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Journal articles on the topic 'High cycle fatigue'

Author: Grafiati

Published: 4 June 2021

Last updated: 7 July 2024

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1

Matikas, T. E. "A high-cycle fatigue apparatus at 20 kHz for low-cycle fatigue/high-cycle fatigue interaction testing." Fatigue & Fracture of Engineering Materials & Structures 24, no. 10 (October 2001): 687–97. http://dx.doi.org/10.1046/j.1460-2695.2001.00427.x.

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2

SHI, Jin-yuan, Yong WANG, Wang-fan LI, Zhi-cheng DENG, and Yu Yang. "ICOPE-15-C035 Crack Propagation Life under Low Cycle Fatigue and High Cycle Fatigue of Nuclear Steam Turbine Rotors." Proceedings of the International Conference on Power Engineering (ICOPE) 2015.12 (2015): _ICOPE—15——_ICOPE—15—. http://dx.doi.org/10.1299/jsmeicope.2015.12._icope-15-_131.

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3

He, Chao, Yong Jie Liu, and Qing Yuan Wang. "Very High Cycle Fatigue Properties of Welded Joints under High Frequency Loading." Advanced Materials Research 647 (January 2013): 817–21. http://dx.doi.org/10.4028/www.scientific.net/amr.647.817.

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Very high cycle fatigue (VHCF) properties of welded joints under ultrasonic fatigue loading have been investigated for titanium alloy (TI-6Al-4V) and bridge steel (Q345). Ultrasonic fatigue tests of base metal and welded joints were carried out in ambient air at room temperature at a stress ratio R=-1. It was observed that the fatigue strength of welded joints reduced by 50-60% as compared to the base metal. The S-N fatigue curves in the range of 107~109 cycles of base metal and welded joints for both materials exhibited the characteristic of continually decreasing type. The fatigue failure still occurred after 107 cycles of loading, and the fatigue limit in traditional does not exist. The fatigue facture mainly located in the weld metal region at low cycle fatigue range, but in the fusion area in HCF and VHCF. Analysis of fracture surfaces analyzed by SEM revealed that the fatigue cracks initiated from welding defects such as pores, cracks and inclusions.

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4

Li, Xin. "A new stress-based multiaxial high- cycle fatigue damage criterion." Functional materials 25, no. 2 (June 27, 2018): 406–12. http://dx.doi.org/10.15407/fm25.02.406.

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5

Šulák, Ivo, Karel Obrtlík, and Ladislav Čelko. "High Temperature Low Cycle Fatigue Characteristics of Grit Blasted Polycrystalline Ni-Base Superalloy." Key Engineering Materials 665 (September 2015): 73–76. http://dx.doi.org/10.4028/www.scientific.net/kem.665.73.

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The present work is focused on the study of low cycle fatigue behavior of grit blasted nickel-base superalloy Inconel 713LC (IN 713LC). Grit blasting parameters are obtained. Button end specimens of IN 713LC in as-received condition and with grit blasted surface were fatigued under strain control with constant total strain amplitude in symmetrical cycle at 900 °C in air. Hardening/softening curves, cyclic stress-strain curve and fatigue life data of both materials were obtained. Both materials exhibit the same stress-strain response. It has not been observed any improvement or reduction of low cycle fatigue life in representation of total strain amplitude versus number of cycles to failure of grit blasted material in comparison with as-received material. Surface relief and fracture surface were observed in SEM. The little effect of surface treatment on fatigue characteristics is discussed.

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6

Zhang, Wei Chang, Ming Liang Zhu, and Fu Zhen Xuan. "Experimental Characterization of Competition of Surface and Internal Damage in Very High Cycle Fatigue Regime." Key Engineering Materials 754 (September 2017): 79–82. http://dx.doi.org/10.4028/www.scientific.net/kem.754.79.

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Axially push-pull cyclic tests of a low strength rotor steel were performed up to the very high cycle fatigue regime at ambient environment under ultrasonic frequency. Fatigue tests were interrupted at selected number of cycles for surface morphology observation and roughness measurement with the help of a 3D surface measurement system (Alicona InfiniteFocusSL). The fatigue extrusions and slip band developed on the specimen surface were recorded. The influence of stress level on the number and morphology of slip band was discussed. The surface roughness of fatigue specimens was found to be increased with the increasing of fatigue cycles. The fatigued specimens were finally cracked from surface or interior micro-defects after observation of fracture surface by scanning electron microscopy. The internal damage behavior consists of crack initiation and early propagation from micro-defect, crack growth within the fish eye, and fast crack growth. It is observed that there exists a competition between surface and internal fatigue damage in the very high cycle fatigue regime, i.e., surface damage is gradually developed with the increasing of fatigue cycles, while the critical interior micro-defect can be dominant for fatigue cracking.

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7

Heinz, Stefan, and Dietmar Eifler. "Very High Cycle Fatigue and Damage Behavior of Ti6Al4V." Key Engineering Materials 664 (September 2015): 71–80. http://dx.doi.org/10.4028/www.scientific.net/kem.664.71.

