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Tunneling Atomic Layer-Deposited Aluminum Oxide: a Correlated Structural/Electrical Performance Study for the Surface Passivation of Silicon Junctions
Nanoscale Research Letters volume 14, Article number: 330 (2019)
Passivation is a key process for the optimization of silicon p-n junctions. Among the different technologies used to passivate the surface and contact interfaces, alumina is widely used. One key parameter is the thickness of the passivation layer that is commonly deposited using atomic layer deposition (ALD) technique. This paper aims at presenting correlated structural/electrical studies for the passivation effect of alumina on Si junctions to obtain optimal thickness of alumina passivation layer. High-resolution transmission electron microscope (HRTEM) observations coupled with energy dispersive X-ray (EDX) measurements are used to determine the thickness of alumina at atomic scale. The correlated electrical parameters are measured with both solar simulator and Sinton’s Suns-Voc measurements. Finally, an optimum alumina thickness of 1.2 nm is thus evidenced.
The reduction in surface recombination losses in silicon p-n junctions is of prime importance in order to improve the efficiency of light absorption and its conversion into photocurrent, with solar cells as one main application [1, 2]. Among the key process that can improve the defect recombination in silicon junctions, the passivation of the surface and the contacts were and are always of prime importance. Front and rear surface passivations have been developed, both for the illuminated non-metallized regions as well as for the metal silicon contacts [3, 4]. The metal-silicon interface features large recombination, so two options have been developed to minimize the losses at the contact area: small contact area associated with low local doping level, or local passivation of the metal-silicon interface by the introduction of a thin tunneling dielectric layer. Recently, a new route with a promising potential has been suggested using a carrier-selective passivation layer . In this case, one polarity of charge carriers is allowed to pass to the metal whereas the other polarity is blocked.
Among all the passivation layers, aluminum oxide (Al2O3) deposited by atomic layer deposition (ALD) is one of the most used methods, even if plasma-enhanced chemical vapor deposition (PECVD) process can be also applied [6, 7]. ALD allows a good control of the thickness down to atomic scale, while the use of alumina leads to a good chemical passivation of interface states as well as to an efficient field effect passivation through localized charges in the oxide layer . For example, Elmi et al. showed that the introduction of embedded Ag nanoparticles in a thin alumina layer can effectively enhance the field effect passivation . It is known that the sign and the density of the localized charges as well as the thickness of alumina layer are important parameters for surface passivation. Many works have been published to study the influence of alumina thickness on the device performance; however, there is no consensus on the optimal alumina thickness since it varies from 0.24 to 30 nm in the literature, as it is summarized in Table 1. Table 1 illustrates the scattering of the optimized alumina thickness. In fact, many data concern the surface recombination velocity (Se) which does not correspond to measurements on the fabricated solar devices. The general trend is a decrease of Se for larger thickness values due to a better chemical passivation by the presence of hydrogen in the alumina layer which passivates interface states during the post-growth thermal annealing.
Richter et al. reported that emitter saturation current down to 30 fA/cm2 could be obtained for thin layer (0.5 to 3 nm) but with a stack structure constituted of alumina and 70 nm of SiNx . The best metal-silicon passivated contact is observed with a 0.24-nm-thick Al2O3 . Finally, concerning the doping and type levels, passivation is more efficient on n+ but a SiO2/alumina stack structure gives the possibility to tune the density of localized charges and can be used on both n- or p-type . Nevertheless, only few works demonstrated the correlation between the quality of the substrate/alumina interface and the electrical performances of devices. It is thus necessary to perform a systematic observation at atomic scale on the alumina passivation layer and to obtain an optimize value of the alumina thickness correlated with electrical performances.
In this paper, alumina layers deposited by using the ALD technique with different thicknesses from 0.24 to 1.9 nm were used to passivate implanted Si n+-p junctions. The interface of alumina layer on the front surface of Si junction was studied by using high-resolution transmission electron microscope (HRTEM), while the thickness of alumina layer was correlated to the associated electrical parameters such as serial resistance, ideality factor, lifetime, external quantum efficiency (EQE), and power conversion efficiency (PCE). Sinton’s Suns-Voc measurements have been performed to resolve the influence of series resistance. Finally, an optimized 1.2 nm alumina thickness was obtained. It should be noted that we focus here only on the front contact passivation of silicon p-n junctions; the device efficiency is not fully optimized which is out of purpose of this work.
