Journal of Materials

Volume 2014 (2014), Article ID 430410, 8 pages

http://dx.doi.org/10.1155/2014/430410

## Fabrication of Thermoelectric Sensor and Cooling Devices Based on Elaborated Bismuth-Telluride Alloy Thin Films

^{1}LMER Laboratory, Faculty of Sciences, University Ibn Zohr, 80001 Agadir, Morocco^{2}LabSIV Laboratory, Faculty of Sciences, University Ibn Zohr, 80001 Agadir, Morocco^{3}Institut d’Electronique de Sud, IES, Equipe Micro-Capteurs, Université Montpellier II (CC 075), Place E. Bataillon, Cedex 05, 34095 Montpellier, France

Received 6 December 2013; Accepted 6 February 2014; Published 10 March 2014

Academic Editor: Ram Gupta

Copyright © 2014 Abdellah Boulouz 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.

#### Abstract

The principal motivation of this work is the development and realization of smart cooling and sensors devices based on the elaborated and characterized semiconducting thermoelectric thin film materials. For the first time, the details design of our sensor and the principal results are published.
Fabrication and characterization of Bi/Sb/Te (BST) semiconducting thin films have been successfully investigated. The best values of Seebeck coefficient (* α*(

*T*)) at room temperature for Bi

_{2}Te

_{3}, and (Bi

_{1−x}Sb

_{x})

_{2}Te

_{3}with

*x*= 0.77 are found to be −220 µV/K and +240 µV/K, respectively. Fabrication and evaluation of performance devices are reported. 2.60°C of cooling of only one Peltier module device for an optimal current of mA is obtained. The values of temperature measured by infrared camera, by simulation, and those measured by the integrated and external thermocouple are reported. A sensitivity of the sensors of 5 mV Torr

^{−1}mW

^{−1}for the pressure sensor has been found with a response time of about 600 ms.

#### 1. Introduction

Thermoelectric microdevices are used in a variety of applications [1–4]. They are used by the military for night vision equipment, electronic equipment cooling, sensors, and portable refrigerators. Thermoelectric modules can also be used as thermocouples for measuring temperature or providing the temperature-sensing element in a thermostat.

The Seebeck effect has two main applications including temperature measurement and power generation [2]. This effect is used for elaboration of thermoelectric cooling and sensor devices. The potential of a material for thermoelectric applications is determined by the figure of merit[2]: whererepresent the Seebeck coefficient,the electrical resistivity, andthe total thermal conductivity whereis the lattice part andis the electronic part [2, 5].

The conversion efficiency of thermoelectric materials can be improved either by lowering their thermal conductivity or by enhancing their capacity for producing electricity.

As known, there are two approaches which can be used for preparing high ZT materials: (1) the multiquantum well structures (MQW) with quantum confinement effects and (2) the concept of reducing lattice thermal conductivity(especially in high temperature applications) in PGEC (phonon glass electron crystal) systems. PGEC systems (e.g., skutterudites based on CoSb_{3}) are studied mainly as bulk materials [6]. The concept of MQW mainly dealt with thin films and superlattices [7–9].

The alloys of bismuth telluride with antimony telluride have attractive properties and are most used in the energy transfer technology and thermoelectric devices at room temperature [3–5, 10, 11]. Some of the electrical and thermoelectrical properties of (Bi_{1-x }Sb_{x})_{2}Te_{3} have been studied [12–16]. The best p-type materials seem to be the Sb-rich thin films of (Bi_{1−x }Sb_{x})_{2}Te_{3}. Thin Films of (Bi_{1−x }Sb_{x})_{2}Te_{3} have been grown by different techniques such as sputtering [17], flash evaporation [18], and molecular beam epitaxy [19]. Venkatasubramanian [7, 8] has reported a high figure of merit ZT of around 2.4 for Bi_{2}Te_{3}/Sb_{2}Te_{3} superlattice devices.

The films of n-type Bi_{2}Te_{3} and p-type Sb_{2}Te_{3} were deposited by thermal coevaporation on thick polyimide (kapton) substrate [1, 20, 21]. Seebeck coefficient values of −190 *μ*V/K and +150 *μ*V/K and electrical resistivity values of 8 *μ*Ω m and 15 *μ*Ω m were measured at room temperature on n-type and p-type films, respectively. These values are better than those reported in the literature for films deposited by cosputtering or electrochemical deposition but not better than those that will be reported for our films deposited by metal-organic chemical vapor deposition. Fan et al. [22] investigated thermoelectric properties of p-type 25% (Bi_{2}Te_{3})-75% (Sb_{2}Te_{3}) prepared via mechanical alloying. (Bi_{0.5}Sb_{0.5})_{2}Te_{3} thin films are also deposited by flash evaporation method and studied by Ganesan and Das [23].