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High frequency fatigue tests were carried out with a 20 kHz ultrasonic testing facility to investigate the cyclic deformation behavior of Ti6Al4V in the Very High Cycle Fatigue (VHCF) regime in detail. The S,Nf -curve at the stress ratio R = -1 shows a significant decrease of the stress amplitude and a change from surface to subsurface failures in the VHCF regime for more than 107 cycles. Microscopic investigations of the distribution of the α-and β-phase of Ti6Al4V indicate that inhomogeneities in the phase distribution are reasons for the internal crack initiation. Scanning electron microscopy as well as light microscopy were used to investigate the internal crack initiation phenomenon in the VHCF-regime. Beside the primary fatigue crack additional defects like micro cracks and crack clusters were observed in the fatigued specimens. SEM-investigations of specimens which were loaded up to 1010 cycles without failure show irreversible microstructural changes inside the specimens. Two step tests were performed to evaluate the influence of internal fatigue induced defects observed in specimens which did not fail within 1010 cycles.

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8

Abdel Wahab, Magd, Irfan Hilmy, and Reza Hojjati-Talemi. "On the Use of Low and High Cycle Fatigue Damage Models." Key Engineering Materials 569-570 (July 2013): 1029–35. http://dx.doi.org/10.4028/www.scientific.net/kem.569-570.1029.

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In this paper, Continuum Damage Mechanics (CDM) theory is applied to low cycle and high cycle fatigue problems. Damage evolution laws are derived from thermodynamic principles and the fatigue number of cycles to crack initiation is expressed in terms of the range of applied stresses, triaxiality function and material constants termed as damage parameters. Low cycle fatigue damage evolution law is applied to adhesively bonded single lap joint. Damage parameters as function of stress are extracted from the fatigue tests and the damage model. High cycle fatigue damage model is applied to fretting fatigue test specimens and is integrated within a Finite Element Analysis (FEA) code in order to predict the number of cycles to crack initiation. Fretting fatigue problems involve two types of analyses; namely contact mechanics and damage/fracture mechanics. The high cycle fatigue damage evolution law takes into account the effect of different parameters such as contact geometry, axial stress, normal load and tangential load.

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9

Drobne, Matej, Peter Göncz, and Srečko Glodež. "High Cycle Fatigue Parameters of High Chromium Steel." Key Engineering Materials 488-489 (September 2011): 299–302. http://dx.doi.org/10.4028/www.scientific.net/kem.488-489.299.

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The determination of monotonic mechanical properties and high cycle fatigue parameters of high chromium steel (HCS) is presented. The monotonic mechanical properties (ultimate compressive and ultimate tensile strength) are determined using standardized testing procedures according to DIN 50125 standard. The high cycle fatigue parameters are determined using uniaxial fatigue test where the tests specimens are loaded with pure pulsating compression load (load ratio R=0 in compression) at different load levels. Therefore, a typical S-N curve and appropriate fatigue parameters (fatigue strength coefficient sf’ and fatigue strength exponent b) are determined. The experimental results determined in this study can serve as a basis for the determination of service life of rolls using stress-life approach. However, a few guidelines for the further research work considering increased temperatures and multiaxial fatigue are given in the conclusions of this study.

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10

Alexander Araújo, José, Gabriel Magalhães Juvenal Almeida, Fábio Comes Castro, and Raphael Araújo Cardoso. "Multiaxial High Cycle Fretting Fatigue." MATEC Web of Conferences 300 (2019): 02002. http://dx.doi.org/10.1051/matecconf/201930002002.

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The aim of this work is to show that multiaxial fatigue can be successfully adpted to model fretting problems. For instance, the paper presents (i) the critical direction method, as an alternative to the critical plane concept, to model the crack initiation path under fretting conditions and (ii) studies on size effects considering the influence of incorporating fretting wear on the life estimation. A wide range of new data generated by a two actuators fretting fatigue rig considering Al 7050-T7451 and of Ti-6Al-4V aeronautical alloys is produced to validate these analyses. It is shown that, the development of appropriate tools and techniques to incorporate the particularities of the fretting phenomenon into the multiaxial fatigue problem allow an accurate estimate of the fretting fatigue resistance/life in the medium high cycle regime. Such tools and techniques can be extended to the design of other mechanical components under similar stress enviroments.

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11

Rodriguez, P., and S. L. Mannan. "High temperature low cycle fatigue." Sadhana 20, no. 1 (February 1995): 123–64. http://dx.doi.org/10.1007/bf02747287.

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12

Wu, Liang Chen, and Dong Po Wang. "Investigation of High Cycle and Low Cycle Fatigue Interaction on Fatigue Behavior of Welded Joints." Applied Mechanics and Materials 217-219 (November 2012): 2101–6. http://dx.doi.org/10.4028/www.scientific.net/amm.217-219.2101.

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Samples of Q345 steel welded joints were tested to failure under low cycle fatigue(LCF),high cycle fatigue(HCF) and combined fatigue(CCF) using an apparatus that is capable of providing interactive LCF/HCF loading. The stress ratio R is 0.5 and the frequency of HCF is about 19kHz. The result indicates that not only high frequency minor cycles superimposed on low frequency major cycles , but also low frequency minor cycles superimposed on high frequency major cycles can do remarkable damage to fatigue performance of welded joints. The CCF strength is characterized by amplitude envelope. If CCF fatigue life is characterized by LCF life, adverse effect of HCF component is underestimated. If CCF fatigue life is characterized by HCF life, adverse effect of LCF component is overrated.

