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Search Results for SCC
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Book Chapter
Series: ASM Failure Analysis Case Histories
Publisher: ASM International
Published: 01 June 2019
DOI: 10.31399/asm.fach.aero.c0048665
EISBN: 978-1-62708-217-4
.... It was concluded that stress-corrosion cracks grew out from the rust pits. The pin material was changed from 300M steel to PH 13-8 Mo stainless steel, which is highly resistant to rusting and SCC and the jacking control system was modified to prevent overdriving. Landing gear Materials substitution Pitting...
Abstract
The jackscrew drive pins on a landing-gear bogie failed when the other bogie on the same side of the airplane was kneeled for tire change. The pins, made of 300M steel, were shot peened and chromium plated on the outside surface and were cadmium plated and painted with polyurethane on the inside surface. The top of the jackscrew was 6150 steel. Both ends of the pins were revealed to be dented where the jackscrew had pressed into them and were observed to have been resulted due to overdriving the jackscrew at the end of an unkneeling cycle. These dented areas were found to be heavily corroded with chromium plating missing. A heavily corroded intergranular fracture mode was revealed by chromium-carbon replicas of the areas of fracture origin. Deep corrosion pits adjacent to the fracture origins and directly beneath cracks in the chromium plate were revealed by metallographic examination. It was concluded that stress-corrosion cracks grew out from the rust pits. The pin material was changed from 300M steel to PH 13-8 Mo stainless steel, which is highly resistant to rusting and SCC and the jacking control system was modified to prevent overdriving.
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Published: 01 January 2002
Fig. 9 Microstructures of stainless steel bolts that failed from SCC. (a) Branched intergranular cracking in a type 410 stainless steel bolt from lot 1 (see Example 4 ). Etched with picral plus HCl. 250×. (b) Microstructure of a type 416 stainless steel bolt typical of those in lots 2 and 3
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Published: 01 January 2002
Fig. 10 AISI type 431 stainless steel T-bolt that failed by SCC. (a) T-bolt showing location of fracture. Dimensions given in inches. (b) Fracture surface of the bolt showing shear lip (arrow A), fine-grain region (arrow B), and oxidized regions (arrows C). (c) Longitudinal section through
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Published: 01 January 2002
Fig. 23 300M steel jackscrew drive pins that failed by SCC. (a) Four views of aft-pin locations of individual origins (numbers), directions of fracture (arrows), and final-fracture regions (wavy lines). (b) Same as (a) except for forward pin. (c) Top surface of forward pin showing slight bend
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Published: 01 January 2002
Fig. 36 Section through type 316 stainless steel tubing that failed by SCC because of exposure to chloride-contaminated steam condensate. Micrograph shows a small transgranular crack that originated at a corrosion pit on the inside surface of the tubing and only partly penetrated the tubing
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Published: 01 January 2002
Fig. 21 Large enclosed cylindrical pressure vessel that failed by SCC because of caustic embrittlement by potassium hydroxide. (a) View of vessel before failure and details of nozzle and tray support. Dimensions given in inches. (b) Micrograph showing corrosion pits at edge of fracture surface
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Published: 01 January 2002
Fig. 22 Chloride SCC in a type 347 stainless steel shaft in a hydrogen-bypass valve.
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Published: 01 January 2002
Fig. 16 Appearance of fracture surface of line pipe that failed by SCC. Actual size. See also Fig. 17 , 18 , and 19 .
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Published: 01 January 2002
Fig. 9 Corrosion products on the grain facets from SCC of a U-700 turbine blade, presumably from combustion-gas attack that induced SCC, with IG and transgranular modes shown
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Published: 01 January 2002
Fig. 16 Beach marks on a 4340 steel part caused by SCC. Tensile strength of the steel was approximately 1780 to 1900 MPa (260 to 280 ksi). The beach marks are a result of differences in the rate of penetration of corrosion on the surface. They are in no way related to fatigue marks. 4×
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Published: 01 January 2002
Fig. 1 Branching cracks typical of stress-corrosion cracking (SCC). (a) Chloride SCC of type 304 stainless steel base metal and type 308 weld metal in an aqueous chloride environment at 95 °C (200 °F). Cracks are branching and transgranular. (b) Caustic SCC in the HAZ of a type 316L stainless
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Published: 01 January 2002
Fig. 3 Relative SCC behavior of austenitic stainless steels in boiling magnesium chloride. Source: Ref 11
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Published: 01 January 2002
Fig. 5 Branching cracks typical of SCC. Cracking occurred in the work-hardened neck regions of a type 316L stainless steel screen that was exposed to printing press exhaust fumes containing toluene, sulfur, chlorine, phosphorus, moisture, and other impurities. (a) Unetched, picture width ∼6 mm
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Published: 01 January 2002
Fig. 9 Silicon bronze contact-finger retainer that failed from SCC in shipboard service. (a) Overall view of retainer showing cracking in corner (arrow). (b) Specimen taken from failure region showing secondary cracks (arrows). Etched with equal parts NH 4 OH and H 2 O 2 . 250×
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Published: 01 January 2002
Fig. 14 Comparison of SCC and corrosion fatigue cracks in copper alloy C26000 (cartridge brass, 70%). (a) Typical intergranular stress-corrosion cracks in tube that was drawn, annealed, and cold reduced 5%. The cracks show some branching. H 4 OH plus H 2 O etch, 150×. (b) Typical transgranular
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Published: 01 January 2002
Fig. 15 Surface of a fracture in type 316 stainless steel resulting from SCC by exposure to a boiling solution of 42 wt% MgCl 2 . The fracture in general exhibited the fan-shaped or feather-shaped transgranular cleavage features shown in (a). In a hasty scrutiny, the presence of local areas
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Published: 01 January 2002
Fig. 19 Micrograph showing tight intergranular SCC originating at the inside surface of a pipe
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Published: 01 January 2002
Fig. 20 Scanning electron micrograph showing intergranular SCC (A) and initiation sites for pitting (B) on the inside surface of a pipe
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Published: 01 January 2002
Fig. 21 Nital-etched specimen of ASTM A 245 carbon steel. Micrograph shows SCC that occurred in a concentrated solution of ammonium nitrate. 100×
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Published: 01 January 2002
Fig. 27 AISI type 316 stainless steel piping that failed by SCC at welds. Cracking was caused by exposure to condensate containing chlorides leached from insulation. (a) View of piping assembly showing cracks on inner surface of cone. Dimensions given in inches. (b) Macrograph of an unetched
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