Before design and fabrication of microdevices, we should elaborate thin films with optimal physical properties. So the focus of the present work is firstly the growth by metal organic chemical vapour deposition (MOCVD) with physical characterizations of n-type Bi_{2}Te_{3} and p-type (Bi_{1−x }Sb_{x})_{2}Te_{3} thin films and then their applications to micromodule thermoelectric cooler and microsensors based on an integrated thermocouple with resistance and a variation temperature measurement. For the first time the details design of our sensor is published.

#### 2. Thin Films Characterization and Experimental Details

Binary Bi_{2}Te_{3} and ternary (Bi_{1−x }Sb_{x})_{2}Te_{3} alloys were grown on pyrex substrates, using an MOCVD with horizontal quartz reactor operating at 700 Torr using hydrogen as the carrier gas. The precursors for bismuth (Bi), antimony (Sb), and telluride (Te) were trimethylbismuth (TMBi), triethylantimony (TESb), and diethyltellurium (DETe), respectively.

An X-ray diffractometer Philips, using monochromatic(*λ* = 1.5405 Å), is employed to obtain diffraction patterns. The composition of the deposited films is measured by means of the energy dispersive X-ray (EDX) microanalyser.

The Seebeck coefficient is calculated from the variation of electromotive force with temperature gradient using two probe techniques [24] at room temperature. The measurements of electrical resistivity and Hall effect were done simultaneously using standard Van der Pauw’s technique.

The X-ray diffraction analysis and energy dispersive X-ray spectroscopy show the stoichiometry of the films. Figure 1(a) shows the X-ray diffraction patterns for Bi_{2}Te_{3} grown at different substrate temperatures. We observe the intense lines (0006), (00015), and (00018). In the high substrate temperatures, the only orientation lines (0001) are observed (Table 1) for Bi_{2}Te_{3} films. For °C, the additional lines have been observed ((01015) and (20210)) indicating a different crystalline orientations.

We can say that MOCVD induce growth in the same direction as for a bulk or a film elaborated by Bridgman method. The* c*-parameter of the hexagonal cell founded is* c* = 30.25 Å. These values are compared to those reported for bulk Bi_{2}Te_{3} (*c* = 30.48 Å) (Table 1).

Figure 1(b) shows the X-ray diffractogram of a typical (Bi_{1−x }Sb_{x})_{2}Te_{3} thin film with . The presence of (006), (015), and (110) plans confirms the polycrystalline structure of the thin layers.

The morphology of the sample is presented in Figures 2(a) and 2(b) which indicate several hexagonal forms of the crystallites oriented in perpendicular to the substrate plane.

The scanning electronic microscopy (SEM) micrograph shows distinct crystallites separated by grains boundaries and other crystallites without preferential orientation in the low temperature region. The composition of the deposited Bi_{2}Te_{3} films is measured by means of the EDX micro analyser (Table 2).

The best value of measured Seebeck coefficient at room temperature is around*μ*V/K. The Seebeck coefficient measurements show that all the Bi_{2}Te_{3} samples are of n-type.

Due to the better cracking efficiency and the growth rate of 0.1–0.45 *μ*m/h for the carrier gas flow = 6 slm, the values offound were larger than those obtained for and atm.

The values of thermoelectric power were measured at 300 K for different substrate temperatures growth. The anisotropic thermoelectric characteristics of Bi_{2}Te_{3} system, which has been evaluated on the basis of orientation distribution of the crystallites at high substrate temperature, can explain the high Seebeck coefficient [18]. The optimal temperature growth of Bi_{2}Te_{3} is around 450°C.

We have observed as known that when the carrier concentration increases from 9 × 10^{19} to cm^{−3} the absolute value of Seebeck coefficient decreases from 213 *μ*V/K to 129 *μ*V/K. The optimal value of is around 450°C for elaboration of thin films with a low electrical resistivity and a high Seebeck coefficient. A low value of electrical resistivity of Bi_{2}Te_{3} is 9 *μ*Ωm at °C.

The variation of the Seebeck coefficient and electrical resistivity of (Bi_{1−x }Sb_{x})_{2}Te_{3} thin films as a function of the antimony composition in the layers was performed. It is observed that, for , the thin films showed and n-type behaviour and p-type (Bi_{1−x }Sb_{x})_{2}Te_{3} are grown when . We obtained a value of *μ*V/K for ; this value is in the same order of magnitude with those published on (Bi_{0,5}Sb_{0,5})_{2}Te_{3} [10, 11] and on p-type 75% Sb_{2}Te_{3}-25% Bi_{2}Te_{3} [25]. The same behaviour was observed recently for p-type (Bi, Sb)_{2}Te_{3} alloys prepared by mechanical alloying and plasma activated sintering [16].