Figure 1a shows the fabrication process of implanted Si n+-p junctions with surface passivation of Al2O3/SiNx:H stacks. Four-inch boron-doped p-type silicon (100) wafers with a resistivity of 5–10 Ω·cm were used as substrates. The samples were cleaned using piranha solution and distilled water before the realization of n+ top layer. Phosphorous ion implantation was performed using a dose of 1014 at/cm2 at 180 keV, followed by an annealing at 900 °C during 5 min to activate the dopants. Detailed descriptions of the technological process can be found in our previous works [24, 25].
An ultrathin Al2O3 tunneling layer with an expected thickness d ranging from 0.24 to 1.9 nm was deposited by using the ALD technique. Note that this thickness has been deduced from the average thickness determined by ellipsometry spectroscopy, obtained for alumina thin films grown with different number of cycles. One ALD cycle deposited one monolayer which equals to 0.12 nm. Junctions without alumina (d = 0), i.e., with unpassivated metal-silicon contacts, have been realized, but the PCE is very low, only 0.4% . The alumina deposition was carried out in a PICOSUN R200 system through a thermal process. The reactants used were trimethylaluminum (TMA) and H2O, while the growth temperature was 290 °C. During the ALD process, water cycles were used to oxidize the TMA precursor. As a result, a thin SiO2 oxide layer was deposited between the silicon surface and the alumina layer due to the natural oxidation of the silicon surface. The thickness of such native oxide layer observed by TEM was close to 1.5 nm. Second, an 80-nm-thick SiNx:H layer which corresponds to the value usually used in Si-solar cell industry was deposited on the sample by using the PECVD approach with a mixture of SiH4 and NH3. The deposition temperature was 340 °C, while the pressure was 1 Torr and the power was 10 W. Sample was then annealed at 650 °C for 10 min to make H diffusing into Si.
Finger electrodes of Ti/Au (20/800 nm) were deposited on the front side by sputtering with a shadow mask after the opening of the SiNx:H coating by using reactive ion etching (RIE). The back contact was then deposited by evaporating a 400-nm-thick Ti/Au film. Finally, the samples were annealed at 400 °C for 10 min to form ohmic contact.
The TEM analysis was performed from cross-sectional thin foils prepared by focused ion beam (FIB) on a FEI Helios dual-beam Nanolab 600i. Prior to the ion thinning down, a carbon film and a platinum layer were deposited to protect the top surface of the sample. The TEM, STEM high-angle annular dark field (HAADF), and STEM energy dispersive X-ray (EDX) observations were done with a double corrected JEOL ARM200F cold FEG microscope operated at 200 kV and equipped with an EDX spectrometer (CENTURION from JEOL). The image processing was performed using DIGITALMICROGRAPH (GATAN). The images were taken with the electron beam parallel to the  direction of the Si (100)-oriented substrate. In this orientation, the electron beam is parallel to the alumina/substrate interface.
The electrical parameters under illumination were measured using a solar simulator (Oriel®Sol3ATM) under AM 1.5G illumination, while the external quantum efficiency (EQE) spectra were measured under standard measurement conditions on a 7-SCSpec system manufactured by 7-STAR Co. To overcome the series resistance influence, Sinton’s Suns-Voc measurements have been performed [26,27,28]. Sinton’s Suns-Voc technique is an open-circuit method to indicate the performance of a p-n junction or solar cell which allows to compare the electrical parameters given by the solar simulator with the ones deduced without the influence of the series resistance. The setup includes a xenon flashlamp with a full set of neutral-density filters and a wafer stage controlled at 25 °C. A standard I-V curve format with an estimated Jsc can be performed by either probing the p+ and n+ regions directly or probing the metallization layer. The data can be used directly to indicate the material and passivation quality of solar cells.
Results and Discussion
Figure 1(b) is a typical HRTEM image taken along the  direction of the silicon substrate. In this direction, the electron beam is necessarily parallel to the film substrate interface. Note that the top surface of the substrate is not perfectly flat. This observation implies that the interfaces between the different above amorphous layers (silica, alumina and silicon nitride) are also rough, making their characterization a very difficult task. Indeed, the thickness measurement is always overestimated due to this roughness. The inset of Fig. 1(b) is an intensity profile perpendicular to the substrate and over a 10 nm wide region as indicated by the white rectangle of the HRTEM image. This profile gives evidence of the difference in contrast between the three amorphous layers on the top of the Si substrate. Indeed, due to the Z contrast, a darker 0.9 nm thick layer can be observed above the silica layer, which is most probably the alumina layer grown by ALD. To confirm this result, high angle annular dark field imaging has been performed on two different alumina layers combined with chemical mapping obtained by scanning transmission electron microscopy coupled with an energy dispersive X ray spectrometer. Figure 1(c) and (d) are two sets of data illustrating two different alumina layer thicknesses.
