Metal-Liquid Reactions: Corrosion

Pryor, M. J.; Staehle, R. W.

doi:10.1007/978-1-4684-8082-5_9

Cited by 5 publications

(7 citation statements)

References 103 publications

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“…4, 5, 7-9 and summarized in Table II are considered for consistency with leading models for passive film breakdown. The kinetic data presented in this paper are inconsistent with the adsorption-displacement models (28)(29)(30)(31)(32)(33), the chemico-mechanical models (34)(35)(36) or the hydrated polymeric oxide models (37-40) but are consistent with the ion exchange processes (41)(42)(43), the point defect (44) or pore models (45,46) for passive film breakdown. A first step in the localized corrosion process is certainly the inhomogeneous chemisorption of the C1-ions, causing an increase of the dissolution rate.…”

Section: Discussioncontrasting

confidence: 77%

“…The unfavorable influence of C1 ions on the corrosion pit can be explained in terms of a modification in the defect structure of barrier layer (17,48). In this modification, C1-ions replace 02-in the oxide lattice (17,(41)(42)(43). A reaction order of unity with regard to chloride ion is consistent with this view and appears contradictory with the view demanding an order equal to the number of C1-in the complex.…”

Section: Discussionmentioning

confidence: 97%

“…The presence of halide ions will greatly enhance cation diffusion and hence, will accelerate film breakdown. It is suggested that C1-from solution replace some O 2-in the oxide lattice (41)(42)(43). The charge imbalance so created can be neutralized by one Cu+-ion passing into solution for each C1-substitution, thereby creating an additional neutral cation vacancy.…”

Section: Discussionmentioning

confidence: 99%

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Passive Films on 90Cu‐10Ni Alloy: The Mechanism of Breakdown in Chloride Containing Solutions

Milošev¹,

Metikoš‐Huković²

1991

J. Electrochem. Soc.

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The complex electrochemical behavior of 90Cu-10Ni alloy in borate buffer solutions containing chloride ions involves Cu oxide formation, passivity onset, and pitting corrosion. The nature of the processes occurring was studied using electrochemical techniques complemented with SEM and EDXA. The overall process can be described by two competing processes: formation and growth of the duplex oxide passive film and formation of the CuC1 layer. The CuC1 layer is poorly protective and when the applied potential exceeds a certain critical value, pitting corrosion takes place. The change in both the kinetics and the morphology indicates that at least three stages should be distinguished in the pitting process: adsorption of C1-ions, pit nucleation, and pit growth. The physical interpretation of the proposed model of passive film breakdown is consistent with its duplex structure, and is discussed in terms of the various conditions leading to nucleation and growth of pits. Experimental kinetic parameters of the passive film breakdown are presented.

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Section: Discussioncontrasting

confidence: 77%

Section: Discussionmentioning

confidence: 97%

Section: Discussionmentioning

confidence: 99%

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Passive Films on 90Cu‐10Ni Alloy: The Mechanism of Breakdown in Chloride Containing Solutions

Milošev¹,

Metikoš‐Huković²

1991

J. Electrochem. Soc.

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“…Based on DE, temper T4 of the alloy Al 6013-20 SiC(P) showed a higher resistance to pitting than The subject of thinning of oxide films in NaCl solution has been extensively investigated on aluminium alloys since 1973. [22][23][24][25] It was observed that aluminium oxide film thins down on exposure in NaCl solution. However, no conclusive mechanism has been suggested for thinning of oxide films in sodium chloride solution.…”

Section: Electrochemical Studiesmentioning

confidence: 99%

Corrosion behaviour of aluminium Al 6013-20 SiC(P) at controlled velocities and elevated temperatures

Aleem

Ahmad

2009

Corrosion Engineering, Science and Technology

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The corrosion behaviour of aluminium alloy 6013-20 SiC(P) at controlled velocities and elevated temperatures was investigated by electrochemical studies. The alloy in temper T4 (solution treated, quenched and naturally aged) showed a higher resistance to corrosion compared to the annealed and as fabricated tempers. It exhibited a decreased resistance to corrosion in 3?5 wt-% NaCl solution containing suspended polystyrene particles at solution velocities 1-3 m s 21 . No significant reduction in corrosion resistance was observed in environmental chamber studies. Alloy Al 6013-20 SiC(P) offered good resistance to corrosion in salt spray chamber. The secondary phase intermetallic precipitates were the preferred sites for localised corrosion.

