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corrosion-fatigue cracking
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Image
Published: 01 December 1998
Fig. 3 Typical corrosion fatigue cracking of a copper alloy. Transgranular cracks originate at the base of corrosion pits on the roughened inner surface of a tube. Etched. Approximately 150×
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Published: 01 June 2024
Fig. 23 Typical corrosion fatigue cracking of a copper alloy. Transgranular cracks originate at the base of corrosion pits on the roughened inner surface of a tube. Etched. Original magnification: ~150×
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Published: 01 January 2005
Fig. 5 Typical corrosion fatigue cracking of a copper alloy. Transgranular cracks originate at the base of corrosion pits on the roughened inner surface of a tube. Etched. Original magnification approximately 150×
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Series: ASM Handbook
Volume: 13C
Publisher: ASM International
Published: 01 January 2006
DOI: 10.31399/asm.hb.v13c.a0004208
EISBN: 978-1-62708-184-9
... related to CF and SCC. biological response cobalt alloys corrosion fatigue dental amalgam stainless steels stress-corrosion cracking titanium alloys AS THE FIELD OF BIOMATERIALS SCIENCE proceeds into the 21st century, many changes are taking place. Traditionally, biomaterials have been...
Abstract
This article provides information on biomedical aspects such as active biological responses and the chemical environment characterizing the internal physiological milieu, as well as electrochemical fundamentals needed for characterizing corrosion fatigue (CF) and stress-corrosion cracking (SCC). It discusses some of the mechanical and electrochemical phenomena related to the in vivo degradation of materials used for biomedical applications. These materials include stainless steels, cobalt and titanium-base alloy systems, and dental amalgam. The article addresses key issues related to the simulation of the in vivo environment, service conditions, and data interpretation. The factors influencing susceptibility to CF and SCC are reviewed. The article describes the testing methodology of CF and SCC. It also summarizes findings from laboratory testing, in vivo testing and retrieval studies related to CF and SCC.
Series: ASM Handbook
Volume: 23
Publisher: ASM International
Published: 01 June 2012
DOI: 10.31399/asm.hb.v23.a0005654
EISBN: 978-1-62708-198-6
... Abstract This article describes mechanical/electrochemical phenomena related to in vivo degradation of metals used for biomedical applications. It discusses the properties and failure of these materials as they relate to stress-corrosion cracking (SCC) and corrosion fatigue (CF). The article...
Abstract
This article describes mechanical/electrochemical phenomena related to in vivo degradation of metals used for biomedical applications. It discusses the properties and failure of these materials as they relate to stress-corrosion cracking (SCC) and corrosion fatigue (CF). The article presents the factors related to the use of surgical implants and their deterioration in the body environment, including biomedical aspects, chemical environment, and electrochemical fundamentals needed for characterizing CF and SCC. It provides a discussion on the use of metallic biomaterials in surgical implant applications, such as orthopedic, cardiovascular surgery, and dentistry. It addresses key issues related to the simulation of an in vivo environment, service conditions, and data interpretation. These include the frequency of dynamic loading, electrolyte chemistry, applicable loading modes, cracking mode superposition, and surface area effects. The article explains the fundamentals of CF and SCC, and presents the test findings from laboratory, in vivo, and retrieval studies.
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Published: 01 January 1996
Fig. 8 Typical corrosion-fatigue crack growth data for chemically small cracks and large cracks. Source: Ref 20
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Published: 01 January 1996
Fig. 25 The effect of chloride on the corrosion fatigue crack initiation resistance of notched steel specimens. r , notch tip radius. Source: Ref 20
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Published: 01 January 1996
Fig. 67 Effect of composition on corrosion fatigue crack growth rates for three different high-strength steels. The steels were tested in air and in a 3% aqueous solution of sodium-chloride at 0.1 Hz Source: Ref 17
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Published: 01 January 1996
Fig. 29 Corrosion fatigue crack growth data for two austenitic stainless steels in normal BWR water compared with A508 steel. The solid and dashed lines are from Section 11 of the ASME Boiler and Pressure Vessel Code and are intended to represent the upper bounds for fatigue crack growth data
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Published: 01 January 1996
Fig. 1 Various sequential processes involved in corrosion fatigue crack growth in alloys exposed to aggressive environments. Source: Ref 1
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Published: 01 January 1996
Fig. 10 Effect of load ratio on the corrosion fatigue crack growth rates of MF-80 HSLA in 3.5% NaCl solution. Source: Ref 10
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Published: 01 January 1996
Fig. 15 Effect of cyclic load waveform on the corrosion fatigue crack growth rates of 15Ni-5Cr-3Mo steel in 3% NaCl solution. Source: Ref 12
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Published: 01 January 1996
Fig. 16 Effect of temperature on the corrosion fatigue crack growth rate of a metastable austenitic steel in distilled water. Source: Ref 13
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Published: 01 January 1996
Fig. 1 Room-temperature corrosion fatigue crack growth rates. (a) Effect of environment on fatigue crack propagation in 4130 steel with a yield strength of 1330 MPa (195 ksi). The band of data about the moist air line represents cracking in 13 steels with varying microstructures and yield
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Published: 01 January 1996
Fig. 8 Corrosion fatigue crack growth rates for A533B low-alloy steel (ASME grade SA533B-1, 0.025% S) in 288 °C pure water. Environmental enhancement is not uniform but reaches a maximum under intermediate Δ K , R , and frequency conditions. Source: Ref 8 , 9
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Published: 01 January 1996
Fig. 11 Modeled effect of loading frequency on corrosion fatigue crack growth in alloy steels in an aqueous chloride solution. The determination of the normalized crack growth rate and the time constants, τ o , from the model can be found in Ref 24 .
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Published: 01 January 1996
Fig. 12 The effect of solution flow rate on the corrosion fatigue crack growth rate of a medium-sulfur, low-alloy steel tested in deaerated 288 °C (550 °F) water. Tests at high flow rate on the 3-side-open compact-type specimens permit the aggressive crack chemistry to be flushed out, reducing
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Published: 01 January 1996
Fig. 13 Cycle-based corrosion fatigue crack growth rates vs. time for an SA333-grade 6 ASME carbon steel tested in 97 °C water. At 0.1 ppm dissolved oxygen, the corrosion rate is low, the crack tip remains sharp, and cracking is sustained. At 1.5 ppm dissolved oxygen, considerable corrosion
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Published: 01 January 1996
Fig. 15 Corrosion fatigue crack growth rates plotted for medium-sulfur A533B and A508-2 low-alloy steels and weldments in 288 °C deaerated (pressurized water reactor primary) water. Data show a stronger environmental effect at R = 0.7 than at R = 0.2. Source: Ref 8 , 9
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Published: 01 January 1996
Fig. 7 Corrosion-fatigue crack growth curves for ZK60A-T5 in different environments. Source: Ref 8
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