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Mar 2013

Volume 31, Issue 2, Articles (02xxxx)

Issue Cover Spotlight Figure

J. Vac. Sci. Technol. A 31, 020605 (2013); http://dx.doi.org/10.1116/1.4791669 (5 pages)

Peter J. Cumpson, Jose F. Portoles, and Naoko Sano
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Competing reactions during metalorganic deposition: Ligand-exchange versus direct reaction with the substrate surface

Jia-Ming Lin, Andrew V. Teplyakov, and Juan Carlos F. Rodríguez-Reyes

J. Vac. Sci. Technol. A 31, 021401 (2013); http://dx.doi.org/10.1116/1.4774031 (17 pages) | Cited 1 time

Online Publication Date: 7 January 2013

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Surface-mediated reactions of metalorganic compounds on solid substrates are key processes in film deposition technology, especially in atomic layer deposition (ALD) or chemical vapor deposition. Since most applications of thin films require high purity, understanding and controlling the mechanisms of desired and undesired surface reactions are of the utmost importance. This work outlines a general approach to understand potential surface reactions during deposition through density functional theory calculations, considering precursors containing the most commonly used types of ligands, namely alkyl (Al(CH3)3), alkoxide (Ti[OC3H7]4), alkylamide (Hf[N(CH3)2]4), diketonate (Cu(acac)2), amidinate (Ni[Pr-amd]2), and cyclopentadienyl (Hf(Cp)2(CH3)2). In all cases, the “desired” ligand-exchange reaction (the basis of most ALD processes) is compared to “undesired” surface reactions, where the ligands of the precursor interact with reactive surface sites and can undergo uncontrolled decomposition pathways, incorporating undesired elements into the growing film. To be able to make an effective comparison across precursor types, all calculations were made considering the same surface model, that of a Si(100) surface, and the same level of theory. Our results show that the undesired ligand-mediated adsorption on reactive sites can often compete (both thermodynamically and kinetically) with the desired ligand-exchange reaction, particularly in the case of alkoxides, alkylamides, and diketonates. The intrinsic reactivity of each precursor (based on their frontier molecular orbitals) is found to determine the manner in which it will react with the surface. This article emphasizes that undesired reactions can often be predicted and evaluated based on the chemical reactivity of each precursor. This approach, applied to specific cases, will be important for probing the chemical performance of a deposition precursor.
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81.15.Gh Chemical vapor deposition (including plasma-enhanced CVD, MOCVD, ALD, etc.)
82.30.Lp Decomposition reactions (pyrolysis, dissociation, and fragmentation)
82.65.+r Surface and interface chemistry; heterogeneous catalysis at surfaces
68.43.Mn Adsorption kinetics
68.55.-a Thin film structure and morphology

Sample-morphology effects on x-ray photoelectron peak intensities

Cedric J. Powell, Sven Tougaard, Wolfgang S. M. Werner, and Werner Smekal

J. Vac. Sci. Technol. A 31, 021402 (2013); http://dx.doi.org/10.1116/1.4774214 (7 pages)

Online Publication Date: 8 January 2013

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The authors have used the National Institute of Standards and Technology Database for the Simulation of Electron Spectra for Surface Analysis to simulate photoelectron spectra from the four sample morphologies considered by Tougaard [J. Vac. Sci. Technol. A 14, 1415 (1996)]. These simulations were performed for two classes of materials, two instrument configurations, and two conditions, one in which elastic scattering is neglected (corresponding to the Tougaard results) and the other in which it is included. The authors considered the Cu/Au morphologies analyzed by Tougaard and similar SiO2/Si morphologies since elastic-scattering effects are expected to be smaller in the latter materials than the former materials. Film thicknesses in the simulations were adjusted in each case to give essentially the same chosen Cu 2p3/2 or O 1s peak intensity. Film thicknesses with elastic scattering switched on were systematically less than those with elastic scattering switched off by up to about 25% for the Cu/Au morphologies and up to about 14% for the SiO2/Si morphologies. For the two morphologies in which the Cu 2p3/2 or O 1s peak intensity was attenuated by an overlayer, the ratios of film thicknesses with elastic scattering switched on to those with elastic scattering switched off varied approximately linearly with the single-scattering albedo, a convenient measure of the strength of elastic scattering. This variation was similar to that of the ratio of the effective attenuation length to the inelastic mean free path for the photoelectrons in the overlayer film. For the two morphologies in which the Cu 2p3/2 or O 1s photoelectrons originated from an overlayer film, the ratios of film thicknesses with elastic scattering switched on to those with elastic scattering switched off varied more weakly with the single-scattering albedo. This weaker variation was attributed to the weaker effects of elastic scattering for photoelectrons originating predominantly from near-surface atoms than for photoelectrons that travel through an overlayer film.
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79.60.Bm Clean metal, semiconductor, and insulator surfaces
68.35.bd Metals and alloys
68.35.bg Semiconductors
68.55.jd Thickness