The occurrence of a maximum in Seebeck coefficient is followed by a rapid decrease when* x* > 0.70. This is due to the lower value of Sb_{2}Te_{3} Seebeck coefficient (110 *μ*V/K). In the variation range of these properties, this result is better than that obtained by Mzerd et al. [19] for (Bi_{01}Sb_{1,9})_{2}Te_{3} elaborated by MBE.

It is observed that the resistivity decreases with increasing* x* exceeding a minimum value of about 9 *μ*Ωm for . This result is in good agreement with that reported by Caillat et al. [13] on (Bi_{1−x }Sb_{x})_{2}Te_{3} single crystals and Sackda [10] have reported a value of *ρ* = 16 *μ*Ωm for flash evaporated (Bi_{0.5}Sb_{0.5})_{2}Te_{3} thin films. The subsequent decrease in *ρ* reflects the exponential increase in the carrier concentration. The important values of Seebeck coefficient, Hall mobility, electrical resistivity, and carrier concentration for the best and optimal n-type Bi_{2}Te_{3} and p-type Sb_{2}Te_{3} and p-type (Bi_{1−x }Sb_{x})_{2}Te_{3} (for ) films are measured at the room temperature and presented in Table 3.

#### 3. Design and Fabrication of Microdevices Based on Elaborated Films

In order to obtain the high performance thermoelectric cooling and sensors, bismuth telluride is widely used. Thermoelectric devices are widely employed in the microelectronics industry for power generators, cooling infrared detectors, and dissipating the heat generated by microelectronic chips [26–30].

In order to evaluate the efficiency of our elaborated films, we present gas and pressure microsensors and a simple micromodule Peltier using n- and p-type semiconductors based on optimal elaborated Bi_{2}Te_{3} and (Bi_{1-x }Sb_{x})_{2}Te_{3} thin films on kapton substrate with the Ni/Cu contact. Thus n-Bi_{2}Te_{3} and p-(Bi_{1−x }Sb_{x})_{2}Te_{3} basic materials are realised under optimal growth conditions setting in previous sections. The thermal conductivities and of the p-type arm of (Bi_{1-x }Sb_{x})_{2}Te_{3} films and n-type arm of the Bi_{2}Te_{3} films were taken as 1.50 WK^{-1 }m^{−1} [2, 31, 32]. The value of figure of merit is found to be K^{−1} at room temperature. This value is very near to the values reported at room temperature by Rowe [31] for bulk materials. Zou et al. [32] found the value of^{−3} K^{−1} for the thermocouple based on p-type arm of Sb_{2}Te_{3} films and n-type arm of Bi_{2}Te_{3}.

The sensor design that can work as gas detection or pressure sensor is presented in Figure 3. This sensor is composed of a resistor (heating element) and an integrated thermocouple deposited on a thermally isolated membrane. Two complementary masks of nickel are used to make the active thermoelement. For the ohmic contact, the Ni films of 1 *μ*m thickness followed by 1.7 *μ*m Cu films are deposited by DC sputtering.

The films are 0.5 *μ*m thick at a growth temperature of 450°C on a 20 *μ*m kapton thick substrate that acts as the thermal insulator of heating element. As a substrate we have chosen the kapton for its use flexibility and high resistance (low thermal conductivity). Thus the conduction losses are minimised and, because of low heating resistance, losses caused by radiance remain low. Therefore the convection losses are predominant that it is the researched goal to obtain a pressure or gas sensor with a high sensitivity. The electric contacts are made of 0.2 *μ*m sputtered nickel film.

A simple micromodule Peltier cooling device based upon elaborated n-type Bi_{2}Te_{3} and p-type (Bi_{1−x }Sb_{x})_{2}Te_{3} semiconductor films on a polyimide membrane was fabricated using suitable masks. The thickness of deposited films is *μ*m and the lateral size of both films is ( *μ*m *μ*m) (Figure 4). For the ohmic contact, the Ni films of 1 *μ*m thickness followed by 1.7 *μ*m Cu films are deposited by DC sputtering.

Our sensor allows measuring gas concentrations or measuring the pressure by measuring a temperature variation. The principle is based on convective thermal exchange onto the active area of the sensor. The integrated thermocouple measures the temperature of the active area that varies according to the pressure or gas concentration. Therefore, by using as gas sensor, the contact of its hot active area with the gas favours the convection losses which depend on the gas thermal conductivity. The vacuum gauge principle refers to the gas kinetic theory [19]. It has been proved that the convection coefficient* H* is proportional to the pressure in the case of low pressure in the molecular regime. The losses caused by convection when the active area sensor is heated are functions of the pressure: at very low pressure, the losses caused by radiance are predominant, and, if the pressure is increased, losses caused by convection become important. Measuring pressure returns to measuring thermoelectric tension given by the thermocouple.

