# Metal work-function-dependent barrier height of Ni contacts with metal-embedded nanoparticles to 4H-SiC

- Min-Seok Kang†
^{1}, - Jung-Joon Ahn†
^{1}, - Kyoung-Sook Moon†
^{2}and - Sang-Mo Koo†
^{1}Email author

**7**:75

https://doi.org/10.1186/1556-276X-7-75

© Kang et al; licensee Springer. 2012

**Received: **15 July 2011

**Accepted: **13 January 2012

**Published: **13 January 2012

## Abstract

Metal, typically gold [Au], nanoparticles [NPs] embedded in a capping metal contact layer onto silicon carbide [SiC] are considered to have practical applications in changing the barrier height of the original contacts. Here, we demonstrate the use of silver [Ag] NPs to effectively lower the barrier height of the electrical contacts to 4H-SiC. It has been shown that the barrier height of the fabricated SiC diode structures (Ni with embedded Ag-NPs) has significantly reduced by 0.11 eV and 0.18 eV with respect to the samples with Au-NPs and the reference samples, respectively. The experimental results have also been compared with both an analytic model based on Tung's theory and physics-based two-dimensional numerical simulations.

## Introduction

Recently, silicon carbide [SiC] has been proposed as the material of choice especially for power electronic and sensing devices operating under high temperature, fast switching, and high-power conditions mainly due to its wide bandgap (3.26 eV), high critical electric field (2.2 × 10^{6} V/cm), superior thermal conductivity (4.9 W/Kcm), and high bulk electron mobility (900 cm^{2}/Vs) of the 4H polytype [1, 2]. For stable operations at high power densities and elevated temperatures, SiC diodes, including Schottky barrier diodes and junction barrier Schottky diodes, as well as SiC transistors, have been under extensive exploration with great improvements in wafer growth technology and device process.

In order to realize stable SiC devices, metal contacts to SiC with suitable physical and electrical characteristics are required. For example, Ohmic contacts with low contact resistances and Schottky contacts with controlled barrier height (*Φ*_{B}) between SiC and metal are among the most important factors for determining the performance of SiC devices [3–5]. Furthermore, electrical characteristics of devices, such as voltage drop and switching speed of such devices, are dependent on the current transport behavior through the structure of the metal/4H-SiC interface. It is, therefore, of critical importance to reduce the barrier height of the metal/4H-SiC interface in order to improve the on-state voltage drop in 4H-SiC devices.

To date, extensive studies have been carried out on the properties of barrier height of various metals on n- and p-types for SiC [6, 7], and many attempts have been made to modify the contact barrier height on SiC. The effect of inhomogeneities and Fermi-level pinning on Schottky contact properties has been known to be minimal, and the barrier height depends mostly on the metal work function without strong Fermi-level pinning for SiC [4, 5]. Recent work on the electrical contacts to SiC includes the implementation of nanostructures such as metal nanoparticles [NPs] to modify the barrier height at metal-SiC interfaces and to alter fundamental SiC device properties by controlling the size of the metal NPs. Previous results in the literature have been primarily focused on the effect of size reduction of NPs on the characteristics of diode structures with embedded NPs, which experimentally investigates the change in transport properties of metal/semiconductor interfaces in SiC depending on the size of NPs [5–10]. However, so far, the focus has been mainly on the scaling effect of the NPs rather than on altering the electrical barrier of the NPs.

In this work, we demonstrate that the work function change in the embedded metal NPs can effectively control the barrier height change of the SiC diode structures. Our results show that incorporating NPs with a larger work function difference to the capping metal layer results in an improved barrier lowering by further enhancing the local electric field. The experimental results have also been compared with both an analytic model based on Tung's theory [11–13] and physics-based two-dimensional numerical simulations.

## Experimental details

*N*

_{D}= 1 × 10

^{16}cm

^{-3}) grown on an n+ substrate (

*N*

_{D}= 1 × 10

^{19}cm

^{-3}). A large area Ohmic contact on the back was formed by e-beam evaporation of a 100-nm-thick Ni film, followed by a rapid thermal annealing process at 950°C in N

_{2}for 90 s [14]. After the samples were cleaned in H

_{2}SO

_{4}:H

_{2}O

_{2}= 4:1, the native oxide was removed by a BOE dip. A thin layer (10 nm) of metal film (Au and Ag, respectively) was then deposited on the front side of the samples by e-beam evaporation, and the samples were annealed in a quartz tube furnace at 500°C for 20 min to induce the formation and growth of the metal NPs [15, 16]. As a capping layer, a 100-nm-thick Ni film was deposited on the front side of the samples to form macroscopic circular patterns with an area of 3.14 × 10