Origin of defects on targets used to make extreme ultraviolet mask blanks

He Yu, Daniel Andruczyk, David N. Ruzic, Vibhu Jindal, and Patrick Kearney

J. Vac. Sci. Technol. A 31, 021403 (2013); http://dx.doi.org/10.1116/1.4788670 (6 pages)

Online Publication Date: 23 January 2013

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Particle formation is a major problem in extreme ultraviolet masks, and one source of these particles has been identified to be the targets used to produce the mask surfaces. In particular, the silicon (Si) and ruthenium (Ru) target appear to produce more particles, especially silicon. The evidence of this is seen as a rough region on the edges of the silicon target. The features in the region were found to be triangular mesas pointing in the direction of the incident beam. The aim of this research is to prevent the mesa formation features on the target and thus reduce particle formation on the target. Both Si and Ru targets were sputtered using different ion beam conditions to understand the mesa formation mechanisms on the target and explore the ion beam conditions that can mitigate mesas. A simple 2D Monte-Carlo computer model (Illinois surface analysis model) was used to understand the formation of mesas with different incident angles of ion beam (0°, 35°, 54°, 75°) that agrees with the shapes of mesas seen in the experiments. Additionally, srim was used to calculate sputtering yields to better understand the different mechanisms between Si and Ru. It is concluded from both experiment and calculation results that an effective way to stop mesas formation is to have a sample oscillating between 0° and the desired angle during sputtering.
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81.16.Nd Micro- and nanolithography
85.40.Hp Lithography, masks and pattern transfer

Surface reconstruction at the initial Ge adsorption stage on Si(114)-2 × 1

Ganbat Duvjir, Hidong Kim, Otgonbayar Dugerjav, Huiting Li, Moaaed Motlak, Amarmunkh Arvisbaatar, and Jae M. Seo

J. Vac. Sci. Technol. A 31, 021404 (2013); http://dx.doi.org/10.1116/1.4792243 (6 pages)

Online Publication Date: 14 February 2013

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By combined investigation of scanning tunneling microscopy and synchrotron core-level photoemission spectroscopy on the structural and chemical evolution at the initial stage of Ge adsorption on Si(114)-2 × 1, it has been observed that one-dimensional (1D) sawtooth-like nanostructures composed of (113) and (117) facets and 1D trenches adjacent to the (113) facets are readily formed without any wetting layer. Due to the absence of chain structures on the reconstructed Si(114)-2 × 1, enhanced Ge interdiffusion detected from Ge/Si(5 5 12)-2 × 1 has not been found. Instead, Si atoms originating from etched surfaces and arriving Ge atoms form the alloy facets with Ge-rich surfaces. These experimental results prove that, if the direction of the Ge overlayer corresponding to that of the substrate is unstable like the present case, the arriving atoms prefer to form facets covered with the species of lower surface free energies rather than a uniform wetting layer.
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68.35.bg Semiconductors
68.43.-h Chemisorption/physisorption: adsorbates on surfaces
68.43.Mn Adsorption kinetics
68.37.Ef Scanning tunneling microscopy (including chemistry induced with STM)
79.60.Bm Clean metal, semiconductor, and insulator surfaces
68.08.Bc Wetting

Nanoscale topographic pattern formation on Kr+-bombarded germanium surfaces

Joy C. Perkinson, Charbel S. Madi, and Michael J. Aziz

J. Vac. Sci. Technol. A 31, 021405 (2013); http://dx.doi.org/10.1116/1.4792152 (5 pages) | Cited 1 time

Online Publication Date: 19 February 2013

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The nanoscale pattern formation of Ge surfaces uniformly irradiated by Kr+ ions was studied in a low-contamination environment at ion energies of 250 and 500 eV and at angles of 0° through 80°. The authors present a phase diagram of domains of pattern formation occurring as these two control parameters are varied. The results are insensitive to ion energy over the range covered by the experiments. Flat surfaces are stable from normal incidence up to an incidence angle of θ = 55° from normal. At higher angles, the surface is linearly unstable to the formation of parallel-mode ripples, in which the wave vector is parallel to the projection of the ion beam on the surface. For θ ≥ 75° the authors observe perpendicular-mode ripples, in which the wave vector is perpendicular to the ion beam. This behavior is qualitatively similar to those of Madi et al. for Ar+-irradiated Si but is inconsistent with those of Ziberi et al. for Kr+-irradiated Ge. The existence of a window of stability is qualitatively inconsistent with a theory based on sputter erosion [R. M. Bradley and J. M. Harper, J. Vac. Sci. Technol. A 6, 2390 (1988)] and qualitatively consistent with a model of ion impact-induced mass redistribution [G. Carter and V. Vishnyakov, Phys. Rev. B 54, 17647 (1996)] as well as a crater function theory incorporating both effects [S. A. Norris et al., Nat. Commun. 2, 276 (2011)]. The critical transition angle between stable and rippled surfaces occurs 10°–15° above the value of 45° predicted by the mass redistribution model.
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81.16.Rf Micro- and nanoscale pattern formation
81.30.Dz Phase diagrams of other materials
81.65.Cf Surface cleaning, etching, patterning
68.35.bg Semiconductors
61.80.Jh Ion radiation effects
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