Both sets are composed of an HAADF image presenting the top surface of the Si substrate (along the  direction) and the three amorphous layers namely silica (dark region), alumina (whiter region) and finally silicon nitride (intermediate contrast). Note that some bright dots are visible especially in Fig. 1(d). These features are due to platinum dusts coming from the protection layer during the FIB preparation of the thin foil. For both structures, STEM EDX chemical maps of aluminum, oxygen and silicon are reported on the top of the Fig. 1(c) and (d). The aluminum maps show nicely the presence of aluminum corresponding to the whiter regions of the HAADF images. It is found that some bright dots are present in the adjacent regions but these correspond to some “noise” in the background during acquisition. Wider regions are visible in the oxygen maps since they image the alumina and silica layers. Finally, the silicon maps depict a dark line corresponding to the alumina layers, the only layer without silicon. Due to diffusion scattering phenomena, the chemical maps are not the best data to estimate properly the thickness values.
In order to show more clearly the different contrast induced by the presence of the alumina layer, we have plotted the intensity profiles for both images as shown in Fig. 1(c) and (d). As clearly demonstrated by these profiles, a broad band indicates the brighter regions corresponding to the alumina layer. Considering that the alumina has a certain roughness, it is reasonable to estimate the layer thickness by measuring the distance between two vertical lines located at the middle of the slopes on each side of the layer. The results are about 1.2 nm and 1.9 nm, respectively.
Evolution of the Series Resistance R s
As shown in Fig. 2a, Rs is almost constant (Rs = 1.1 ± 0.15 Ω) from d = 0.24 to 1.2 nm and increases abruptly to 3.1 ± 0.2 Ω for d = 1.9 nm. The measured resistance Rs is the addition of the emitter and base zones, of the metallic fingers, and of the resistance associated with the thin SiO2 oxide layer, altogether labeled Ri, plus the resistance Rthu associated to the alumina layer. For all the samples, in the limit of the reproducibility of the technology procedure given by the error bars (± 0.15 Ω) in Fig. 4, Ri is considered as constant since the same technological process is applied. d is the only modified parameter. So, as Rs is constant up to d = 1.2 nm and as the tunneling resistance Rthu obviously varies with d, we conclude that up to d = 1.2 nm, Rthu varies but its variation is less than the dispersion of the measurements, i.e., 0.15 Ω. Rthu is directly bound to the inverse of the transfer coefficient γ for tunneling, i.e., the tunneling probability of carriers through a rectangular barrier, given by :
where m* is the effective mass in the alumina barrier (m* = 0.75 m0 , with m0 as the electron mass), h is the Planck constant, q is the electron charge, and ϕB is the effective barrier height, equal to the conduction band offset ΔEC between dielectric and the n+ silicon contact. The tunneling resistance is given by:
where A is a constant. For d = 1.9 nm, Rthu corresponds to the step measured on Rs, and therefore, we deduce Rthu (1.9 nm) = 2 Ω. From this value, A can be calculated. For that, we have to know ϕB which is equal to the conduction band offset between Si and the dielectric layer, since the Fermi level is within the minimum of the conduction band in the heavily doped n+ silicon contact. In fact, the dielectric layer is actually a few nanometers SiO2/Al2O3 stack, so the band offset depends on these two dielectric layers. The conduction band offset is in the 3.13–3.5 eV and 2.08–2.8 eV range for SiO2 and Al2O3 , respectively. Table 2 gives the values of the A prefactor deduced from the value of Rs measured at d = 1.9 nm, for the two extreme values of ϕB.
In Fig. 2b, we have plotted Rs and the total simulated resistance Rsimu = Ri + Rthu for the two ϕB values versus d (Rs has been taken to its average value 1.1 Ω between d = 0.24 and 1.2 nm). Whatever ϕB, for d ≤ 1.2 nm, Rthu is negligible. It confirms our starting hypothesis: the step observed at 1.9 nm in the evolution of Rs is associated with the evolution of the tunneling barrier. For d less than 1.2 nm, the main effect of alumina layer is to passivate the n+ contacts and the p surface, by means of field effect passivation associated with the fixed charges localized in the oxide. For larger d values, the alumina layer introduces a parasitic series contact resistance that decreases the electrical performances of the cells.