^{-2}cm

^{2}. We then obtained macroscopic Ni/SiC diodes with embedded NPs with different metal work function values from the capping metal/4H-SiC interface. Note that the bulk work function differences along Ni-Au and Ni-Ag are Δ

*Φ*

_{B(Ni-Au)}which is 0.21 eV and Δ

*Φ*

_{B(Ni-Ag)}which is 0.84 eV, respectively [17, 18]. The device structures studied in this work are basically Ni/SiC contacts embedded with the metal NPs to the 4H-SiC substrate. Figure 1 shows the fabricated samples with metal NPs: Ni/SiC contacts embedded with the Au-NPs (NP-1) and Ni/SiC contacts embedded with the Ag-NPs (NP-2). Note that control samples (Ref) were also prepared for comparison by sputtering a 100-nm-thick Ni directly onto the SiC substrate without the NPs. Table 1 summarizes all the different sets of fabricated samples and process conditions.

Summary of all the different sets of fabricated samples and process conditions

Sample | NPs | Capping layer | < 2R> (nm) | σ (nm) | NP Annealing |
---|---|---|---|---|---|

Ref | - | Ni | - | - | - |

NP-1 | Au | Ni | 40.5 | 11.7 | 500°C, 20 min |

NP-2 | Ag | Ni | 36.1 | 10.3 | 500°C, 20 min |

The barrier height and ideality factor were compared with the physical distribution condition of the NPs as determined by field emission scanning electron microscopy [FE-SEM]. To investigate the effect of the NPs at the Ni/SiC interface on the electrical properties, current-voltage [*I-V*] and capacitance-voltage [*C-V*] characteristics of the devices were measured by using a Keithley 4200 semiconductor parameter analyzer (Keithley Instruments Inc., Cleveland, OH, USA). The experimental results have also been compared with an analytic model based on Tung's theory [11–13] and further verified by considering band diagram and electric field distribution using a physics-based two-dimensional numerical simulator Atlas (Silvaco Inc., Santa Clara, CA, USA) [19].

## Results and discussion

*R*>), with a standard deviation [

*σ*]. The average diameters of the Au and Ag NPs were 40.5 nm with a

*σ*of 11.7 nm and 36.1 nm with a

*σ*of 10.3 nm, respectively. It is noticeable in Figure 2 that the difference of the NPs' sizes compared to the NP-1 sample and NP-2 sample was rather small (below 6%).

*J-V*] characteristics of the as-deposited Ni contacts and samples with different embedded NPs. From

*I-V*measurements, the saturation current density, effective ideality factor, and effective barrier height can be extracted in a plot of ln (

*J*)-

*V*characteristics. According to the thermionic emission model, the

*J-V*characteristics are given by [20, 21] the following equations:

where *J*_{s} is the saturation current density, *Φ*_{B} is the effective barrier height [*Φ*_{B} = *kT*/*e* ln(*A***T*^{2}/*J*_{s})], *A** is the Richard constant (for 4H-SiC, 146 A/cm^{2} K^{2}) [22], *T* is the absolute temperature, *k* is the Boltzman constant, *q* is the electron charge, and *n* is the ideality factor [*n = kT*/*e*(*dV*/*d*(ln*J*))]. The values of the effective ideality factor and barrier height were calculated from the ln (*J*) versus forward voltage *V* characteristics. Under forward voltage conditions, it clearly shows that the current value of sample NP-2 was about one order of magnitude higher than that of reference samples (10^{-3} A/cm^{2}), due to the smaller barrier height of NP-2 (0.87 eV) compared with that of Ref (1.04 eV).

*C-V*measurements was extracted as well for comparison with the

*I-V*measurements. The doping concentration (

*N*

_{D}) of the epilayers can be determined from the slope in plotting 1/

*C*

^{ 2 }versus the reverse voltage, which can be expressed as follows [23]:

*A*is the contact area of the diode (3.14 × 10

^{-2}cm

^{2}),

*K*

_{S}is the semiconductor dielectric constant for 4H-SiC (6.52 at high frequency), and

*ε*

_{0}is the permittivity free space charge. Figure 4 shows the 1/

*C*

^{2}versus reverse voltage characteristics measured at a frequency of 1 MHz at room temperature. The straight line intercepts of the 1/

*C*

^{2}-

*V*characteristics with voltage axis are obtained, and thus, the barrier height values can be given as follows [23]:

where *V*_{i} is the voltage intercept, *V*_{n} is the energy difference between the minimum of the conduction band and Fermi level in the bulk of n-type SiC [*V*_{n} = *kT*/*e* ln(*N*_{C}/*N*_{D})], and *N*_{C} is the conduction band density of states for 4H-SiC at 300 K (approximately 1.66 × 10^{19} cm^{-3}) [24]. As observed from both *I-V* and *C-V* measurement results, all the samples exhibit excellent rectifying behavior with stable ideality factors.

