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Commerce Max Load Pro Crack
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where da/dN is the incremental crack extension per cycle, A and m are constants, and ΔK is the cyclic stress intensity range. The FCGR in Region 2 is governed mainly by crack tip stress intensity levels, but can be affected by testing variables such as stress ratio (R = Kmin/Kmax) . As a fatigue crack grows, Kmax increases to the point where it is essentially equivalent to the critical stress intensity for unstable crack growth (KC), or KIC if the crack is propagating under plane strain conditions. Fatigue crack growth in Region 3 occurs as KIC is approached, and is characterized by significant increases in growth rates.
Diffusional transport of atomic hydrogen depends on the hydrogen fugacity (function of gas pressure) at the crack tip, the kinetics of the dissociation reaction, and the concentration (activity) and stress field in the steel near the crack tip. The HEDE mechanism envisions a loss in cohesive strength within this hydrogen enriched region as a mechanism for crack advance, and except for the high mobility of atomic hydrogen, has much in common with embrittlement of grain boundaries by segregated impurities. While the mechanics and kinetics of crack propagation in a wide variety of hydrogen rich environments are consistent with the HEDE mechanism, detailed understanding of exactly how the hydrogen enrichment decreases fracture strength is lacking.
Several key relationships between hydrogen embrittlement, FCG, and FCG testing variables were accounted for in the research conducted by Cialone and Holbrook. Testing variables that may affect FCG in hydrogen include frequency, pressure, stress ratio, alloy microstructure, and strength. Each of these variables will be addressed individually in subsequent sections. Baseline results for fatigue crack growth rates in hydrogen and nitrogen for X42 and X70 alloys at gas pressures of 6.9 MPa (1,000 psi), stress ratio of 0.1 and frequency of 1 Hz are provided in Fig. 5. The investigators reported little dependence of FCG on cyclic frequencies between 0.1 Hz and 10 Hz and therefore performed most of their tests at 1 Hz. The FCGR were determined over stress intensity ranges between 20 MPa m1/2 and 70 MPa m1/2. The baseline test results for the X42 pipeline steel in hydrogen exhibited FCGR increases of up to 150 times those observed in nitrogen at stress intensity ranges near 20 MPa m1/2. At lower stress intensities, the deviation in FCGR between the hydrogen and inert environments decreased, indicating that the threshold stress values may be less affected by hydrogen. FCGR for the X70 alloy were also accelerated in the high pressure gaseous hydrogen environment, but the increases were about half of those exhibited by the X42 alloy.
The stress intensity range, ΔK, is generally considered to be the primary variable controlling fatigue crack growth in both inert and hydrogen environments . The magnitude of enhancement in the FCGR is proportional to approximately the square of the maximum stress intensity for constant frequency and load ratio , and recall that for fixed R, the maximum stress intensity is directly proportional to the stress intensity range (Eq. 3). Other variables that are relevant to quantitative FCGR models are; loading frequency, stress ratio, loading waveform, temperature, and stress intensity range. In order to relax codes for steel pipelines in hydrogen service, type II crack propagation as a function of loading frequency and gas pressure should be the starting point. Then, in decreasing order of importance would be stress ratio, temperature, and loading waveform.
The kinetics of HA-FCG do however depend on the stress waveform and stress ratio, at least for high-strength steels . Nothing unusual is reported when the stress intensity is above the threshold for stress corrosion cracking. However, for FCG below the threshold value of stress intensity for stress corrosion cracking and for low stress ratios, hydrogen has a much smaller effect on FCG when fast-rising waveforms are used than when slow-rising waveforms (e.g., sinusoidal waveforms) are used. On the other hand, FCGR in hydrogen environments at high stress ratios is largely independent of whether fast-rising or slow-rising wave forms are used. At high stress ratios, this is to be expected, as high load ratios have relatively small changes in loading, where the limit mimics static loading.
Agreement has still not been reached on whether hydrogen diffusion or surface reactivity is the rate-limiting factor for HA-FCG in steel. Models based on either being the rate-limiting step can be found [46, 52, 53]. To date, most of these analyses have been applied to HA-FCGR data obtained in aqueous environments. Frequency effects due to the enhancement of cracking due to hydrogen may be modeled by use of exponential functions of the inverse of frequency of the form [53, 54]
where Q is a rate constant and f is the loading frequency. Temperature effects are generally accounted for in the rate constant, where an Arrhenius-type expression is typically used so that an apparent activation energy can be determined for the process. However, determination of these rates for the cases of strained material near a crack tip, and the relationship between gas environment and electrochemical environments have yet to be convincingly demonstrated.
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