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13

Calabrese, Angelo Savio, Tommaso D’Antino, Pierluigi Colombi, and Carlo Poggi. "Low- and High-Cycle Fatigue Behavior of FRCM Composites." Materials 14, no. 18 (September 18, 2021): 5412. http://dx.doi.org/10.3390/ma14185412.

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This paper describes methods, procedures, and results of cyclic loading tensile tests of a PBO FRCM composite. The main objective of the research is the evaluation of the effect of low- and high-cycle fatigue on the composite tensile properties, namely the tensile strength, ultimate tensile strain, and slope of the stress–strain curve. To this end, low- and high-cycle fatigue tests and post-fatigue tests were performed to study the composite behavior when subjected to cyclic loading and after being subjected to a different number of cycles. The results showed that the mean stress and amplitude of fatigue cycles affect the specimen behavior and mode of failure. In high-cycle fatigue tests, failure occurred due to progressive fiber filaments rupture. In low-cycle fatigue, the stress–strain response and failure mode were similar to those observed in quasi-static tensile tests. The results obtained provide important information on the fatigue behavior of PBO FRCM coupons, showing the need for further studies to better understand the behavior of existing concrete and masonry members strengthened with FRCM composites and subjected to cyclic loading.

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14

Kondo, Yoshiyuki, Chu Sakae, Masanobu Kubota, and Kazutoshi Yanagihara. "OS11W0383 Non-propagating crack at ultra high cycle fretting fatigue limit." Abstracts of ATEM : International Conference on Advanced Technology in Experimental Mechanics : Asian Conference on Experimental Mechanics 2003.2 (2003): _OS11W0383. http://dx.doi.org/10.1299/jsmeatem.2003.2._os11w0383.

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15

LUKÁŠ, P., and L. KUNZ. "Specific features of high-cycle and ultra-high-cycle fatigue." Fatigue & Fracture of Engineering Materials & Structures 25, no. 8-9 (September 2002): 747–53. http://dx.doi.org/10.1046/j.1460-2695.2002.00562.x.

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16

Shao, Chuang, Claude Bathias, Danièle Wagner, and Hua Tao. "Very High Cycle Fatigue Behavior and Thermographic Analysis of High Strength Steel." Advanced Materials Research 118-120 (June 2010): 948–51. http://dx.doi.org/10.4028/www.scientific.net/amr.118-120.948.

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Very high cycle fatigue behavior of high strength steel, were investigated using ultrasonic fatigue testing equipment at 20 kHz up to 109cycles. S-N curves at room temperature with different stress ratio (R=0.01 and R=0.1) was determined. The experimental results show that fatigue strength decrease with increasing number of cycles between 105 and 109. SEM examination of fracture surface reveals that fatigue damage was governed by the formation of cracks, and subsurface crack initiation was in the very long life range. The results shown that the portions of life attributed to subsurface crack initiation between 107 and 109 cycles are 99%.

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17

Bratasena, M. E., T. Kato, O. Umezawa, Y. Ono, and M. Komatsu. "High-cycle fatigue strength of 22Cr-12Ni austenitic stainless steel at 77 K." IOP Conference Series: Materials Science and Engineering 1302, no. 1 (May 1, 2024): 012001. http://dx.doi.org/10.1088/1757-899x/1302/1/012001.

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Abstract The high-cycle fatigue strength of 22Cr-12Ni austenitic stainless steel was evaluated at 77 K for three types of materials with partially recrystallized (PR), finely recrystallized (FR), and solution-treated (ST) microstructures. Subsurface crack initiation was detected at the lower stress level and/or higher cycles in the materials, such that the fatigue crack initiation sites were shifted from the specimen surface to the interior of the specimen with increasing cycles. The ST showed a significant decrease in fatigue strength over 106 cycles due to subsurface crack initiation. Both PR and FR showed a significant improvement in their high-cycle fatigue strength in the high-cycle regime, although the increase in fatigue strength in the low-cycle regime was approximately equal to the increase in tensile strength.

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18

Scott-Emuakpor, Onome, M. H. Herman Shen, Tommy George, Charles J. Cross, and Jeffrey Calcaterra. "Development of an Improved High Cycle Fatigue Criterion." Journal of Engineering for Gas Turbines and Power 129, no. 1 (March 1, 2004): 162–69. http://dx.doi.org/10.1115/1.2360599.

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An integrated computational-experimental approach for prediction of total fatigue life applied to a uniaxial stress state is developed. The approach consists of the following elements: (1) development of a vibration based fatigue testing procedure to achieve low cost bending fatigue experiments and (2) development of a life prediction and estimation implementation scheme for calculating effective fatigue cycles. A series of fully reversed bending fatigue tests were carried out using a vibration-based testing procedure to investigate the effects of bending stress on fatigue limit. The results indicate that the fatigue limit for 6061-T6 aluminum is approximately 20% higher than the respective limit in fully reversed tension-compression (axial). To validate the experimental observations and further evaluate the possibility of prediction of fatigue life, an improved high cycle fatigue criterion has been developed, which allows one to systematically determine the fatigue life based on the amount of energy loss per fatigue cycle. A comparison between the prediction and the experimental results was conducted and shows that the criterion is capable of providing accurate fatigue life prediction.

