The effects of diborane ͑B 2 H 6 ͒ pretreatment on atomic layer deposition ͑ALD͒ of tungsten ͑W͒ thin film using a sequential supply of WF 6 and SiH 4 on thermally grown SiO 2 and TiN films at 300°C were investigated. The results show that the B 2 H 6 pretreatment reduces the incubation time for film growth. X-ray photoelectron spectroscopy and scanning electron microscopy analysis suggest that elemental B on SiO 2 , released during B 2 H 6 pretreatment, induce rapid W nucleation. The drastically improved step coverage of ALD-W film is achieved at the ultrahigh aspect ratio contact ͑height: 2.23 m and top diameter: 0.14 m͒ by the enhanced nucleation and growth via B 2 H 6 pretreatment. The effects of B 2 H 6 pretreatment on the properties of ALD-W films such as roughness, phase, microstructure, and resistivity are also investigated.Tungsten ͑W͒ thin film, which has been widely used in semiconductor devices as a contact plug material, is typically formed in two steps. The first step is the W nucleation layer deposition which is basically the reduction of WF 6 using SiH 4 due to its fast nucleation on a typical glue/barrier layer, TiN film, and the second is the W-plug fill deposition accomplished by H 2 reduction of WF 6 without any supply of SiH 4 because of its excellent step coverage. Though a chemical vapor deposited ͑CVD͒-W nucleation layer has been successfully used in the semiconductor industry as a nucleation layer, 1 its limited conformality at ultrahigh-aspect-ratio ͑UHAR͒ contact can induce potential problems such as the seam or void in final W-plug, leading to the degradation in contact resistance. 2 The above problem can be solved by atomic layer deposition ͑ALD͒ because ALD is known to provide excellent step coverage. [2][3][4][5][6] Tungsten ALD is the most successful case among elemental metal ALD processes. This is fundamentally due to the fact that W ALD can be carried out using a well-known good metal-containing precursor, WF 6 , and a good reducing agent such as Si 2 H 6 , SiH 4 , and B 2 H 6 . The smooth ALD-W films were deposited using a sequential supply of WF 6 and Si 2 H 6 at low growth temperatures at growth rates close to the ideal 1 ML/cycle, ϳ2.5 Å/cycle, and the resistivity of 122 ⍀ cm. 3 Neither Si nor F was found in the film, suggesting a complete surface reaction between these two precursors. It was also reported 5 that the smooth ALD-W films with low F content below 0.1 atom % were obtained with the resistivity of 150 ⍀ cm by using B 2 H 6 as a reducing agent.However, there has been a report that for W ALD on SiO 2 at 300°C, the nucleation delay for the film growth is significant, ϳ10 cycles. 4 Furthermore, the thin surface oxide layer impedes W film nucleation and growth during WF 6 exposure on Si at 300 ϳ 550°C. 7 This in turn, causes the degradation in the conformality of ALD-W film to occur, particularly when the step coverage of the TiN underlayer is not good. This is because the SiO 2 layer is exposed in the contact and the ALD-W film should grow on it. The nucleation of ALD...