Facile and time-resolved chemical growth of nanoporous Ca x CoO 2 thin films for flexible and thermoelectric applications

CaxCoO2 thin films can be promising for widespread flexible thermoelectric applications in a wide temperature range from room-temperature self-powered wearable applications (by harvesting power from body heat) to energy harvesting from hot surfaces (e.g., hot pipes) if a cost-effective and facile growth technique is developed. Here, we demonstrate a time resolved, facile and ligand-free soft chemical method for the growth of nanoporous Ca0.35CoO2 thin films on sapphire and mica substrates from a water-based precursor ink, composed of in-situ prepared Ca-DMF and Co-DMF complexes. Mica serves as flexible substrate as well as sacrificial layer for film transfer. The grown films are oriented and can sustain bending stress until a bending radius of 15 mm. Despite the presence of nanopores, the power factor of Ca0.35CoO2 film is found to be as high as 0.50 × 10 WmK near room temperature. The present technique, being simple and fast to be potentially suitable for cost-effective industrial upscaling.


able for cost
effective industrial upscaling.

Introduction

Since the discovery of single crystalline Na0.50CoO2 exhibiting a large Seebeck coefficient and low electrical resistivity in 1997 [1] extensive research interests have been paid to develop new layered cobaltates (alias cobalt oxides) of significant thermoelectric (TE) performance.In this regard, Na0.7CoO2 is reported to exhibit a high power factor (PF=S 2 /, where S is the Seebeck coefficient,  is the electrical resistivity) similar to the standard Bi2Te3 [1], however with one drawback that Na0.7CoO2 due to its poor chemical stability cannot offer sustainable performance, particularly, at elevated temperatures.Many sustainable layered cobaltates, such as CaxCoO2 [2,3], SrxCoO2 [4,5] and Ln0.30CoO2 (Ln = La, Pr and Nd) [6,7] have been developed simply by exchanging the Na + ions with other divalent or trivalent cations from NaxCoO2 precursor.Among all, calcium cobaltates (e.g.CaxCoO2 and Ca3Co4O9) has attracted significant interest because of their high TE performance, remarkable thermal and chemical stability and nontoxicity.In particular, thin films of these calcium cobaltates can be promising for flexible applications if the film deposition be possible on flexible substrates or otherwis transferable onto flexible platforms.

Since the thermal conductivity of CaxCoO2 is higher than Ca3Co4O9, the latter has been more investigated for high temperature thermoelectric applications.For high output from a thermoelectric converter, its constituent leg materials need to have high power factor [8].In particular, achieving high power factor is more important than efficiency for low power applications (such as wearable applications).The Ca0.35CoO2 is reported to exhibit a high power factor of 0.9 mWm -1 K -2 at 300 K [9], which is several times higher than the values reported for misfit layered cobaltate Ca3Co4O9 [10][11][12][13][14], and remarkably higher than other layered cobaltates AxCoO [A = Sr, La, Pr, Nd] [4][5][6][7].

Compared to the bulk materials, thin films of these layered cobaltates are advantageous because of their low-dimension, cost-effectiveness and easy integration in different platforms for advanced applications.Although physical deposition techniques have been investigated for the growth of CaxCoO2 thin films [15][16][17] the investigation on chemical solution deposition (CSD) method is still elusive.On the other hand, to address the scalability, chemical growth methods are often preferred over physical methods.Although some investigations have already been done to grow the misfit layered cobaltate thin films by chemical methods [18][19][20], however, with no report on CaxCoO2.Furthermore, the challenges associated with the chemical methods are from the nonuniformity of the films [18] due to the undesired cross-reactions or non-homogenous precipitation.Panchakarla et al. reported the growth of misfit layered Ca3Co4O9 nanotubes by base-treatment of pre-formulated calcium cobalt oxide [21] but the process seems to be complicated to obtain thin films.The growth of high quality thin film of misfit layered cobaltate has been accomplished using a water-based solutions containing the co-ordinate complex of metal ions with EDTA (ethylenediaminetetraacetic acid) and PEI (polyethileneimine) [20].However, the processing of the complex-solution remains tedious and time consuming.Therefore, development of alternative strategies is imperative to produce good quality CaxCoO2 thin films in a facile and time-resolved process that also allow their easy integration in multiple modules.Here, we demonstrate a ligand-free water-based CSD method for the growth of Ca0.35CoO2 thin films on sapphire and flexible mica substrate.Muscovite mica, because of its inherently layered structure, where aluminosilicate layers are loosely bound by the boundary layer of potassium (K+) ions, can serve as the flexible substrate [22].Furthermore, it can sustain high processing temperature of 700 ⁰C.The film growth technique being simple and low cost is potentially suitable for industrial upscaling.TE performance of the films is characterized in terms of their power factor.The nanoporous structure of the film is found not to affect its power factor, however, the presence of pores of nanometer length-scale in the film can be expected to reduce thermal conductivity of the film as co

also nonhazardous [35] and recyclable.