Finally, we can estimate the resistivity ρ of the alumina layer. For that, we consider the measured resistance R for a thickness value of 1.9 nm. The tunneling effect decreases, and the layer begins to have a “bulk-like” behavior (a crude approximation). With such an alumina thickness (d = 1.9 nm) and considering the surface S of the contact (10.54 mm2), we deduce ρ using the following equation:
That leads to ρ = 1.1 × 106 Ω·cm. For bulk materials on the markets, depending of the growth temperature and of the impurities in the alumina, the resistivity value varies from 105 to 1014 Ω·cm (from Kyocera™). So, our estimated value shows that we have a “pseudo-bulk” material, at the limit between a thin layer and a bulk layer.
Evolution of the Ideality Factor n
In the presence of a series resistance, the I-V curve of a solar cell is:
where I is the cell output current, IL is the light generated current, V is the voltage across the cell, T is the temperature, k is the Boltzmann constant, n is the ideality factor, and RS is the cell series resistance. For low injection level, with only band-to-band or Schottky Read-Hall recombinations, the ideality factor n is less than 2. It reaches the value of 1 when recombination is limited by minority carriers . An increase of n indicates that an unusual recombination mechanism is taking place, involving both minority and majority carriers . So, n is a signature of the recombination (or of the passivation) of the device. Moreover, n is also bound to Rs that increases the ideality factor . The evolution of n versus the alumina thickness is shown in Fig. 3a.
For low thickness value (0.24 nm), n is greater than 2, which is the signature of unpassivated surface. As the alumina thickness increases, n decreases and stabilizes at about 1.5, evidencing an efficient passivation effect through the alumina. For an alumina thickness value of 1.9 nm, n increases abruptly to 4, accordingly to the abruptly increase of Rs. So, both Rs and n show that the alumina layer well passivates the Si junction, associated with a low tunneling barrier. For d = 1.9 nm, the tunneling barrier increases, with a subsequent degradation of Rs and therefore of the ideality factor.
Another key parameter which illustrates the passivation effect is the lifetime of the photocarriers, τ. Indeed, the lifetime is directly associated with the recombination rate of the carriers, bound to the concentration of surface defects (recombination centers). It was deduced from the measured open-circuit voltage, its time derivative, and the actual illumination level. Its evolution versus the alumina thickness is given in Fig. 3b. The evolution of the lifetime is in agreement with the previous results. The average value is low, mainly due to the unpassivated rear contact. However, it clearly exhibits an increase with the alumina thickness, accordingly to a better passivation of the front contact and with an optimum thickness value of 1.2 nm. For d = 1.9 nm, the lifetime decreases. It is possible that as the alumina thickness increases, less hydrogen diffuses from the SiNx layer to the contact during the thermal annealing, and therefore, the chemical passivation effect decreases.
Figure 4 gives the measured EQE versus the alumina thickness. The best EQE is observed for d = 1.2 nm. The main improvement is observed for the wavelength varying from 600 to 900 nm. In all cases, the EQE is far from an ideal rectangular shape in the IR which is a signature of recombination at the unpassivated rear contact.
In order to complete the analysis, we have studied the electrical parameters under illumination measured both under a solar simulator and using Sinton’s method. Figure 5 shows the power efficiency of the solar cells versus the alumina thickness: the measured one with the solar simulator and the optimized one without Rs. As the alumina thickness increases, the measured PCE increases due to a better passivation effect reaching a maximum value of 5% for d = 1.2 nm, before decreasing for d = 1.9 nm. The corrected PCE for Rs = 0 has a quite constant value around 11%. This value is a reasonable one considering only the passivation of the rear contact. For d = 1.9 nm, the corrected yield decreases down to 6%, due to parasitic shunt resistance.
Alumina deposited by ALD is an efficient method to passivate electrical contacts, a key parameter for silicon p-n junctions. In this work, tunneling atomic layer-deposited alumina layer with various thicknesses from 0.24 to 1.9 nm was used to passivate the implanted Si n+-p junctions. We have performed systematic HRTEM, STEM HAADF, and STEM EDX structural analyses correlated with a complete set of electrical measurements using both solar simulator and Sinton’s analyses. This original approach allows to claim that the optimum alumina thickness for achieving an efficient passivation effect is 1.2 nm. Although the device efficiency is not fully optimized in this work, the optimum alumina passivation could be beneficial for the development of the high-efficiency silicon-based solar cells.
