Creep and rupture in Type 316 stainless steel at temperatures between 525 and 900°C Part I: Creep rate

Morris, David G.; Harries, D.R.

doi:10.1179/msc.1978.12.11.525

Cited by 50 publications

(27 citation statements)

References 15 publications

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“…15 During creep in austenitic stainless steels, precipitation takes place and intermediate values of n were reported between those of solid solution alloys and precipitation hardened materials. 16–18 Furthermore, creep data on AISI 347 stainless steel foil examined in this study was mapped onto transient creep mechanism maps for austenitic stainless steels. 19 Result indicates that power-law creep mechanism dominates during the initial deformation stage.…”

Section: Resultsmentioning

confidence: 99%

Creep ruptures of AISI 347 austenitic stainless steel foils at elevated temperature of 750 ℃

Osman

Nor

Hamdan

et al. 2015

Proceedings of the Institution of Mechanical Engineers, Part L:

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The creep rupture properties of AISI 347 austenitic stainless steel foil used in compact recuperators have been evaluated at 750 C in the stress range of 54-221 MPa to establish baseline behavior for its extended use. The creep curve of the foil shows that the primary creep stage is brief and creep life is dominated by tertiary creep deformation with rupture lives in the range 3-433 h. Power law relationship was obtained between the minimum creep rate and the applied stress with stress exponent value of n ¼ 4.25. The creep damage tolerance parameter for specimen tested at 750 C and 54 MPa indicates that creep fracture takes place by precipitate coarsening mechanism. Nucleation of voids mainly occurs at second-phase particles (Cr 23 C 6 carbides). The improvement in strength is attributed to the precipitation of fine niobium carbides in the matrix which prevents dislocation movement of the microstructure.

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Section: Resultsmentioning

confidence: 99%

Creep ruptures of AISI 347 austenitic stainless steel foils at elevated temperature of 750 ℃

Osman

Nor

Hamdan

et al. 2015

Proceedings of the Institution of Mechanical Engineers, Part L:

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“…Creep data of Type 316H stainless steel obtained by Morris and Harries 45 showed various creep stress exponents, up to n=22.3 for the test temperature of 525°C in Figure 2 (b). The presence of a three dimensional dislocation network was observed in the temperature range from 525°C to 625°C 45,65 .…”

Section: Creep Of a Complex Engineering Alloymentioning

confidence: 92%

“…The presence of a three dimensional dislocation network was observed in the temperature range from 525°C to 625°C 45,65 . Stress exponents from about n=7…”

Section: Creep Of a Complex Engineering Alloymentioning

confidence: 99%

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A review of the changes of internal state related to high temperature creep of polycrystalline metals and alloys

Chen

Flewitt

Cocks

et al. 2014

International Materials Reviews

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When polycrystalline metals and their alloys are used at high temperature, creep deformation leads to changes in their internal state. The change in internal state manifests itself in many ways, but the two ways that concern us in this review are (i) the creation of internal stress arising from the strain incompatibility between grains and/or the formation of cell/sub-grain structures and (ii) a change in the material resistance. This review aims to provide a clear separation of these two concepts by exploring the origin of each term and how it is associated with the creep deformation mechanism. Experimental techniques used to measure the internal stress and internal resistance over different length-scales are critically reviewed. It is demonstrated that the interpretation of the measured values requires knowledge of the dominant creep deformation mechanism. Finally, the concluding comments provide a summary of the key messages delivered in this review and highlight the challenges that remain to be addressed.

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“…was determined by DiMelfi [6] from analysing the data obtained from creep experiments on Type 316 stainless steel undertaken by Morris and Harries [17]. Eqn (9) was applied to predict the stress relaxation response of ex-service 316H austenitic stainless steel.…”

Section: Earlier Stress Relaxation Modelsmentioning

confidence: 99%

Constitutive equations that describe creep stress relaxation for 316H stainless steel at 550°C

Chen¹,

Smith²,

Flewitt

et al. 2011

Materials at High Temperatures

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The prediction of the stress relaxation behaviour of welding induced residual stresses in thick section 316H austenitic stainless steel welded component provides an input for quantifying reheat crack initiation observed in the heat affected zone. The cracks occur after service at a temperature range from 490 to 520 C. The present work reviews some of the widely applied stress relaxation models. The relative strengths and weaknesses of these existing models are discussed. An improved constitutive equation derived from a forward uniaxial creep deformation law is proposed. The relative importance of the parameters selected in the new constitutive model, when compared with experimental data, is discussed. The importance of a better understanding of the role of the internal stress and its measurement is highlighted.Units for all of these symbols are given in the text. All strains and stresses considered in this paper are engineering strains and engineering stresses, rather than the true strains and true stresses.

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Creep and rupture in Type 316 stainless steel at temperatures between 525 and 900°C Part I: Creep rate

Cited by 50 publications

References 15 publications

Creep ruptures of AISI 347 austenitic stainless steel foils at elevated temperature of 750 ℃

Creep ruptures of AISI 347 austenitic stainless steel foils at elevated temperature of 750 ℃

A review of the changes of internal state related to high temperature creep of polycrystalline metals and alloys

Constitutive equations that describe creep stress relaxation for 316H stainless steel at 550°C

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