C49-C54 Titanium Disilicide (TiSi2)
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Titanium disilicide (TiSi2) is a form of TiSix materials. TiSi2 is a refractory metal silicide commonly applied as interconnects in ultra-large-scale integrated (ULSI) circuits and as gate electrodes in metal–oxide–semiconductor (MOS) transistors [1 - 2] because of its low resistivity, thermal stability and excellent electrical contact properties with silicon [3 - 5]. TiSi2 among the refractory metal silicides shows the lowest resistivity (~12.4 µΩ cm).

Table 150a. Properties of TiSi2 materials.

Thin film resistivity
(μΩ − cm)
Melting point (°C)
Thermal expansion (ppm/°C)
Sintering temperature (°C)
700-900 (high thermal budget)
Stable on Si up to (°C)
Reaction with Al at (°C)
nm of Si consumed per nm of
High Si consumption results in problem in scaling junctions: Not scalable to ultrashallow junctions
nm of resulting silicide per nm of metal
Si consumption (nm Si/nm Silicide)
Barrier height to n-Si (eV)

Table 150b. Comparison of the properties of CoSi2 and TiSi2.



10-25 µΩ/cm

12-24 µΩ/cm

Metal-dopant compound formation


Thermal stability on single crystalline Si
Thermal stability on undoped poly-Si
Thermal expansion
~10 ppm/°C
12 ppm/°C
Mechanical stress
(8-10) x 109 dyne/cm2
(2-2.25) x 1010 dyne/cm2
Si consumption (nm Si/nm Silicide)
Reaction temperature with SiO2
> 1000 °C
700 °C

Dominant diffusion species during silicide formation


Sheet resistance control
Resistivity to dry/wet etching
Native oxide consumption

Thermal stability in the Al/silicide/Si system


Lattice match with Si
Melting point
1325 °C
1540 °C

The TiSi2 formed by solid state reaction of between Ti and Si films has two different structures: the C49 (base-centered orthorhombic) structure formed between 450 °C and 650 °C, and the C54 (face-centered orthorhombic) structure formed above 650 °C. The C49 TiSi2 is a metastable phase and is usually the first crystalline phase to form in the reaction between Ti and Si, while the C54 TiSi2 phase is a stable phase, having a lower electrical resistivity than the C49 phase. Both crystal structures have similar atomic arrangements with a hexagonal array of Si atoms around Ti atoms at the center, but the staking arrangement of the unit cells are different:  the C49 phase has a two-layer repeat while the C54 phase has a four-layer repeat. C54 TiSi2 has orthorhombic structure with lattice parameters of a = 0.8267 nm, b = 0.4800 nm, and c = 0.855 nm and has 24 atoms per unit cell. C49 TiSi2 has lattice parameters of a = 0.3552 nm, b = 1.3759 nm, and c = 0.3506 nm.

The C49–C54 transition temperature increases as the Ti film thickness decreases and varies as a function of substrate orientation [6] and stress
effects [7]. For instance, the phase transition of C49 to C54 TiSi2 occurs between 600 °C and 700 °C for the thick Ti films (e.g. 20 nm thick) on (100) Si wafers, but the transition temperature increases with decrease of the Ti film thickness or for Ti films formed on Si (111) substrates (e.g. for 20 nm thick Ti on Si (111), the transition temperature is between 700 °C and 800 °C). The volume reduction associated with the C49 to C54 irreversible transition is from 2.1% to 6% [11 - 14] depending on the quality of the crystals.

The C49 TiSi2 present an anisotropic thermal expansion coefficients: the αb is considerably smaller than αa and αc because of the presence of
planar defects perpendicular to the large b-axis of the unit-cell [15].

Assuming Ti (titanium) film is first deposited on a Si substrate, the free energy of the system will change if the Ti atoms react with the Si atoms to form titanium silicide (TiSi2) film. To form a TiSi2 layer in thickness t, 0.4t of the Ti film and 0.9t of the Si substrate need to be consumed. Therefore the free energy change ΔG to form the TiSi2 layer is,
          ΔG = A [(G0TiSi2 - 0.4G0Ti - 0.9G0Si)t + γTiSi2+ γTiSi2/Si - γSi] = AΔγ ----------------------------- [150]
          A -- The area of the surface/interface,
          G0TiSi2 -- The volume term of TiSi2,
          G0Ti -- The volume term of Ti,
          G0Si -- The volume term of Si,
          Δγ -- The surface/interface term of the Gibbs free energy change,
          γSi -- The Si substrate surface energy,
          γTiSi2/Si -- The TiSi2/Si interface energy,
          γTiSi2 -- The TiSi2 surface energy.