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19

Lanning, D., G. K. Haritos, T. Nicholas, and D. C. Maxwell. "Low-cycle fatigue/high-cycle fatigue interactions in notched Ti-6Al-4V*." Fatigue & Fracture of Engineering Materials & Structures 24, no. 9 (September 28, 2001): 565–77. http://dx.doi.org/10.1046/j.1460-2695.2001.00411.x.

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20

Huang, Zhiyong, Qingyuan Wang, Danièle Wagner, and Claude Bathias. "Effect of low cycle fatigue pre-damage on very high cycle fatigue." Theoretical and Applied Mechanics Letters 2, no. 3 (2012): 031007. http://dx.doi.org/10.1063/2.1203107.

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21

Nový, František, Libor Trško, Robert Ulewicz, and Sylvia Dundeková. "Influence of Electrodeposited Coatings on Ultra-High-Cycle Fatigue Life of S235 Structural Steel." Materials Science Forum 818 (May 2015): 37–40. http://dx.doi.org/10.4028/www.scientific.net/msf.818.37.

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The article deals with experimental results of fatigue life of plain carbon steel electrodeposited with nickel, chromium and iron-zinc coatings in the ultra-high-cycle region of loading (N = 6×106 ÷ 1010 cycles) obtained at high-frequency fatigue testing (f ≈ 20 kHz, T = 20 ± 5 °C, R = -1). The results confirm continuous decrease of S-N curves after N = 107 cycles. Electrodeposited coatings caused decrease of the fatigue life in the low and high-cycle fatigue region. In the ultra-high cycle region the influence of electrodeposited coatings on fatigue properties is negligible. There was observed no significant influence of thickness of electrodeposited coatings on fatigue lifetime decrease.

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22

Wei, Kang, and Bo Lin He. "Failure Mechanism of Very High Cycle Fatigue for High Strength Steels." Key Engineering Materials 664 (September 2015): 275–81. http://dx.doi.org/10.4028/www.scientific.net/kem.664.275.

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In recent years, the core engineering components of high-speed train, automobiles and aircrafts are required to endure fatigue loads up from 108 to 1010 cycles. The present study results show that in the very high cycle fatigue (VHCF) regimes of more than 107 cycles, the fatigue failure of high strength steel materials can occur below the traditional fatigue limit, hence the VHCF investigations of high strength steels not only help to further understand the fatigue essence and mechanism, but also do research on the fatigue design and life assessment method. This paper summarizes works of VHCF researches for high strength steels in recent years, such as the characteristics of S-N curve, the observations on fish-eye, which is one of the typical characteristics of fracture surface, crack initiation, crack propagation, etc. The present work also analyzes the fatigue mechanisms and briefly discusses several factors that affect VHCF properties, such as hydrogen effect, inclusion effect, frequency effect. Some possible and prospective aspects of future researches are also proposed.

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23

Issler, Stephan, Manfred Bacher-Hoechst, and Steffen Schmid. "Fatigue Designing of High Strength Steels Components Considering Aggressive Fuel Environment and Very High Cycle Fatigue Effects." Materials Science Forum 783-786 (May 2014): 1845–50. http://dx.doi.org/10.4028/www.scientific.net/msf.783-786.1845.

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Automotive components for injection systems are subjected to load spectra with up to 1E9 load cycles during the expected service life. However, fatigue testing with such a large number of cycles using original components is extremely time-consuming and expensive. A contribution for fatigue reliability assessment is available by the application of specimen testing and the transfer of the results to components including the verification by component spot tests.In this contribution very high cycle fatigue results in laboratory air and in ethanol fuel using notched specimens of high strength stainless steel are discussed. The influence of testing frequency was studied using ultrasonic and conventional test techniques. The validation and transfer of these accelerated testing results to components is one of the main challenges for a reliable fatigue designing.KeywordsVery High Cycle Fatigue (VHCF), automotive components, fuel injection, bio-fuels, corrosion fatigue, testing concepts, fatigue design concepts

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24

Nie, Xu Tao, Wan Hua Chen, and Yuan Xing Wang. "Numerical Simulation Study on High-Cycle Fatigue Damage for Metals." Advanced Materials Research 941-944 (June 2014): 1477–82. http://dx.doi.org/10.4028/www.scientific.net/amr.941-944.1477.

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High-cycle fatigue damage analysis and life prediction is a most crucial problem in the research field of solid mechanics. Based on the thermodynamic potentials in the framework of thermodynamics a numerical method for high-cycle fatigue damage was studied and provided by using a two-scale damage model. Furthermore, according to the “jump-in-cycles” procedure the numerical simulation of high-cycle fatigue damage was implemented in a user subroutine of ABAQUS software. Finally, a numerical simulation instance of high-cycle fatigue damage was provided and compared with a set of test data, which indicates that the numerical simulation method presented is reasonable and applicable.

