication of cell with single catalyst TiO₂ film.

The current density-voltage characteristics of TiO₂/PS/Si cell with ammonia for different concentrations at room temperature are presented in Figure 4. It is seen that increase of ammonia concentration in the range 0% - 50% is accompanied by increase of both the open circuit voltage and short circuit current density. Moreover, TiO₂/PS/Si cells produced the electricity (V_oc = 0.63 V, J = 0.8 mA/cm²) with clear water. It should be noted that Au/TiO₂/PS/Si and Au/PS/Si cells also showed characteristics of direct water fuel cell.

Figure 5 shows the performance of the Au/TiO₂/PS/Si and TiO₂/PS/Si cells operating with 50% ammonia solution fuel and the Au/TiO₂/PS/Si cell with water fuel. The maximum power density of the Au/TiO₂/PS/Si and TiO₂/PS/Si cells operating at room temperature are 1.6 mW/cm² and 1.2 mW/cm² respectively. The lower performance of 0.25 mW/cm² was obtained for Au/TiO₂/PS/Si cell with water fuel (Figure 5, curve (3)).

Thus the following experimental results were obtained on investigating the electrical characteristics of porous silicon based fuel cells operating at room temperature with ammonia solution as fuel.

a) The TiO₂/PS/Si, Au/TiO₂/PS/Si and Au/PS/Si cells showed direct ammonia fuel cell properties at room temperature.

b) The open circuit voltage and short-circuit current density of cells increase with increase of ammonia concentration in the range 0% - 50%.

c) Titanium dioxide containing catalysts play the main role in determining of electrical parameters of cells. The electrical parameters of Au/TiO₂/PS/Si and TiO₂/PS/Si cells with ammonia solution as fuel (P = 1.6 mW/cm², V_oc = 0.87 V, J = 3.3 mA/cm² and P = 1.2 mW/cm², V_oc = 0.67 V, J = 3.2 mA/cm² respectively, for 50 % NH₃ fuel) are higher than those for Au/PS/Si cells with only Au catalyst (V_oc = 0.35 V, J = 0.9 mA/cm²).

d) The investigated cells also showed properties of direct water fuel cell at room temperature. The Au/TiO₂/ PS/Si cell generated the electricity (P = 0.25 mW/cm²) with water as fuel.

We suggest that the mechanism of the generation of the electricity in investigated cells is similar to proposed early mechanism generation for Au/PS/Si cell exposed directly hydrogen or hydrogen-containing composition as fuel [9] . Herewith TiO₂, Au/TiO₂ or Au films play the role of the catalytic anode for TiO₂/PS/Si, Au/TiO₂/PS/Si or Au/PS/Si cell respectively. The porous silicon layer acts as proton-conducting membrane and the PS/Si interface which is very imperfect and stressed plays the role of the cathode. Data of Figure 3 and Figure 5 related with best electrical parameters of Au/TiO₂/PS/Si cell in comparing with those for TiO₂/PS/Si and Au/PS/Si cells

one can to comment as result of more efficient hydrogen production from ammonia solution for double Au/TiO₂ catalyst film. Electrochemical reactions proceeding in direct ammonia fuel cell with porous silicon proton-con- ducting can be expressed as [11] :

Electrons and protons formed in the Au/TiO₂, TiO₂ or Au catalyst film pass through the external circuit and PS membrane, respectively, and reach the cathode (PS/Si interface). Here the hydrogen and electron is recombined producing hydrogen molecule which reacts with oxygen to form water molecules.

It is evident that the open circuit voltage produced in Au/TiO₂/PS/Si direct ammonia fuel cell was sufficiently large whereas values of the short circuit current density and thereby the cell performance were lower than those presented for direct ammonia SOFC operating at higher temperatures [2] - [4] . This may be caused (besides low temperature operation of presented porous silicon based cells) also by the low proton-conductivity of porous silicon membrane. It is known that structure of porous silicon is like a sponge or columnar and pore surfaces are covered by silicon hydrides (Si-H) and silicon oxides (Si-O). We suppose that the proton conductivity in PS layer is mainly realized via broken bonds of Si-H. Our estimation value of the proton conductivity of porous silicon layer with use the data on diffusion coefficient of hydrogen in PS [12] gave about 12 - 15 mS/cm which is lower than proton conductivity of Nafion membrane (about 40 mS/cm) which is used in DMFC [13] . The increase of proton conductivity porous silicon membranes and thereby improvement of performance of DAFC can be actualized by using of PS filled with acidic solutions (HCl, H₂SO₄ etc.) to partially oxidize the pore surfaces. We are presently searching for more efficient oxidization of pores surfaces.

Thus, preparation and characterization of novel direct ammonia fuel cell using porous silicon proton conduction membrane, TiO₂ or Au/TiO₂ layer as catalyst and ammonia solution as fuel was demonstrated in this report. The open circuit voltage of 0.87 V and power density of 1.6 mW/cm² were achieved for Au/TiO₂/PS/Si fuel cell operating at room temperature. Moreover, the investigated type of fuel cells generated the electricity also with water as fuel at room temperature. Advantages of investigated direct ammonia fuel cells consist in simplicity of fabrication technology, which can be integrated into standard silicon micro fabrication processes and operation of cells at room temperature. Further improvement of performance of porous silicon based DAFC are still needed for portable applications.

The study was supported by the Research Found (2012-01-01-YL04) of Yildiz Technical University.