Figure 5 shows the experimental and measure system which is composed of a reactor where gas and air are mixed and a manometer set on the reactor. Three floodgates that control gas input to realise vacuum in the reactor and two pumps are needed, one pump for a primary vacuum and the other for a secondary vacuum. The sensor is powered by a low frequency generator (BGF). We use the integrated thermocouple to measure the temperature variations of heating resistance.

Three methods were used to measure the temperature of the active part of our sensor by varying the applied current injected into the resistance. We have used a discrete thermocouple, an infrared camera, and the integrated thermocouple. These three means will confirm the reliability of our integrated thermocouple.

#### 4. Test and Evaluation of Thermoelectric Devices

In Figures 6 and 7 we present, respectively, simulation results of theoretical gradient temperature variation and the infrared camera measurement of the temperature variation of the heating part of the sensor for the injected current* I* of 8 mA.

In Figure 8 we reported the values of temperature ( (°C)) obtained by the three means of characterization. We see the weak difference between the values of temperature measured by infrared camera, by simulation, and those measured by the integrated thermocouple.

The good function of this thermocouple is accuracy being verified. The measure obtained by thermocouple on contact with the resistance field presents a difference compared to that of the infrared camera. This difference increases with the heating current. It is due to the heating dissipation that crosses through the thermocouple by conduction. Generally, the rule of variation of the resistance temperature is* I*^{2}. This means the heating by Joule effect of the charge.

In Figure 9 we represent the tension variation of the sensor for different powers of heating. is the thermoelectric tension got by the thermocouple at a pressure value and the tension measure at atmospheric pressure. From to Torr, the resistance changes from the heat caused by thermal radiance. There is no gas in the enclosure and the changes caused by convection are close to zero. The response of sensor in this part is constant. From to 10 Torr, the changes of heat are caused by convection and the coefficient* H* approaches to the Knudsen formula and it is a function of the pressure [33]. From 10 to 760 Torr, the response of the sensor is saturated because the exchanges caused by convection are constants. The similar behavior of variation versus pressure was found by VolkLein and Schnelle in n-Bi_{1−x }Sb_{x} and p-Sb films [34].

Important measurement specifications to consider when to look for gas or pressure sensors include the response time, the flow rate, and the reproducibility. The response time, *τ*, is the amount of time required from the initial variation of the pressure or contact with the gas to the sensors processing the signal.

Figure 10 shows the* V* (mV) voltage variation as function of time using LABVIEW (Laboratory Virtual Instrument Engineering Workbench, distributed by National Instruments):
where at time , and time constant of sensor.

When , (*t * one time constant):
Response time, *τ*, is the time it takes the to reach 63% of its maximum value . We found ms.

Table 4 shows the cooling characteristic, (), of the p-n junction (is the applied current). Here (*I*) = , where () is the temperature at the p-n junction and is the ambient temperature of the ohmic contact at the ends.

The Peltier effect is predominant for an applied current less than 2.50 mA. For an applied current more than mA, the Joule heating phenomena of the n- and p-type materials causes the growth of the measured temperature and then decreases .

In order to reduce thermal convection losses, the maximum cooling was measured at pressure of mbar. We have found the maximum cooling of 2.10°C and 2.60°C, at atmospheric pressure and under vacuum, respectively, with an optimal input current of 2.50 mA. Compared to earlier studies [21, 32], we should note that the same Peltier cooling is obtained with a much lower input current.

Our results are compared to the MMP elaborated by Zou et al. [32] who reported thin film Sb_{2}Te_{3}-Bi_{2}Te_{3} junction based thermocouple fabricated by coevaporation, = 2.00°C, for an input current of 2.50 mA.

#### 5. Conclusion

Fabrication and characterization of Bi-Sb-Te thermoelectric thin film materials are presented and the obtained results are very promising. The reliability of the gas sensor and the pressure sensor, which are obtained using Bi-Sb-Te materials with good thermoelectric characteristics, has been proved. For the pressure sensor, the optimal sensibility is observed for the pressure range to 10 Torr. The response time of the sensor, about 600 ms, does not vary with the injected electric power. Good sensibility is due to high thermoelectric power and the good reproducibility is obtained. A direct measure of the temperature by the integrated thermocouple and low consummation of the electric energy make them interesting for the measure systems powered by battery. Kapton’s low thermal conductivity, good substrate adhesion, and mechanical flexibility make Kapton a good choice for the fabrication of lateral thermoelectric devices.

#### Conflict of Interests

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

#### Acknowledgments

The authors would like thank Pr. André Boyer (IES-France) for allowing the use of all elaborated and measurement systems. They are thankful to him for his advice and for the helpful discussions to accomplish this work.

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