Formulati
n of DMF-complexes with Ca 2+ and Co 2+

In this work, hydrated acetate salts of Ca 2+ (Ca(CH3COO)2.H2O) and Co 2+ (Co(CH3COO)2.H2O) were taken as the precursor mat rials which were easily soluble in DMF.

The DMF complexes of the metal ions namely, Ca 2+ -DMF and Co 2+ -DMF were prepared simply by adding the salts separately in a molar ratio 3:4 into the excess DMF, followed by stirring for 30 min at 60°C.After cooling at room temperature white precipitate of Ca 2+ -DMF and violet precipitate of Co 2+ -DMF appeared (as shown in Figure 1 (a)), which were reprecipitated (for 4-times) from hot DMF.Here, the precursor salts and

MF were procured from Sigma Aldrich.


Formu
ation of precursor thermoelectric ink

The precipitates were mixed together by dissolving in excess of DMF followed by stirring for 1 hour at 90°C.After cooling at room temperature, a purple color precipitate was obtained (as shown in Figure 1) which was re-precipitated from hot DMF (for 4-times) to remove the unwanted impurities.After washing with ether, the precipitate was dried at 60 °C to obtain a pink brown color precursor solid (as shown in extreme left of Figure 1(b)), which was easily soluble in de-ionized (DI) water to obtain a stable homogenous solution of bluish precursor in

having solid content of 10mg/mL.


Fab
ication of thermoelectric samples

For the investigation thin films of Ca0.35CoO2 were grown by CSD method on sapphire and mica substrates.The ink was simply drop-casted onto the top-surfaces of cleaned substrates and heated to 700°C for 10 min in ambient condition.Subsequently, black-colored thin film of Ca0.35

O2 appeared on th
substrates.


Characterization

The crystal structure and morphology of the films were characterized by θ -2θ XRD analyses using monochromatic Cu Kα radiation (λ = 1.5406Å) and scanning electron microscopy (SEM, LEO 1550 Gemini).The θ-2θ XRD scans were performed with a Philips PW 1820 diffractometer.Compositional analyses of the films were performed by energy dispersive Xray spectroscopy (EDS) with an accuracy of ±5%.In-plane electrical resistivity and Seebeck coefficient were simultaneously measured as a function of temperature using an ULVAC-RIKO ZEM3 system.


Results and Discussion

Figure 1 shows the different steps for the growth of Ca0.35CoO2 thin-films on mica and sapphire substrates, which is partly discussed before in the experimental section.Figure 1(a) and (b) show the step-by-step formulation of the water-based precursor thermoelectric ink from the corresponding solid mixture of Ca 2+ -and Co 2+ -DMF complexes.The DMF-complexes of the metal ions have been formulated by adding their acetate salts (i.e., Ca-acetate and Co-acetate) in hot (60 ⁰C) DMF followed by cooling at room temperature.The DMF is a highly susceptible material to form complexes with the metal ions through its amide functionality (as schematically shown in Figure 1 (a)).Although, the precursor salts are soluble in hot DMF, the precipitation was observed during cooling at room temperature, which is indicative to the formation of DMF-complexes of Ca 2+ and Co 2+ .During formation of the DMF-complexes, there is a possibility of partial substitution of the acetate ions (-COOCH3 -) by the DMF.Consequently, the DMF-complexes are thought to behave like zwitterions.During mixing of the DMF-complexes in excess DMF with heating and vigorous stirring, the zwitterions electrostatically interacts each other, resulting in formation of electrostatical

balanced precipitate o
the complex-conjugates, which was dried to obtain the pink brown precursor solid (as shown in Figure 1 (b)).Because of abundant ionic characteristics of the solid, it likely to be s luble in polar solvent.Water being the most environment friendly polar solvent, here, we have demonstrated the formulation of highly stable (stability was noticed for 60 days) aqueous thermoelectric ink.

The aqueous solution was drop-casted on two different substrates, sapphire and mica (Figure 1(b)).After heat treatment at 700 C in ambient atmosphere, dark films were obtained.

The Ca0.35CoO2 film on mica substrate was found to be more uniform as compared that on sapphire substrate.This is because, angle of contact between solution and hydrophilic mica [36,37] is much smaller than between solution and sapphire, which results in uniform spreading of the solution over mica substrate.The formation of Ca0.35CoO2 thin films was repeatedly observed.During mixing of the DMF-complexes under vigorous stirring, the Co 2+ -DMF complex (because of its smaller size) will occupy within the interstitial spaces of Ca 2+ -DMF through the favorable electrostatic interaction among the active groups in the periphery of metal ions, resulting in-situ electrically and stoichiometrically balanced thermoelectric precursor solid (i.e., Ca 2+ /Co 2+ -DMF mixed complex).During heat treatment, the coordinated DMF reduces the Co 2+ to Co 0 nanoparticles, which in presence of abundant oxygen transforms to CoO2.Plausible reaction mechanism is shown in Scheme 1.On application of elevated temperature in air, the DMF degrades to produce H2O, CO2, N2, NOx, etc., resulting porosity in the film [38,39].Ca 2+ -DMF is ionized at high temperature and forms Ca0.35CoO2.The peaks from no other planes, except (00l) planes of Ca0.35CoO2 indicate the c-axis orientation of both the films.Apart from Ca0.35CoO2, the peaks from mica and sapphire substrates are also visible in Figure 2 (a) and (b) respectively.The d-spa ing for both the films is calculated to be 5.437 Å, which nearly matches with the value reported elsewhere [40].Seemingly flat surface of both the films is attributed to the out-of-plane orientation of the film, which is in consistent with the observation by XRD.The growth of oriented films on both the substrates is intrinsically attributed to the effect of self-assembly during annealing, where the driving force is the external stress due to solvent evaporation [41].The higher porosity of Ca0.35CoO2 film on mica substrate as compared to that on sapphire substrate might be due to the slow evaporation of the surface absorbed water in the more hygroscopic mica during the formation of the film from the precursor ink [42].