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“…However, if the electrical potential is over 200 mV, galvanic corrosion could result. 12 During orthodontic treatment, brackets are coupled to orthodontic arch wires made of SS and NiTi alloys and recent laboratory electrochemical studies have recorded high galvanic values when dissimilar alloy brackets and arch wires are in contact. [13][14][15] This indicates an active process, leading to metal ion loss.…”

Section: Introductionmentioning

confidence: 99%

Galvanic coupling and mechanical properties of low Ni orthodontic brackets with representative types of orthodontic wires

Kummer

Polychronis

Zinelis

et al. 2019

Australasian Orthodontic Journal

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To characterise the mechanical properties and galvanic coupling of Ni-free orthodontic brackets with stainless steel (SS) and Nickel-Titanium (NiTi) orthodontic wires. Methods: Three Ni-free bracket types (Topic [TOP], Equilibrium [EQU] and Orthos [ORT] made of Ni-free alloys), one conventional (Mini 2000 [MIN]) made of SS alloy and an SS and a NiTi wire were examined in the present study. All brackets and wires were embedded in epoxy resin and, after metallographic grinding and polishing, the Martens hardness (HM), the indentation modulus (E IT ), and the elastic index (η IT ) were recorded, employing Instrumented Indentation Testing (IIT) by monitoring force over indentation depth curves during a loading-unloading cycle. The galvanic coupling of all bracket-wire combinations was tested in 0.1M NaCl-0.1M lactic acid and 0.3% (wt.) NaF solutions by noting the potential differences over 48 hours. The mechanical properties were statistically analysed by one-way ANOVA and Tukey multiple comparison tests at alpha = 0.05. Results: Significant differences were identified in the mechanical properties of the materials tested. The TOP (2372 ± 182 N/ mm 2 ), ORT (wing) (2418 ± 164) and SS wire (2302 ± 85) showed significantly higher HM compared with all other materials tested. The MIN (base) (1115 ± 81) and ORT (base) (1237 ± 101) showed the lowest HM while MIN (wing) (1520 ± 138), EQU (1620 ± 139) and NiTi wire (1526 ± 42) demonstrated intermediate HM values. The ORT (wing) (101 ± 6 GPa) displayed the highest E IT while NiTi wire (24 ± 5) showed the lowest. The latter had the highest elastic index (59 ± 5%) with MIN (base)(15 ± 3) possessing the lowest. The potential difference for all bracket wire combinations was found below the threshold for the initiation of galvanic corrosion (200 mV) apart from MIN coupled with NiTi wire in the NaF solution. Conclusions: The mechanical properties of Ni-free brackets are significantly different compared with the SS bracket assessed. Galvanic testing revealed that conventional and Ni-free brackets are compatible with both SS and NiTi wires in media containing chloride and fluoride ions.

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Metal-Liquid Reactions: Corrosion

Cited by 5 publications

References 103 publications

Passive Films on 90Cu‐10Ni Alloy: The Mechanism of Breakdown in Chloride Containing Solutions

Passive Films on 90Cu‐10Ni Alloy: The Mechanism of Breakdown in Chloride Containing Solutions

Corrosion behaviour of aluminium Al 6013-20 SiC(P) at controlled velocities and elevated temperatures

Galvanic coupling and mechanical properties of low Ni orthodontic brackets with representative types of orthodontic wires

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