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25

Hong, You Shi, and Gui An Qian. "Effect of Aqueous Environment on High Cycle and Very-High-Cycle Fatigue Behavior for a Structural Steel." Key Engineering Materials 462-463 (January 2011): 355–60. http://dx.doi.org/10.4028/www.scientific.net/kem.462-463.355.

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In this paper, rotary bending fatigue tests for a structural steel were performed in laboratory air, fresh water and 3.5% NaCl aqueous solution, respectively, thus to investigate the influence of environmental media on the fatigue propensity of the steel, especially in high cycle and very-high-cycle fatigue regimes. The results show that the fatigue strength of the steel in water is remarkably degraded compared with the case tested in air, and that the fatigue strength in 3.5% NaCl solution is even lower than that tested in water. The fracture surfaces were examined to reveal fatigue crack initiation and propagation characteristics in air and aqueous environments.

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26

Zhao, Rong Guo, Ya Feng Liu, Yong Zhou Jiang, Xi Yan Luo, Qi Bang Li, Yi Yan, Peng Cai, and Yue Chen. "Analysis on High Cycle Fatigue Properties and Fatigue Damage Evolution of TC25 Titanium Alloy." Key Engineering Materials 697 (July 2016): 658–63. http://dx.doi.org/10.4028/www.scientific.net/kem.697.658.

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The high cycle fatigue tests for smooth specimens of TC25 titanium alloy under different stress ratios are carried out on a MTS 809 Material Test Machine at a given maximum stress level of 917MPa at ambient temperature, the high cycle fatigue lifetimes for such alloy are measured, and the effects of stress amplitude and mean stress on high cycle fatigue life are analyzed. The initial resistance is measured at the two ends of smooth specimen of TC25 titanium alloy, every a certain cycles, the fatigue test is interrupted, and the current resistance values at various fatigue cycles are measured. The ratio of resistance change is adopted to characterize the fatigue damage evolution in TC25 titanium alloy, and a modified Chaboche damage model is applied to derive the fatigue damage evolution equation. The results show that the theoretical calculated values agree well with the test data, which indicates that the modified Chaboche damage model can precisely describe the accumulated damage in TC25 titanium alloy at high cycle fatigue under unaxial loading. Finally, the high cycle fatigue lifetimes for TC25 titanium alloy specimens at different strain hardening rates are tested at a given stress ratio of 0.1, the effect of strain hardening on fatigue life is investigated based on a microstructure analysis on TC25 titanium alloy, and an expression between fatigue life and strain hardening rate is derived

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27

Jin, Ling Ling, Cai Yan Deng, Dong Po Wang, and Rui Ying Tian. "Research on Ultra-High Cycle Fatigue Property of 45 Steel." Advanced Materials Research 295-297 (July 2011): 1911–14. http://dx.doi.org/10.4028/www.scientific.net/amr.295-297.1911.

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Fatigue property of 45 steel was studied in this paper with the method of ultrasonic fatigue testing, and SEM was used to analyze microscopic characteristics of the fatigue fracture. Fatigue test results show that: S-N curves descend continuously after 108 cycles, there is no fatigue limit as the traditional fatigue conception describes. Therefore, it is very dangerous to design welded structure working in the ultra-high cycle interval with the fatigue strength corresponding to 5×106 cycles. In the super-long life range, the fatigue property of welded joints is worse than the base metal. SEM analysis shows that: fatigue crack mainly initiates from the defects in the surface or sub-surface.

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28

FURUYA, Yoshiyuki. "Fatigue limit in very high cycle fatigue of high-strength steel." Proceedings of the Materials and Mechanics Conference 2019 (2019): OS0901. http://dx.doi.org/10.1299/jsmemm.2019.os0901.

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29

Luo, Ze Fu, Shi Ming Cui, Yan Zeng Wu, and Qing Yuan Wang. "Super Long Life Fatigue Properties of Rail Steel U71Mn and U75V." Advanced Materials Research 690-693 (May 2013): 1753–56. http://dx.doi.org/10.4028/www.scientific.net/amr.690-693.1753.

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Railway track steel, U71Mn and U75V were fatigued in this study, with the help of ultrasonic fatigue test system, to investigate the high cycle fatigue life behaviors. The results showed that the fatigue damage still occurs when the fatigue life exceeds 107, and the evolution of S-N curve showed a ladder type. This test showed that the traditional view of fatigue design and life prediction method were unable to meet the requirements of machinery and equipment working in gigacycle fatigue range, very high cycle fatigue behavior of fatigue has become a major challenge for researchers. The scanning electron microscope analysis of crack initiation was performed to clarify the mechanism of very high cycle fatigue failure.

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30

Shimamura, Yoshinobu, Reo Kasahara, Hitoshi Ishii, Keiichiro Tohgo, Tomoyuki Fujii, Toru Yagasaki, and Soichiro Sumida. "Fretting Fatigue Behaviour of Alloy Steel in the Very High Cycle Region." MATEC Web of Conferences 300 (2019): 18002. http://dx.doi.org/10.1051/matecconf/201930018002.

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It is well known that fretting fatigue strength is much lower than the fatigue strength of smooth specimens and the fatigue limit disappears. Many studies on fretting fatigue have been reported but most of the studies have not cover fatigue properties in the very high cycle regime more than 107 cycles. In this study, an accelerated fretting fatigue testing method was developed by using an ultrasonic torsional fatigue testing machine with a clamping fretting pad. Fretting fatigue tests of CrMo steel were conducted by using the developed method. Test results showed that fretting fatigue failure occurs in the very high cycle region.

