Mechanisms of r.f. plasma nitriding of Ti-6Al-4V alloy

Raveh, A.

doi:10.1016/0921-5093(93)90349-j

Cited by 32 publications

(21 citation statements)

References 27 publications

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“…The error bar are now reduced mainly in its depths spreads, showing most expected values at near surface region in agreement with literature data 4,[7][8][9][10]12 . In order to verify if the corrected values, obtained by the present analysis process, were not influenced by artifacts that can be introduced by this correction, it was also performed another correction recently introduced and based in the adjustment of the loading curve by using a power law function fitting (Odo-Lepienski method 5 ).…”

Section: Resultssupporting

confidence: 77%

“…All of these phases have hardness higher than titanium substrate 4,[7][8][9][10]12 . Consequently, it is expected that the hardness profiles decrease with depth until reaching the substrate value.…”

Section: Resultsmentioning

confidence: 99%

“…The treatment time was 3 hours for all samples. According to the literature [7][8][9][10] , at the highest treatment temperature (900 °C), a modified region of up to 4 µm in thickness is obtained. The nitriding parameters are shown in Table 1.…”

Section: Methodsmentioning

confidence: 99%

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Nanomechanical properties of rough surfaces

et al. 2006

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The nanoindentation technique allows the determination of mechanical properties at nanometric scale. Hardness (H) and elastic modulus (E) profiles are usually determined by using the Oliver-Pharr method from the load/unload curves. This approach is valid only for flat surfaces, or at least, when a very low degree of asperity is present (lower than 30 nm). The basic statement is the determination of the zero tip-surface contact point. If a rough surface is present, errors can occur in determining this contact point and, as a consequence, the surface hardness and elastic modulus profiles are drastically altered resulting in under evaluated values. Surfaces with different roughness were produced by controlled nitrogen glow discharge process on titanium. The changed nitriding parameters were different N 2 /H 2 atmospheres and temperatures (600 °C-900 °C). The most correct H and E profiles were obtained by using the contact stiffness analysis method, proposed here, that overcomes the surface roughness. The obtained results were compared with available literature data.

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Section: Resultssupporting

confidence: 77%

Section: Resultsmentioning

confidence: 99%

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Nanomechanical properties of rough surfaces

et al. 2006

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“…The intergranular β phase is, thereby, absent at the top region of the Ti-N compound layer. Raveh [11] reported that for a plasma nitrided Ti-6Al-4V alloy, aluminum and vanadium concentrations decreased in the nitrided layer and aluminum depletion near the surface promoted the initiation of TiN formation. In this study, vanadium, which stabilizes cubic β-Ti, was depleted in the Ti-N compound layer, and in the equiaxed α-Ti grains in the Ti(N) diffusion layer.…”

mentioning

confidence: 98%

Oxidation of nitride layers formed on Ti-6Al-4V alloys by gas nitriding

et al. 2011

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Ti-6Al-4V alloys were nitrided through gas nitriding at 950°C for 3 h in deoxygenated, atmospheric nitrogen gas. During nitriding, nitrogen reacted and diffused into the alloys to form Ti2N and a meager amount of TiN in a Ti-N compound layer with a thickness of 20 µm to 25 µm. An α-Ti(N) diffusion layer with a thickness of 40 µm to 80 µm formed below this layer. A small amount of Al was dissolved at the top of the Ti-N compound layer because of the strong interaction of nitrogen with Ti and Al. Nitriding resulted in the dissolution of interstitial nitrogen and the formation of nitrides. Oxidation of the nitrided Ti-6Al-4V alloys initially resulted in the formation of a Ti-N-O layer, which later oxidized to TiO2. Above 800°C, the nitrided alloys oxidized rapidly, accompanied by microcracking of the TiO2 surface layer.

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“…The samples nitrided for 18 h exhibited a relatively thicker nitrided layer compared to the samples nitrided for 4 h. As the nitriding was performed at the relatively low temperature of 520°C, the compound layer and diffusion layer could not be distinguished. Raveh [20] reported that the thickness of the compound and diffusion layer was 2-8 and 2-20 lm, respectively, for Ti-6Al-4V plasma nitrided at 490°C for different lengths of time (10 min to 10 h). Table 1 shows the surface roughness values of samples in different conditions.…”

Section: Methodsmentioning

confidence: 99%

Effect of Plasma Nitriding Environment and Time on Plain Fatigue and Fretting Fatigue Behavior of Ti–6Al–4V

Ali

Raman

2010

Tribol Lett

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Plasma nitriding was performed on Ti-6Al-4V fatigue test samples at 520°C in two environments (nitrogen and nitrogen-hydrogen mixture in a ratio of 3:1) for two time periods (4 and 18 h). Plain fatigue and fretting fatigue tests were conducted on unnitrided and plasma nitrided samples. Plasma nitriding degraded lives under both plain fatigue and fretting fatigue loadings. The samples nitrided in nitrogen exhibited superior lives compared with the samples nitrided in the nitrogen-hydrogen mixture, possibly due to the relatively higher hardness (and presumably lower toughness) of the nitrided layer of the samples nitrided in the nitrogen-hydrogen mixture environment. For those samples nitrided in the nitrogen-hydrogen mixture, those nitrided for 18 h exhibited superior lives compared with those nitrided for 4 h. This trend was observed for samples nitrided in nitrogen gas at lower stress levels only; the converse was true at higher stress levels of 550 MPa and 700 MPa under plain fatigue loading. However, under fretting fatigue loading, the plasma nitriding time did not influence the lives significantly.

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Mechanisms of r.f. plasma nitriding of Ti-6Al-4V alloy

Cited by 32 publications

References 27 publications

Nanomechanical properties of rough surfaces

Nanomechanical properties of rough surfaces

Oxidation of nitride layers formed on Ti-6Al-4V alloys by gas nitriding

Effect of Plasma Nitriding Environment and Time on Plain Fatigue and Fretting Fatigue Behavior of Ti–6Al–4V

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