From the above study it is conjectured that the present CSD method can be applicable to grow Ca0.35CoO2 thin films on arbitrary substrates, who sustain high annealing temperature 700 ⁰C.The porosity of the films can also be controlled by preferential selection of the substrate with desired hygroscopic properties.nm on mica substrate (25 µm thickness).The film is bendable to a bending radius of 15 mm without developing any crack in the film, as confirmed by optical microscopy.In Figure 4 (b) the transferability of the film is demonstrated by transferring the film from the parent mica substrate onto a sticky tape.The top surface of the film is first adhered to a sticky tape and then the film is transferred by stripping, i.e. the mica substrate can act as sacrificial layer.

Figure 5 (a) shows temperature dependent electrical resistivity of Ca0.35CoO2 films on sapphire (red circles) and mica (black open circles) substrates.The room temperature resistivity values are 15.6, and 14.6 mΩcm for the films Ca0.35CoO2-on-sapphire, and Ca0.35CoO2-onmica, respectively, which higher than the values for Ca0.35CoO2 reported elsewhere [16,43], however, comparable to the reported values for undoped Ca3Co4O9 thin films [44,45].Even with nanoporous structure the electrical resistivity of Ca0.35CoO2-on-mica is slightly lower than the film Ca0.35CoO2-on-sapphire, which is attributed to the better crystalline quality of former than later.This is apparent that the nanopores in the film Ca0.35CoO2-on-mica do not act as scattering centre for the charge carriers, which might be due to the higher interpore separation than the electroni mean free path.However, thermal conductivity of the film is anticipated to be reduced, due to the enhanced scattering of phonons by nanopores.This anticipation is since the phononic mean free path is one order of magnitude higher than the electronic mean free path, and by controlling the characteristic length scale of the nanoporous structure within the range of electronic and phononic mean free path the phonons can be selectively scattered, but without hampering the electronic transport [23,46].Figure 4 (b) shows the temperature dependent Seebeck coefficient of the films.The room temperature S ebeck coefficient values are 78 and 88 µV/K for the films Ca0.35CoO2-on-sapphire, and Ca0.35CoO2-on-mica, respectively, which are comparable to the value reported for single crystalline Ca0.33CoO2 [9], however, sufficiently higher than sputter deposited CaxCoO2 thin films reported elsewhere [16].

The Seebeck coefficient varies with temperature in a similar manner as electrical resistivity.

Figure 4c shows the temperature dependent power factor of the grown films.The room temperature power factor values are 0.39 an

0.50 × 10 -4
Wm -1 K -2 for the film Ca0.35CoO2-onsapphire, and Ca0.35CoO2-on-mica, respectively, which are interestingly comparable to the reported values for undoped Ca3Co4O9 thin films [44,45].The slightly higher power factor of the film Ca0.35CoO2-on-mica as compared to Ca0.35CoO2-on-sapphire, is attributed to the reduced electrical resistivity of the former than later.

To investigate the effect of bending stress on thermoelectric performance the film Ca0.35CoO2on-mica was subjected to repeated bending, 100 times, and then Seebeck measurements were performed.No notable changes in the values of Seebeck coefficient and electrical resistivity were found; whatever little variation in the values are within the error limit specified for the measuring instrument.It is noteworthy that the present films are undoped and further improvement of power factor is still possible upon doping.


Conclusions

We have demonstrated a facile and eco-friendly chemical route to prepare the aqueous thermoelectric precursor ink for the growth of Co0.35CoO2 thin films on sapphire and mica substrates.The growth of nanoporous Co0.35CoO2 thin film has been realized, following the steps of drop casting of precursor ink and then annealing at 700 ⁰C for only 10 min in air.The film deposition is expected to be possible on arbitrary substrates, who sustain high annealing temperature 700 ⁰C.The formation of nanopores in t e film is attributed to the degradation of DMF, producing H2O, CO2, N2, NOx, etc., during the heat treatment.The higher porosity of the film Co0.35CoO2-on-mica as compared to the film Co0.35CoO2-on-sapphire is attributed to the slow evaporation of the surface absorbed water in the more hygroscopic mica during the growth of the film.It is anticipated that the control over the porosity of the films is possible by preferential selection of substrates with desired hygroscopic properties.Despite the high porosity the power factor of the fi