“…Figure 6(b) shows the behaviour of the variation in mass during 300 cycles for the Ti6Al4V alloy. As shown in the graph, the generation of oxide layers was constant, which is associated with the movement of metal cations during the stage of oxide growth towards the outside, which generates voids that separate the oxide layer and the Ti6Al4V substrate [23–25]. It can be seen that the change in mass becomes greater as the number of thermal corrosion cycles increases, which indicates that the oxide layer has a certain protective behaviour [21,26].…”
Section: Resultsmentioning
confidence: 99%
“…[22], with an XRD pattern taken for the Ti-Zr-Si-N coating after being subjected to annealing at a temperature of 800°C, where TiO 2 , ZrO 2 , TiO, Fe 2 O 3 , and TiN are found. The formation of chromite is also possible, by the reaction of the chromium of stainless steel with air [23], which has been observed in oxidation processes from the grain boundaries to the centre. Figure 10 Cyclic oxidation diffractogram of the coating on 316L steel substrate (a) up to 50 cycles and (b) up to 300 cycles.…”
Section: Resultsmentioning
confidence: 99%
“…, where TiO 2 , ZrO 2 , TiO, Fe 2 O 3 , and TiN are found. The formation of chromite is also possible, by the reaction of the chromium of stainless steel with air [23], which has been observed in oxidation processes from the grain boundaries to the centre.…”
We present a study of the synthesis and an evaluation of the corrosion resistance of Ti-Zr-Si-N coatings deposited by means of the co-sputtering technique on 316L steel and Ti6Al4V alloy substrates. The thin films were obtained using Ti 5 Si 2 and Zr targets with 99.9% purity for the deposition, and a power of 200 W was applied in the DC source and 170 W in the RF source. The corrosion resistance was evaluated via the cyclic oxidation test with consistent cycles of 1 hour of cooling, 1 hour of heating, and 16 minutes of stabilisation for 300 cycles at a temperature of 600°. The coatings were characterised by means of scanning electron microscopy (SEM), X-ray diffraction (XRD), and confocal laser microscopy. The coating was effective up to 150 cycles for the case of 316L steel, and up to 50 cycles for the Ti6AlV alloy.
“…Figure 6(b) shows the behaviour of the variation in mass during 300 cycles for the Ti6Al4V alloy. As shown in the graph, the generation of oxide layers was constant, which is associated with the movement of metal cations during the stage of oxide growth towards the outside, which generates voids that separate the oxide layer and the Ti6Al4V substrate [23–25]. It can be seen that the change in mass becomes greater as the number of thermal corrosion cycles increases, which indicates that the oxide layer has a certain protective behaviour [21,26].…”
Section: Resultsmentioning
confidence: 99%
“…[22], with an XRD pattern taken for the Ti-Zr-Si-N coating after being subjected to annealing at a temperature of 800°C, where TiO 2 , ZrO 2 , TiO, Fe 2 O 3 , and TiN are found. The formation of chromite is also possible, by the reaction of the chromium of stainless steel with air [23], which has been observed in oxidation processes from the grain boundaries to the centre. Figure 10 Cyclic oxidation diffractogram of the coating on 316L steel substrate (a) up to 50 cycles and (b) up to 300 cycles.…”
Section: Resultsmentioning
confidence: 99%
“…, where TiO 2 , ZrO 2 , TiO, Fe 2 O 3 , and TiN are found. The formation of chromite is also possible, by the reaction of the chromium of stainless steel with air [23], which has been observed in oxidation processes from the grain boundaries to the centre.…”
We present a study of the synthesis and an evaluation of the corrosion resistance of Ti-Zr-Si-N coatings deposited by means of the co-sputtering technique on 316L steel and Ti6Al4V alloy substrates. The thin films were obtained using Ti 5 Si 2 and Zr targets with 99.9% purity for the deposition, and a power of 200 W was applied in the DC source and 170 W in the RF source. The corrosion resistance was evaluated via the cyclic oxidation test with consistent cycles of 1 hour of cooling, 1 hour of heating, and 16 minutes of stabilisation for 300 cycles at a temperature of 600°. The coatings were characterised by means of scanning electron microscopy (SEM), X-ray diffraction (XRD), and confocal laser microscopy. The coating was effective up to 150 cycles for the case of 316L steel, and up to 50 cycles for the Ti6AlV alloy.
“…[47] Fluidized bed sublimation of precursor powder in a binary particle bed of inert alumina powder not only improves its fluidization quality, but also solves dual purposes of simultaneous solid phase precursor transport and in-situ precursor vapour generation. [48][49][50][51][52][53][54][55] Carbon steel of ASTM A106 grade A (henceforth "ASTM A106") with 0.25% carbon content, medium carbon steel AISI 1045 with 0.45% carbon, and high carbon steel ASTM A227 with 0.65% carbon were used. Utilization of air as a carrier gas lowers the temperature required for chemisorption-assisted thermal decomposition of precursor vapours to aluminum and acts as an in-situ oxygen precursor for attaining thin, dense amorphous alumina coatings from the deposited aluminum at atmospheric pressure.…”
The degradation of carbon steels due to corrosion and gaseous permeation phenomena can be significantly reduced by a thin alumina coating. Tubular carbon steel structures, commonly employed in nuclear establishments are particularly vulnerable to chemical degradation on the inner surface due to the flow of corrosive fluids. In the present work, a fluidization-based chemical vapour deposition process is applied as a one-step solution for simultaneous chemical passivation of both inner and outer substrate surfaces meanwhile optimizing precursor inventory by utilizing fluidized bed sublimation and induction heating techniques. The process is studied by using a 2D-1D mathematical model, which has been validated with experimental results for different carbon steel grades. It was observed that there exists an optimum fluidization velocity for a specified initial mass fraction of precursor powder at which mass of alumina deposited per unit mass of precursor sublimated is maximized.
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