Materials for High Temperature Engineering Applications

Meetham, Geoffrey W.; Voorde, MH Van de; Mishnaevsky, Leon

doi:10.1115/1.1399413

Cited by 14 publications

(25 citation statements)

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“…No nickel-bearing phases could be identified at 1,000 • C. In addition, no protective scale of Cr 2 O 3 was found. This result is in good agreement with the literature [1][2][3][4][5]: when there is no protective oxide scale, such as Cr 2 O 3 , because it has been destroyed, breakdown occurs.…”

Section: Resultssupporting

confidence: 92%

“…However, at a certain point, the scale thickness is unable to bear the increased stress and the stress is released. The release of stress may be due to either cracking in the scale or creep of the substrate metal (base metal) [1][2][3][4][5]. Figure 1 shows in our case the curve before and after the breakdown.…”

Section: Resultsmentioning

confidence: 99%

“…This breakdown corresponds to the formation of a duplex layer consisting of an inner scale of a spinel and an exterior scale of Fe 2 O 3 . Depending on the material and the environment, this fast oxidation can continue or, on the contrary, the oxidation velocity can decrease [1][2][3][4][5]. There has been little work on the breakdown and the subsequent degradation of these types of stainless steels at 1,000 • C. At temperatures above 800 • C, the evaporation of chromium can occur, and this tends to convert the 50-200 μm thick protective scale of Cr 2 O 3 which was formed initially to a less protective scale, rich in iron oxides (Fe 2 O 3 /Fe 3 O 4 ) and less thick [6].…”

Section: Introductionmentioning

confidence: 99%

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Breakdown and Evolution of the Protective Oxide Scales of AISI 304 and AISI 316 Stainless Steels under High-Temperature Oxidation

Habib

Damra

Saura

et al. 2011

International Journal of Corrosion

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The failure of the protective oxide scales of AISI 304 and AISI 316 stainless steels has been studied and compared at 1,000°C in synthetic air. First, the isothermal thermogravimetric curves of both stainless steels were plotted to determine the time needed to reach the breakdown point. The different resistance of each stainless steel was interpreted on the basis of the nature of the crystalline phases formed, the morphology, and the surface structure as well as the cross-section structure of the oxidation products. The weight gain of AISI 304 stainless steel was about 8 times greater than that of AISI 316 stainless steel, and AISI 316 stainless steel reached the breakdown point about 40 times more slowly than AISI 304 stainless steel. In both stainless steels, reaching the breakdown point meant the loss of the protective oxide scale of Cr2O3, but whereas in AISI 304 stainless steel the Cr2O3scale totally disappeared and exclusively Fe2O3was formed, in AISI 316 stainless steel some Cr2O3persisted and Fe3O4was mainly formed, which means that AISI 316 stainless steel is more resistant to oxidation after the breakdown.

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Section: Resultssupporting

confidence: 92%

Section: Resultsmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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Breakdown and Evolution of the Protective Oxide Scales of AISI 304 and AISI 316 Stainless Steels under High-Temperature Oxidation

Habib

Damra

Saura

et al. 2011

International Journal of Corrosion

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“…The need of refractory materials for uses in particularly harsh conditions has led to significant advances in many fields of the materials science [1]. These high temperature components are usually coated to protect them against corrosion, intense heat fluxes or wear.…”

Section: Introductionmentioning

confidence: 99%

Transient stages during the chemical vapour deposition of silicon carbide from CH3SiCl3/H2: impact on the physicochemical and interfacial properties of the coatings

et al. 2012

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International audienceTransient CVD experiments were produced from CH 3 SiCl 3 (MTS)/H 2 mixtures, by varying linearly as a function of time the deposition temperature or the initial gas flow rates (Q MTS or Q H2). The consequences on the composition of the gas phase, the deposition rates, and the physicochemical properties of the transient coating layers ( Tr) have been respectively examined by in situ FTIR, thermogravimetric analyses, Raman spectroscopy and TEM. Finally, the adhesion of SiC/ Tr /SiC bilayers, obtained using various transient stages, was investigated by scratch testing. For transient stages resulting from a decrease of Q MTS or T, crystallized or amorphous silicon can be co-deposited, due the higher reactivity of SiCl x radicals as compared to hydrocarbons. In this case, the continuous covalent bonding through the Si-rich interfacial layers preserves the strong adhesion between the two stoichiometric layers. Transient stages resulting from a decrease of Q H2 close to zero eventually lead to the co-deposition of anisotropic carbon, due to the formation of unsaturated hydrocarbons in the gas phase. The interfacial layers with the largest thicknesses and including a continuous anisotropic carbon interlayer lead to poor adhesion properties. Conversely, thin and discontinuous carbon-rich interfacial layers do not affect the interfacial properties significantly. Highlights  Systematic investigations of various CVD transient stages: f(T or H 2 /CH 3 SiCl 3)  Correlation between changes of CVD parameters and in situ gas phase composition  Correlation between CVD parameters and deposition rate  Correlation between CVD parameters and nature of the gradient Si-C coating

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“…The single crystal superalloy shows excellent high-temperature and high-stress mechanical properties, and is widely used as the turbine blade material in aircraft engines [39]. During the heat treatment, the L1 2 cubic γ' phase separates out from the face-centered cubic (fcc) γ phase matrix regularly.…”

Section: In Situ Observation Of Dd10 Single Crystal Superalloymentioning

confidence: 99%

Recent Progress of Residual Stress Distribution and Structural Evolution in Materials and Components by Neutron Diffraction Measurement at RSND

Sun

et al. 2018

QuBS

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Neutron diffraction is an effective and nondestructive method to investigate inner structure and stress distribution inside bulk materials and components. Compared with X-ray diffraction, neutron diffraction allows a relatively high penetration depth and covers a larger gauge volume, enabling it to measure the lattice structure and three-dimensional (3D) distribution of residual stress deep inside thick sample materials. This paper presents the recent development of a Residual Stress Neutron Diffractometer (RSND) at the

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Materials for High Temperature Engineering Applications

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Cited by 14 publications

References 0 publications

Breakdown and Evolution of the Protective Oxide Scales of AISI 304 and AISI 316 Stainless Steels under High-Temperature Oxidation

Breakdown and Evolution of the Protective Oxide Scales of AISI 304 and AISI 316 Stainless Steels under High-Temperature Oxidation

Transient stages during the chemical vapour deposition of silicon carbide from CH3SiCl3/H2: impact on the physicochemical and interfacial properties of the coatings

Recent Progress of Residual Stress Distribution and Structural Evolution in Materials and Components by Neutron Diffraction Measurement at RSND

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