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31

Weibel, Dominic, Frank Balle, and Daniel Backe. "Ultrasonic Fatigue of CFRP - Experimental Principle, Damage Analysis and Very High Cycle Fatigue Properties." Key Engineering Materials 742 (July 2017): 621–28. http://dx.doi.org/10.4028/www.scientific.net/kem.742.621.

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Structural aircraft components are often subjected to more than 108 loading cycles during their service life. Therefore the increasing use of carbon fiber reinforced polymers (CFRP) as primary lightweight structural materials leads to the demand of a precise knowledge of the fatigue behavior and the corresponding failure mechanisms in the very high cycle fatigue (VHCF) range. To realise fatigue investigations for more than 108 loading cycles in an economic reasonable time a novel ultrasonic fatigue testing facility (UTF) for cyclic three-point bending was developed and patented. To avoid critical internal heating due to viscoelastic damping and internal friction, the fatigue testing at 20 kHz is performed in resonance as well as in pulse-pause control resulting in an effective testing frequency of ~1 kHz and the capability of performing 109 loading cycles in less than twelve days. The fatigue behavior of carbon fiber twill 2/2 fabric reinforced polyphenylene sulfide (CF-PPS) and carbon fiber 4-H satin fabric reinforced epoxy resin (CF-EP) was investigated. To study the induced fatigue damage of CF-PPS and CF-EP in the VHCF regime in detail, the fatigue mechanisms and damage development were characterized by light optical and SEM investigations during interruptions of constant amplitude tests (CAT). Lifetime-oriented investigations showed a significant decrease of the bearable stress amplitudes of CF-PPS and CFEP in the range between 106 to 109 loading cycles. The ultrasonically fatigued thermoset matrix composite showed a significantly different VHCF behavior in comparison to the investigated thermoplastic matrix composite: No fiber-matrix debonding or transversal cracks were present on the specimen edges, but a sudden specimen failure along with carbon fiber breakage have been observed. The fatigue shear strength at 109 cycles for CF-PPS could be determined to τa, 13 = 4.2 MPa and to τa, 13 = 15.8 MPa for the thermoset material CF-EP.

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32

Yang, You, Hua Wu, and Xue Song Li. "High Cycle Fatigue Behavior of MB8 Magnesium Alloy." Advanced Materials Research 314-316 (August 2011): 945–48. http://dx.doi.org/10.4028/www.scientific.net/amr.314-316.945.

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High cycle fatigue behavior of MB8 magnesium alloy were investigated using an up-and-down load method. High cycle fatigue tests were carried out up to 107cycles at a stress ratio R=0.1 and frequency of 90Hz on specimens using a high frequency fatigue machine. Fatigue fracture surfaces of specimens that in the high cycle fatigue tests were also observed using a scanning electron microscope for revealing the micro-mechanisms of fatigue crack initiation and propagation. The results showed that fatigue limit of MB8 alloy at room temperature is 90.2 MPa under the numbers of cycle to failure Nf=107 conditions using up-and-down method calculation. The fatigue strength of the alloy is about 34% of its tensile strength. The micro-fatigue fracture surface of MB8 alloy included three representative regions. These regions are fatigue initiation area, fatigue crack propagation area and fatigue fracture area. Fatigue cracks of MB8 alloy initiate principally at surface and subsurface, and propagate along the grain boundary. The fatigue striations of fatigue crack propagation area are not clear. The fatigue fracture of test specimens show the rupture characteristics of dimple.

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33

Bao, Xuechun, Li Cheng, Junliang Ding, Xuan Chen, Kaiju Lu, and Wenbin Cui. "The Effect of Microstructure and Axial Tension on Three-Point Bending Fatigue Behavior of TC4 in High Cycle and Very High Cycle Regimes." Materials 13, no. 1 (December 21, 2019): 68. http://dx.doi.org/10.3390/ma13010068.

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The effects of microstructure and axial tension on the fatigue behavior of TC4 titanium alloy in high cycle (HCF) and very high cycle (VHCF) regimes are discussed in this paper. Ultrasonic three-point bending fatigue tests at 20 kHz were done on a fatigue life range among 105–109 cycles of the alloys with equiaxed, bimodal and Widmanstatten microstructures. Experimental results without axial tension show that three typical shapes of S-N curves clearly present themselves for the three different microstructures. Moreover, the crack initiation sites abruptly shifted from surface to subsurface of the specimen in the very high cycle fatigue regime for equiaxed and bimodal microstructures. But for the Widmanstatten microstructure, both surface and subsurface crack initiation appeared in the high cycle fatigue regime, and the multi-points crack initiation was found in the bimodal microstructure. The subsurface fatigue crack originated from the αp grains in equiaxed and bimodal microstructures. However, it originated from the coarse grain boundary α in the Widmanstatten microstructure. Additionally, the S-N curve shape, fatigue life and fatigue crack initiation mechanism with axial tension are similar to that without axial tension. However, the crack origin point shifts inward with axial tension.