*I-V*and

*C-V*measurements. There is some quantitative difference between the extracted values from the two different measurements; the extracted values for the barrier heights for the reference sample and the ideality factor are

*Φ*

_{B(I-V)}which is 1.04 eV and

*Φ*

_{B(C-V)}which is 1.69 eV, respectively, with

*n*at 1.50 for the control samples. The difference from the two different methods is commonly observed, which normally shows higher values for

*C-V*measurements than those obtained from

*I-V*characteristics due to additional capacitance at the interface [3, 25].

The results, however, clearly suggest that the barrier height difference between the Ni/SiC contacts (Ref) and samples with embedded NPs significantly increases and that the enhancement becomes greater for Ag particles (NP-2) than for Au particles (NP-1). The values of barrier height lowering are 0.06 eV and 0.07 eV for NP-1, whereas the values are clearly increased to 0.17 eV and 0.18 eV for NP-2 as obtained from *I-V* and *C-V* measurements, respectively. Note that the reduced barrier height and improved ideality factor are attributed to the the larger difference in the metal work function of Ag than that of Au with respect to the capping metal of Ni.

*E*for the circular patch geometry of NPs at the depletion region close to the surface of the semiconductor is given by the following equation [6, 13]:

where *z* is the distance from the surface of the semiconductor, *w* is the depletion width, *R*_{0} is the radius of the circular patch, and Δ*Φ* is the difference of the barrier height between the capping metal and NPs.

*Φ*

_{B}- Δ, due to the difference of the barrier height between the capping metal (Ni) and NPs results in the increased electric field at the depletion region close to the surface of the semiconductor. As shown in Figure 6, the values of the electric field are estimated to be 2.6 × 10

^{4}V/cm (Ref), 0.1 × 10

^{7}V/cm (NP-1), and 3.9 × 10

^{7}V/cm (NP-2) for the given experimental conditions including the diameters of the NPs, namely, 2

*R*

_{0}which is 40 nm for NP-1 and 2

*R*

_{0}which is 35 nm for NP-2. The insets of Figure 6 show the electric field distribution as a function of the size of the NPs at n-type 4H-SiC. The electric field is increased as the small size of the NPs decreases due to the increased difference of the barrier height between Ni and the NPs. The electric field at the surface of sample NP-2 is therefore higher than that of NP-1 for a similar particle diameter.

^{6}and 2.4 × 10

^{6}for NP-1 and NP-2, respectively, compared to the value of 5.18 × 10

^{5}for Ref. The increased electric field of the samples with the Au and Ag NPs is mainly attributed to the reduction of barrier height as the effective barrier of the conduction band at the depletion region decreases. As shown in Figure 7a, the extracted energy band diagram profiles along the cut line across the NP-substrate structures show that the reduction of barrier is more profound in NP-2 (with Ag) than in NP-1.

## Conclusions

In summary, we demostrate that the work function change in the embedded metal NPs can effectively lower the barrier height of the SiC diode structures. It has been experimentally shown that incorporating NPs (Ag) with a larger work function difference to the capping metal layer (Ni) results in an improved barrier lowering by further enhancing the local electric field. The barrier height of the fabricated SiC diode structures (NP-1; Ni with embedded Ag-NPs) has significantly reduced by 0.11 eV and 0.18 eV with respect to the samples with Au-NPs (NP-2) and the reference samples, respectively. The experimental results are in agreement with both analytic calulations based on Tung's model and physics-based two-dimensional numerical simulations, which confirm that the increased electric field of the samples with NPs is mainly attributed to the reduction of barrier height as the effective barrier of the conduction band at the depletion region of the surface decreases.

## Notes

## Declarations

### Acknowledgements

This work was supported by the National Research Foundation Grants 2011-0017942 and 2011-0003298 through a research grant from Kwangwoon University in 2011, and Korea-Sweden Collaboration Project.

## Authors’ Affiliations

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