Atomic layer deposition
Energy dispersive X-ray
External quantum efficiency
Focused ion beam
High-angle annular dark field
High-resolution transmission electron microscope
Power conversion efficiency
Plasma-enhanced chemical vapor deposition
Reactive ion etching
Transmission electron microscope
Wang HP, He JH (2017) Toward highly efficient nanostructured solar cells using concurrent electrical and optical design. Adv Energy Mater 7:1602385
Zhong WW, Shen SJ, He M, Wang D, Wang ZP, Lin ZP, Tu WG, Yu JG (2019) The pulsed laser-induced Schottky junction via in-situ forming Cd clusters on CdS surfaces toward efficient visible light-driven photocatalytic hydrogen evolution. Appl Catal B-Environ 258:117967
Rehman AU, Iqbal MZ, Bhopal MF, Khan MF, Hussain F, Iqbal F, Khan M, Lee SH (2018) Development and prospects of surface passivation schemes for highefficiency c-Si solar cells. Sol Energy 166:90–97
Zhong WW, Shen SJ, Feng SS, Lin ZP, Wang ZP, Fang BZ (2018) Facile fabrication of alveolate Cu2−xSe microsheets as a new visible-light photocatalyst for discoloration of Rhodamine B. CrystEngComm 20:7851
Schmidt J, Peibst R, Brendel R (2018) Surface passivation of crystalline silicon solar cells: present and future. Sol Energy Mat Sol C 187:39–54
Veith B, Dullweber T, Siebert M, Kranz C, Werner F, Harder NP, Schmidt J, Roos BFP, Dippell T, Brendel R (2012) Comparison of ICP-AlOx and ALD-Al2O3 layers for the rear surface passivation of c-Si solar cells. Energy Procedia 27:379–384
Liu YP, Shen SJ, Zhang JT, Zhong WW, Huang XH (2019) Cu2−xSe/CdS composite photocatalyst with enhanced visible light photocatalysis activity. Appl Surf Sci 478:762–769
Dingemans G, Kessels WVM (2012) Status and prospects of Al2O3-based surface passivation schemes for silicon solar cells. J Vac Sci Technol A 30:040802
Elmi OI, Cristini RO, Chen MY, Wei B, Bernard R, Yarekha D, Okada E, Ouendi S, Portier X, Gourbilleau F, Xu T, Stiévenard D (2018) Local Schottky contacts of embedded Ag nanoparticles in Al2O3/SiNx:H stacks on Si: a design to enhance field effect passivation of Si junctions. Nanotechnology 29:285403
Hoex B, Heil SBS, Langereis E, Van de Sanden MCM, Kessels WMM (2006) Ultralow surface recombination of c-Si substrates passivated by plasma-assisted atomic layer deposited Al2O3. Appl Phys Lett 89:042112
Hoex B, Gielis JJH, Van de Sanden MCM, Kessels WMM (2008) On the c-Si surface passivation mechanism by the negative-chargedielectric Al2O3. J Appl Phys 104:113703
Schmidt J, Veith B, Brendel R (2009) Effective surface passivation of crystalline silicon using ultrathin Al2O3 films and Al2O3/SiNx stacks. Phys Status Solidi-R 3:287–289
Dingemans G, Engelhart P, Seguin R, Einsele F, Hoex B, Van de Sanden MCM, Kessels WMM (2009) Stability of Al2O3 and Al2O3/a-SiNx:H stacks for surface passivation of crystalline silicon. J Appl Phys 106:114907
Terlinden NM, Dingemans G, Van de Sanden MCM, Kessels WMM (2010) Role of field-effect on c-Si surface passivation by ultrathin (2–20 nm) atomic layer deposited Al2O3. Appl Phys Lett 96:112101
Dingemans G, Seguin R, Engelhart P, Van de Sanden MCM, Kessels WMM (2010) Silicon surface passivation by ultrathin Al2O3 films synthesized by thermal and plasma atomic layer deposition. Phys Status Solidi-R 4:10–12
Werner F, Veith B, Zielke D, Kühnemund L, Tegenkamp C, Seibt M, Brendel R, Schmidt J (2011) Electronic and chemical properties of the c-Si/Al2O3 interface. J Appl Phys 109:113701
Richter A, Benick J, Hermle M, Glunz SW (2011) Excellent silicon surface passivation with 5 Å thin ALD Al2O3 layers: influence of different thermal post-deposition treatments. Phys Status Solidi-R 5:202