Note that the driving force for the C49 to C54 transition is the energy differences of G0TiSi2, γTiSi2/Si, and γTiSi2. for the two phases.

Under some conditions, prior to the disilicide formation [8-10], the initial crystalline phase formed during the Ti–Si interaction is a metal-rich silicide (either Ti5Si3 or Ti5Si4). Then, the disilicides form at the expense of the metal-rich silicide at higher annealing temperature.

The TEM images in Figure 150a shows the stacking structures before and after annealing at 900 K. The layers A, B, C, D, and E are capped TiN, deposited Ti, TiSi2, amorphous Si (for (a)) or polycrystalline Si (for (b)), and SiO2, respectively. The as-deposited TiN film has a columnar texture and is preferentially oriented with (111) planes parallel to the surface. After annealing, a TiSi2 layer with mixed C49 (close to the TiN layer) and C54 (close to the polycrystalline Si layer) phases is formed.

TEM images of the stacking structures before and after annealing at 900 K

Figure 150a. TEM images of the stacking structures before (a) and after (b) annealing at 900 K. Adapted from [16]

Figure 150b shows the atomic arrangement of the two TiSi2 crystals C49 and C54. TiSi2 C49 has two Si sites: Si1 and Si2. Si1 is in the form of a two-dimensional hexagonal sheet, while Si2 forms a zigzag chain. In both C49 and C54, only the nearest-neighbor Si–Si bonds are connected.

Crystal structures of C54 and C49 TiSi2

Figure 150b. Crystal structures of TiSi2 C49 and C54. [17]

Figure 150c shows experimental ELNES spectra at the Si-L2,3 edge taken from amorphous, C49, and C54 TiSi2. All the three spectra consist of a small peak located at around 102 eV superposed on a very broad peak. The clear difference between three spectra is the width of the first peak. This peak is sharper in the C54 sample than in the C49 sample, while the amorphous sample is similar to the C49 sample.

Experimental Si-L23 edge ELNES spectra taken from amorphous, C49, and C54 TiSi2

Figure 150c. Experimental Si-L2,3 edge ELNES spectra taken from amorphous, C49, and C54 TiSi2. [17]

Note the experimental ELNES spectra at the Ti-L2,3 edge taken from amorphous, C49, and C54 TiSi2 are very similar.

Figure 150d shows several chemical reactions occurring during annealing of a transistor structure coated with Ti to form a low resistive TiSi2 layer at the source, gate, and drain. When silicon and titanium are reacted, Ti and Si can diffuse laterally over the isolation regions and form thin filaments of TiSix that can electronically connect a gate electrode and source/drain regions and can cause failure of the device. This phenomenon is called "bridging". On the other hand, those by-products (TiSix, TiOx, and TiN) form over the isolation regions and cannot easily be etched in conventional salicide etching solutions. The use of a nitrogen atmosphere during thermal annealing is essential in preventing this failure mechanism [18] because nitrogen quickly diffuses into the grain boundaries and significantly suppresses any long-range silicon diffusion in the titanium layer. Furthermore, to avoid the by-product formation, the annealing temperature cannot be too high.

several chemical reactions occurring during annealing of a transistor structure coated with Ti to form a low resistive SiTi2 layer

Figure 150d. Several chemical reactions occurring during annealing of a transistor structure coated with Ti to form a low resistive TiSi2 layer.

The resistivities of the C49 phase and the C54 phase are very different as shown in Figure 150e so that to form low resistive contacts the phase transformation from C49 to C54 is very important. Figure 150e shows that the resistivity increases because of silicon diffusion into the metal as the temperature is increased from room temperature, while the resistivity reduces abruptly as C49 is formed, followed by further reduction to C54 phase. At temperatures above 900 °C the TiSi2 becomes discontinuous and the resistivity increases due to agglomeration. Therefore, the C54 process window is about 100 °C. On the other hand, the doping, reduced linewidth, and film thicknesses narrows the process window down significantly. Since the transformation is nucleation-limited, the transformation on narrow lines is more difficult. Note that the C54 nucleation density is increased by higher temperature annealing.

Dependence of phase and resistivity on annealing temperature TiSi2

Figure 150e. Dependence of phase and resistivity on annealing temperature.



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