Issue 24

Yu. G. Matvienko, Frattura ed Integrità Strutturale, 24 (2013) 119-126; DOI: 10.3221/IGF-ESIS.24.13 120 noted that the most essential results on the numerical analysis of the effect of cyclic loading on hydrogen diffusion and concentration around a crack tip was published by A.T. Yokobori et al. [15]. In this research, experimental analysis of the distribution of hydrogen concentration ahead of the crack tip in the martensitic high strength steel under hydrogen induced cracking and fatigue I mode loading conditions has been carried out. The generalized concept of damage evolution has been employed to explain fatigue crack propagation in connection with the hydrogen redistribution ahead of the crack tip. The physical criterion of local failure based on the hydrogen peak in the fracture process zone and the maximum stress intensity factor has been suggested. E XPERIMENTAL PROCEDURES he martensitic high strength steel is investigated to analyse the effect of hydrogen charge on the fracture toughness, the fatigue crack growth rate and the distribution of hydrogen concentration ahead of the crack tip. The fraction of retained austenite in the steel did not exceed 10%. Chemical composition of the studied steels is given in Tab. 1. Mechanical properties of the steel at room temperature are the following: the Young’s modulus E=210 GPa, yield strength y  =850 MPa and ultimate strength u  =1150 MPa. C Cr Ni Si Mn P S 0.06 16 7 <0.8 <0.8 <0.03 <0.02 Table 1 : Chemical composition of high strength steel (weight %). The hydrogen-charged and pre-fatigued specimens were employed. Hydrogen was artificially charged into specimens by a cathodic charging method before the tests. The solution used for the cathodic charging was a 10 mass% H 2 SO 4 aqueous solution with an addition of SeO 2 . The current density was i =1 A/dm 2 and charging time was 5 hours. Prior to immersing the specimen in the solution, its surface (with the exception of the crack surface) was coated with a chemically stable lacquer. The testes were carried out on HUS-1025 machine at room temperature in laboratory air. The fracture toughness C K was measured using compact-tension specimens (60x60 mm) with 5 mm thickness according to the standard method reported in the ASTM Standard E399. The fatigue crack growth tests were conducted in order to clarify the hydrogen effect on fatigue crack growth behaviour and the distribution of hydrogen concentration ahead of the fatigue crack tip. Rectangular specimens 50 mm high and 5 mm thick with an edge crack loaded in cantilever bending were employed. The loading frequency was 20 Hz with a constant amplitude sinusoidal waveform for the applied load. The stress ratio was maintained at R =-0.3. The length of a growing fatigue crack was recorded by an optical microscope. At the given load or fatigue crack length the specimen was unloaded and 10x10 mm templates, which included the zone of the crack tip, were cut out from it. Template sizes were caused by sizes of the analytical chamber of the mass spectrometer. The secondary ion mass spectrometry method was then used to analyse the distribution of hydrogen in the zone of the crack tip and at its edges [12]. The small size of the analysed area (5 m  ) was ensured using a molybdenum diaphragm placed on the specimen. Prior to this, molybdenum was degassed in vacuum. The sensitivity of analysis for hydrogen was 10 -2 cm 3 /100 g. The reproducibility of the results of determining the intensities of the spectral lines was high. The mass spectrometric results were calibrated using reference specimens employed in installations for vacuum heating manufactured by LECO Company with linear grain sizes in the metal larger than 30 m  . This eliminated the apparatus error in recording local hydrogen concentrations associated with segregations of hydrogen at the grain boundary in the reference specimen since the size of the ion beam in analysis was smaller than the size of the grain within which the distribution of hydrogen was usually uniform. It should be noted that secondary ion mass spectrometry was successfully employed for an analyses of the hydrogen distribution around the fatigue crack on type 304 stainless steel [16]. According to the reported data [17], the fatigue crack growth is accompanied by microplastic deformation and formation of hydrogen collectors and traps. This greatly reduces the diffusion mobility of hydrogen in the zone of the crack tip. The curve of hydrogen distribution through thickness for the specimen during removal of layers of the material was constructed (Fig. 1). It can be seen that the position of the maximum hydrogen concentration remains unchanged in specimens with different crack lengths. After finding the depth with the maximum concentration of hydrogen, the distribution of hydrogen ahead of the fatigue crack tip was measured at this depth. T