Zielke D, Petermann JH, Werner F, Veith B, Brendel R, Schmidt J (2011) Contact passivation in silicon solar cells using atomic-layer-deposited aluminum oxide layers. Phys Status Solidi-R 5:298–300
Garcia-Alonso D, Smit S, Bordihn S, Kessels WMM (2013) Silicon passivation and tunneling contact formation by atomic layer deposited Al2O3/ZnO stacks. Semicond Sci Technol 28:082002
Kotipalli R, Delamre R, Poncelet O, Tang X, Francis LA, Flandre D (2013) Passivation effects of atomic-layer-deposited aluminum oxide. EPJ Photovoltaics 4:45107
Albadri AM (2014) Characterization of Al2O3 surface passivation of silicon solar cells. Thin Solid Films 562:451–455
Deckers J, Cornagliotti E, Debucquoy M, Gordon I, Mertens R, Poortmans J (2014) Aluminum oxide-aluminum stacks for contact passivation in silicon solar cells. Energy Procedia 55:656–664
Van de Loo BWH, Knoops HCM, Dingemans G, Janssen GJM, Lamers MWPE, Romijn IG, Weeber AW, Kessels WMM (2015) “Zero-charge” SiO2/Al2O3 stacks for the simultaneous passivation of n+ and p+ doped silicon surfaces by atomic layer deposition. Sol Energy Mater Sol C 143:450–456
Xu T, Tian ZH, Ibrahim EO, Krzeminski C, Robbe O, Lambert Y, Yakeda D, Okada E, Wei B, Stiévenard D (2017) Optical and electrical properties of nanostructured implanted silicon n+-p junction passivated by atomic layer deposited Al2O3. Phys E 93:190–195
Zhou D, Xu T, Lambert Y, Cristini-Robbe O, Stiévenard D (2015) Enhancement of electrical properties of nanostructured polysilicon layers through hydrogen passivation. J Nanosci Nanotechnol 15:9772–9776
Mahan JE, Ekstedt TW, Frank RI, Kaplow R (1979) Measurement of minority carrier lifetime in solar cells from photo-induced open-circuit voltage decay. IEEE Trans on Elect Dev 26:33
Sinton RA, Cuevas A (1996) Contactless determination of current–voltage characteristics and minority-carrier lifetimes in semiconductors from quasi-steady-state photoconductance data. Appl Phys Lett 69:2510
Kerr MJ, Cuevas A, Sinton RA (2002) Generalized analysis of quasi-steady-state and transient decay open circuit voltage measurements. J Appl Phys 91:399
Sze SM, Ng Kwok K (2007) Physics of semiconductor devices, vol 440, 3rd edn. Wiley, New York
Rippard WH, Perrella AC, Albert FJ, Buhrman RA (2002) Ultrathin aluminum oxide tunnel barriers. Phys Rev Lett 88:046805
Bersch E, Rangan S, Bartynski RA, Garfunkel E, Vescovo E (2008) Band offsets of ultrathin high-oxide films with Si. Phys Rev B 78:085114
Schenk A, Krumbein U (1995) Coupled defect-level recombination: theory and application to anomalous diode characteristics. J Appl Phys 78:3185
Breitenstein O, Bauer J, Lotnyk A, Wagner JM (2009) Defect induced non-ideal dark I-V characteristics of solar cells. Superlattice Microst 45:182–189
This work was supported by the Natural Scientific Foundation of Shanghai (19ZR1419500), the “GENESE” contract (ref: 13-BS09-0020-03) from the French National Research Agency, and the Equipex Programs Excelsior ANR-11-EQPX-0015. X. Portier is grateful to F. Lemarié for the thin foil FIB preparation and to the French National Research Agency in the framework of the PAI program (ANR-11-EQPX-0020) for financial support.
The authors declare that they have no competing interests.
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Liu, K., Cristini-Robbe, O., Elmi, O.I. et al. Tunneling Atomic Layer-Deposited Aluminum Oxide: a Correlated Structural/Electrical Performance Study for the Surface Passivation of Silicon Junctions. Nanoscale Res Lett 14, 330 (2019). https://doi.org/10.1186/s11671-019-3160-2
- Surface passivation
- Atomic layer deposition
- Alumina layer
- Structural/electrical properties
- Silicon p-n junction