Conduction mechanisms of silicon oxide/titanium oxide MOS stack structures
Introduction
During the last decades, the dimensions of MOS transistors (MOST) have been continuously scaled down. This reduction has produced the necessity of ultrathin gate dielectric films, with thickness less than 1.2 nm for the sub-100 nm technology node for high performance MOST [1].
It is well known that as the SiO2 film thickness is reduced below 2 nm, several problems appear that limit its use as gate dielectric in MOST [1], [2], [3]. In order to continue with the device scaling, it is necessary to look for alternative gate dielectrics and structures.
Several high-k dielectric materials have been studied as possible candidates for this purpose, although several concerns have not yet been solved. Among them, low interfacial quality and stability [4], [5], as well as the small conduction band offset at silicon/dielectric interface [2], [3] as k increases, are the main problems that make difficult their application.
To avoid these problems, stack structures formed by a SiO2 interfacial layer and a high-k dielectric over it have been proposed as possible candidates with the advantage of a better interface with silicon and a physically thicker overall layer [6], [7], [8], [9]. In this case the equivalent oxide thickness (Teq) can be expressed aswhere and are the thickness and the dielectric constant of the underlying or interfacial SiO2 layer in contact with the silicon substrate. TH-k and kH-k are the thickness and the dielectric constant of the high-k material.
According to (1), if a medium dielectric constant material is used in the stack, for example HfO2 or ZrO2, it will be necessary a very thin high-k layer in order to obtain an Teq below 1.5 nm. In this case, the physical thickness would not be enough to maintain the benefits of high-k dielectrics.
On the other hand, if a higher dielectric constant film is used, the Teq can be reduced even below 1.5 nm, with the benefits of both a good quality SiO2 interfacial film and high-k material. A material such as TiO2, with a dielectric constant between 40 and 100, could be used for this purpose. Its low band offset with Si may not be a problem due to the presence of the interfacial SiO2. To verify this assumption, it is necessary to study the conduction mechanisms and barrier present in these structures, in order to determine their advantages and possibilities, as well as, to improve and control their properties.
Previously we reported stack structures formed by a TiO2 layer on top of a SiO2 layer obtained using room temperature plasma oxidation (RTPO) technique [10], [11]. In this contribution we complement the characterization of stack structures prepared under different conditions and using different reactor types, in order to determine their characteristics and the main conduction mechanism in each case. The expected general behavior and advantages are summarized indicating possible fields of application.
Section snippets
Experiment
The stack structures were prepared on 0.1 Ω cm n-type, (1 0 0) oriented silicon substrate, using RTPO technique as was described previously in [10], [11]. Different structures were made varying the SiO2 and TiO2 film thickness. The SiO2 interfacial films were obtained by RTPO using O2 or N2O as oxidant gases; the TiO2 films were obtained by RTPO using O2, parallel-plate (P-P) and barrel reactors were used to compare the behavior of films with different qualities. The thicknesses of both films were
Conduction mechanism
Fig. 1 shows the band diagram in strong accumulation of a stack structure. An appropriate determination of the conduction mechanisms in MOS structures requires knowledge of the electric field in each dielectric film. If we consider that a positive voltage is applied at the gate, it will produce a band bending across each film as shown in Fig. 1. The gate voltage is expressed aswhere is the voltage across the silicon oxide film, VH-k the voltage across the high-k film, φ
Experimental results
Fig. 2 shows a comparison between the voltage drop across the whole stack and across the each of the dielectric layers for a SiO2/TiO2 stack structure with 1.5/8.5 nm thickness, respectively, calculated according with Eqs. (3), (5), (6).
Fig. 3a and b show typical J–V curves for two different samples fabricated in the barrel reactor, where some dispersion on the measured current can be observed. Fig. 4a and b show typical J–V curves for two different samples were SiO2 interfacial film was
Discussion
As indicated in Table 1, both dielectric films, for samples TiOA to TiOD were processed in a barrel reactor type. The barrel reactor does not reach high vacuum. This feature allows the presence of high density of impurities in the reactor chamber and thus low films quality. For this reason the stack structure obtained seems to have higher trap density and PF become the main conduction mechanism. The barrier height ϕb was always smaller than 0.7 eV. The dynamic dielectric constant of TiO2 has
Conclusions
The main conduction mechanism observed in SiO2/TiO2 MOS stack structures fabricated by RTPO in parallel-plate and barrel reactors was analyzed. It was demonstrated that good quality films, where the main conduction mechanism is thermionic emission through a barrier higher than 0.7 eV, can be obtained when both dielectric films are processed in the P-P reactor for Teq down to 1.2 nm. Considering the values of the measured barrier heights and dynamic permittivity, the current density as function of
Acknowledgements
We want to thank Olga Gallegos and Enriqueta Aguilar for sample preparation. This work was supported by CONACYT Project No. 39708.
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