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34

Pyttel, B., D. Schwerdt, and C. Berger. "Very high cycle fatigue – Is there a fatigue limit?" International Journal of Fatigue 33, no. 1 (January 2011): 49–58. http://dx.doi.org/10.1016/j.ijfatigue.2010.05.009.

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35

Bhuiyan, Shahnewaz, Youshiharu Mutoh, Yuichi Ostuka, Yukio Miyashita, and Toshikatsu Koike. "309 High cycle fatigue properties of notched die cast AM60 magnesium alloy." Proceedings of the Materials and processing conference 2009.17 (2009): _309–1_—_309–2_. http://dx.doi.org/10.1299/jsmemp.2009.17._309-1_.

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36

Ebara, Ryuichiro. "Grain Size Effect on Low Cycle Fatigue Behavior of High Strength Structural Materials." Solid State Phenomena 258 (December 2016): 269–72. http://dx.doi.org/10.4028/www.scientific.net/ssp.258.269.

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This paper presents grain size effect on low cycle fatigue behavior of high strength maraging steel with gain size of 20,60 and 100μm and Ti-6Al-4V alloy with grain size of 0.5,1.4 and 5.1μm. Low cycle fatigue strength of the maraging steel depends on grain size in number of cycles up to 103.The smaller the grain size, the higher the low cycle fatigue strength was. Quasci-cleavage fracture surfaces were predominant for material with grain size of 20μm,while intergranular fracture surfaces were predominant for materials with larger grain size in number of cycles lower than 60. Striation was predominant for all tested materials in number of cycles higher than 60.Low cycle fatigue strength of Ti-6Al-4V alloy also depends on grain size in number of cycles up to 104. Grain size dependent transgranular fracture surfaces were predominant for materials with ultra-fine grain size of 0.5μm and fine grain size of 1.4μm.

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Horst, P., T. J. Adam, M. Lewandrowski, B. Begemann, and F. Nolte. "Very High Cycle Fatigue - Testing Methods." IOP Conference Series: Materials Science and Engineering 388 (July 19, 2018): 012004. http://dx.doi.org/10.1088/1757-899x/388/1/012004.

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Charkaluk, Eric, and Andrei Constantinescu. "Dissipative aspects in high cycle fatigue." Mechanics of Materials 41, no. 5 (May 2009): 483–94. http://dx.doi.org/10.1016/j.mechmat.2009.01.018.

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39

NICHOLAS, T. "Critical issues in high cycle fatigue." International Journal of Fatigue 21 (September 1999): 221–31. http://dx.doi.org/10.1016/s0142-1123(99)00074-2.

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Mazumdar, P. K. "A model for high cycle fatigue." Engineering Fracture Mechanics 41, no. 6 (April 1992): 907–17. http://dx.doi.org/10.1016/0013-7944(92)90239-b.

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Michler, J. R., and S. R. Bhonsle. "HIGH-CYCLE SPRING FATIGUE TEST MACHINE." Experimental Techniques 17, no. 2 (March 1993): 17–19. http://dx.doi.org/10.1111/j.1747-1567.1993.tb00733.x.

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42

Stanzl-Tschegg, Stefanie. "Very high cycle fatigue measuring techniques." International Journal of Fatigue 60 (March 2014): 2–17. http://dx.doi.org/10.1016/j.ijfatigue.2012.11.016.

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Hagiwara, Masuo, Tomonori Kitashima, Satoshi Emura, Satoshi Iwasaki, and Mitsuharu Shiwa. "Very High-Cycle Fatigue and High-Cycle Fatigue of Minor Boron-Modified Ti–6Al–4V Alloy." MATERIALS TRANSACTIONS 60, no. 10 (October 1, 2019): 2213–22. http://dx.doi.org/10.2320/matertrans.mt-m2019169.

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44

FARFAN, S. "High cycle fatigue, low cycle fatigue and failure modes of a carburized steel." International Journal of Fatigue 26, no. 6 (June 2004): 673–78. http://dx.doi.org/10.1016/j.ijfatigue.2003.08.022.

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45

Altenberger, I., Ivan Nikitin, P. Juijerm, and Berthold Scholtes. "Residual Stress Stability in High Temperature Fatigued Mechanically Surface Treated Metallic Materials." Materials Science Forum 524-525 (September 2006): 57–62. http://dx.doi.org/10.4028/www.scientific.net/msf.524-525.57.

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Different classes of metallic materials (aluminum alloys, steels, titanium alloys) were mechanically surface treated by deep rolling and laser shock peening and isothermally fatigued at elevated temperature under stress control. The fatigue tests were interrupted after different numbers of cycles for several stress amplitudes and residual stresses and FWHM-values were measured by X-ray diffraction methods at the surface and as a function of depth. The results summarize the response of the surface treatment induced residual stress profiles to thermomechanical loading conditions in the High Cycle Fatigue (HCF)- as well as in the Low Cycle Fatigue (LCF) regime. The effects of stress amplitude, plastic strain amplitude, temperature and frequency are addressed in detail and discussed. The results indicate that residual stress relaxation during high temperature fatigue can be predicted for sufficiently simplified loading conditions and that thermal and mechanical effects can be separated from each other. A plastic strain based approach appears to be most suitable to describe residual stress relaxation. Frequency effects were found to be not very pronounced in the frequency range investigated.

