strengthening and fracture in fatigue (approaches for achieving high fatigue strength)

Grosskreutz, J. C.

doi:10.1007/bf02642460

Cited by 93 publications

(14 citation statements)

References 10 publications

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“…Contrary, a high SFE will help splitting of partial dislocations and allows for climbing and cross slip [12] and thereby facilitate cell formation. The SFE strongly depends on the chemical composition of the material and is generally increased by the addition of nickel [13].…”

Section: Introductionmentioning

confidence: 93%

The effects of subsurface deformation on the sliding wear behaviour of a microtextured high-nitrogen steel surface

Büscher

Gleising

Dudziński

et al. 2004

Wear

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Section: Introductionmentioning

confidence: 93%

The effects of subsurface deformation on the sliding wear behaviour of a microtextured high-nitrogen steel surface

Büscher

Gleising

Dudziński

et al. 2004

Wear

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“…[32,33] The deformation in the alloy with higher B concentration, however, would be more dispersed, which would eliminate the deleterious effect of inhomogeneous distribution of plastic deformation by preventing an early nucleation of cracks due to the presence of intense slip bands, thus improving the fatigue resistance of the alloy. [33,34,35] Since slip concentration was observed only in the alloy containing 12 ppm B, its LCF fatigue life was the lowest, and improved as the B concentration increased.…”

Section: Effect Of B On Cyclic Deformation Mechanism and Fatigue Lmentioning

confidence: 99%

Low-cycle fatigue behavior of INCONEL 718 superalloy with different concentrations of boron at room temperature

Lin

Chaturvedi

Chen

2005

Metall Mater Trans A

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Symmetrical push-pull low-cycle fatigue (LCF) tests were performed on INCONEL 718 superalloy containing 12, 29, 60, and 100 ppm boron (B) at room temperature (RT). The results showed that all four of these alloys experienced a relatively short period of initial cyclic hardening, followed by a regime of softening to fracture at higher cyclic strain amplitudes (⌬ t /2 Ն 0.8 pct). As the cyclic strain amplitude decreased to ⌬ t /2 Յ 0.6 pct, a continuous cyclic softening occurred without the initial cyclic hardening, and a nearly stable cyclic stress amplitude was observed at ⌬ t /2 ϭ 0.4 pct. At the same total cyclic strain amplitude, the cyclic saturation stress amplitude among the four alloys was highest in the alloy with 60 ppm B and lowest in the alloy with 29 ppm B. The fatigue lifetime of the alloy at RT was found to be enhanced by an increase in B concentration from 12 to 29 ppm. However, the improvement in fatigue lifetime was moderate when the B concentration exceeded 29 ppm B. A linear relationship between the fatigue life and cyclic total strain amplitude was observed, while a "two-slope" relationship between the fatigue life and cyclic plastic strain amplitude was observed with an inflection point at about ⌬ p /2 ϭ 0.40 pct. The fractographic analyses suggested that fatigue cracks initiated from specimen surfaces, and transgranular fracture, with well-developed fatigue striations, was the predominant fracture mode. The number of secondary cracks was higher in the alloys with 12 and 100 ppm B than in the alloys with 29 and 60 ppm B. Transmission electron microscopy (TEM) examination revealed that typical deformation microstructures consisted of a regularly spaced array of planar deformation bands on {111} slip planes in all four alloys. Plastic deformation was observed to be concentrated in localized regions in the fatigued alloy with 12 ppm B. In all of the alloys, ␥Љ precipitate particles were observed to be sheared, and continued cyclic deformation reduced their size. The observed cyclic deformation softening was associated with the reduction in the size of ␥ Љ precipitate particles. The effect of B concentration on the cyclic deformation mechanism and fatigue lifetime of IN 718 was discussed.

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“…The fatigue strength was found to be directly proportional to the difficulty of the cross slip of dislocations, that in turn was explained by the low values of stacking fault energy (Grosskreutz 1972). 1, the strain behaviour of austenitic steels is characterised by planar slip.…”

Section: Austenitic Steelsmentioning

confidence: 99%

High Nitrogen Steels

Gavriljuk¹,

Berns²

1999

Engineering Materials

385

110

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The use of general descriptive names, registered names, trademarks, ete. in this publication does not imply, even in the absence of a specific statement, that such names are exempt from the relevant protective laws and regulations and therefore free for general use.Typesetting: Camera-ready eopies from authors Cover-Design: MEDIO, Berlin Printed on acid-free paper SPIN 10730039 6213020 5 4 3 2 1 0 to BELA and ISOLDE PrefaceDuring the second half of this century the nitrogen concentration of steel moved in both directions: down in constructional grades by oxygen blowing to prevent brittle fracture upon age hardening at ambient temperature and up in stainless grades to improve strength, corrosion resistance and austenite stability. The gradual recognition of the beneficial effects of this element on the properties of high alloy steels led to a widespread development of high nitrogen steels (HNS) documented by numerous applications and the proceedings of five HNS conferences at LilIe (France) 1988, Aachen (Germany) 1990, Kiev (Ukraine) 1993, Kyoto (Japan) 1996 and HelsinkilStockholm (FinnlandISweden) 1998. The word "high" in HNS is not clearly defined but accounts e.g. for 0.1 mass% of nitrogen in creep resistant steels, 0.9 mass% in stainless grades or 2 mass% in tool steels. "High" best refers to "intentionally raised" by appropriate alloying or by pressure and powder metallurgy. For convenience steel grades are designated by their approximate content of alloying elements in mass% omitting unintentional minor additons of Si, Mn, C, P, S asf. As an example Cr22Ni5M03NO.2 stands for a stainless duplex grade.The present book starts by comparing the effects of nitrogen and carbon on the atomic structure and interaction within the crystallattice. Next the constitution of HNS is investigated leading to specific microstructural features. Based on this background the mechanisms behind the mechanical, chemical and tribological properties of HNS are derived. This concludes the fundamentals treated in chapters one to three. Chapter four comes down to shop practice of manufacturing HNS which, in respect to e.g. melting, hot working, and welding, may be quite different from respective carbon grades. In chapter five, different HNS for special applications are presented like e.g. hardenable steels for stainless bearings, high strength austenitic steels for non-magnetic retaining rings, superaustenitic stainless sheet for the chemical industry or solution nitrided impellers for pumps. Chapter six is an attempt to summarize key aspects of HNS.The book is meant for material scientist working in the field of high alloy steels and also for engineers engaged in materials technology, material selection and design. The work covers a wide scope from the atomic structure to the application of HNS and was written by a metal physicist and an engineer.

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strengthening and fracture in fatigue (approaches for achieving high fatigue strength)

Cited by 93 publications

References 10 publications

The effects of subsurface deformation on the sliding wear behaviour of a microtextured high-nitrogen steel surface

The effects of subsurface deformation on the sliding wear behaviour of a microtextured high-nitrogen steel surface

Low-cycle fatigue behavior of INCONEL 718 superalloy with different concentrations of boron at room temperature

High Nitrogen Steels

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