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Gui, Long Ming, Xiao Chun Jin, Hong Tao Li, and Mei Zhang. "High Cycle Fatigue Performances of Advanced High Strength Steel CP800." Advanced Materials Research 989-994 (July 2014): 238–41. http://dx.doi.org/10.4028/www.scientific.net/amr.989-994.238.

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A low carbon content and improved steel making practices have imparted advanced high strength steel (AHSS) CP800 with superior combination of strength, ductility and weldability. Its performance in fatigue, however, is not well understood. Stress-controlled high cycle fatigue (HCF) tests were conducted to obtain stress vs. fatigue life curve (S-N curve), and the fatigue limit of CP800. The follow HCF performances were obtained. , SRI1=1940MPa, b=-0.09972, Nc1=2.89×106, and R2= 0.88. The collected material data are used as a basis of comparison of CP800 with more common grades of structural steel. CP800 steel shows high strength, comparable ductility, and high fatigue limit level. The test results indicate that compare to that of lower strength common grades of structural steels, CP800 steel has a much higher fatigue endurance limit (say, 476MPa), about 0.6 of its tensile strength (TS). Thus, provides a distinct advantage.

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47

Nagy, Gyula, and János Lukács. "Connection among the Characteristics of the Low Cycle Fatigue, High Cycle Fatigue and Fatigue Crack Growth." Key Engineering Materials 345-346 (August 2007): 533–36. http://dx.doi.org/10.4028/www.scientific.net/kem.345-346.533.

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The material quality, the deformation rate, the temperature and the stress state influence mechanical behaviour and properties of different materials. Due to this great variety of the influencing factors we do not have one model of general validity describing the behaviour of materials, but we have to use a great number of material constants in order to characterize the properties. The exponents of the Manson-Coffin, the Basquin and the Paris-Erdogan laws were applied for the verification of the connection among the fatigue fracture types. Own measured values and test results can be found in the literature were used for the illustration of the connections. “Fracture surface”-s were determined for characterizing of different steel grades and their welded joints. It can be concluded that “fracture surface”-s are suitable for the describing of the fracture behaviour and the conversion of different fracture parameters of steels.

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Yan, Ming, Hao Chuan Li, and Lin Li. "Stress Intensity Factor of Thermal Fatigue Crack in High Temperature." Advanced Materials Research 581-582 (October 2012): 677–80. http://dx.doi.org/10.4028/www.scientific.net/amr.581-582.677.

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Stress intensity factor of thermal fatigue crack was calculated within one cycle by using finite element method in consideration of the multi-linear kinematic hardening characteristic of a material. The affection of loading sequence to stress intensity factor was studied under circularly variational temperature by comparing to that in one cycle. The low temperature cycle can not affect the stress intensity factor of latter cycles with high temperature; but high temperature cycle can affect the stress intensity factor of latter cycles with low temperature, and make it be equal to that of the high temperature cycle.

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Zhao, Xiao, and Jian Jun Zhao. "Experimental Study on Ultra-High Cycle Fatigue Property of Q345 Welded Joint." Advanced Materials Research 538-541 (June 2012): 1488–91. http://dx.doi.org/10.4028/www.scientific.net/amr.538-541.1488.

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The present paper deals with experimental studies on the ultra-high cycle fatigue property of Q345 bridge steel. Using the ultrasonic fatigue testing technique, specimens of Q345 welded joint with hourglass shape were designed using an analytical method combining with the finite element method and then fatigue tested in air at room temperature under fully reversed cyclic loading conditions (R=-1). The results show that the S-N curves of welded joints and relative base material specimens show continuously decreasing tendency in the very high cycle regime (105-109 cycles). Fatigue property of welded joint is much lower than that of base material and the fatigue strength of welded joint is only 45.0% of base material. Fracture can still occur on welded joints beyond 5 106 cycles, which indicates the fatigue limit defined at lifetime of 5 106 cycles cannot guarantee a safe design.

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50

Song, Qingpeng, Jiwang Zhang, Ning Zhang, Wei Li, and Liantao Lu. "High cycle fatigue property and fracture behavior of high-strength austempered ductile iron." Proceedings of the Institution of Mechanical Engineers, Part L: Journal of Materials: Design and Applications 231, no. 4 (August 11, 2015): 423–29. http://dx.doi.org/10.1177/1464420715599800.

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The high cycle fatigue tests of high-strength austempered ductile iron of grade 1200/850/04 (ASTM 897 M-06) were conducted by the high frequency fatigue machine. The results show that the S–N curve decreases continuously and there is no conventional fatigue limit at 107 cycles. According to the fracture surface observations, at short fatigue life region the specimens fail from defects at specimen surface and at long fatigue life region the specimens fail from internal defects with fish-eye area around it. According to the defect sizes measured in the standard inspection areas of the material, the maximum defect size evaluated by the statistics of extreme values method is in accordance with that of the fatigue test results. Meanwhile, it is obvious that the fatigue strength of austempered ductile iron is influenced by the original defect size and the fatigue limit can be well evaluated by the Murakami equation.

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