Temper embrittlement

Olefjord, I.

doi:10.1179/imtr.1978.23.1.149

Cited by 13 publications

(6 citation statements)

References 58 publications

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“…The combined phenomena lead to intergranular cracking. Temper embrittlement can increase the ductile-brittle transition temperature [15] [16],, which did not occur in the present case (see section 4).…”

Section: Accepted Manuscriptcontrasting

confidence: 58%

Experimental assessment of thermal grain boundary embrittlement after tubeplate failure in a petrochemical heat exchanger

Otegui

Booman

Massone

2017

Engineering Failure Analysis

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Section: Accepted Manuscriptcontrasting

confidence: 58%

Experimental assessment of thermal grain boundary embrittlement after tubeplate failure in a petrochemical heat exchanger

Otegui

Booman

Massone

2017

Engineering Failure Analysis

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“…The 550 °C PWHT results in a complete loss of ductility, whereas the 600 °C PWHT leads to a most recovery of ductility, achieving a reduction in area of ~35% and an elongation-to-failure of ~6%. It appears that the weld ductility has a strong dependence on the PWHT temperature, similar as the temper embrittlement phenomenon of quenched-and-tempered steels [42][43][44][45][46]. In general, the mechanism for temper embrittlement and de-embrittlement of steels can be related to the following factors: (1) grain size, (2) precipitate microstructure, (3) grain-boundary segregation, and (4) reversion of austenite [5,[42][43][44][45][46].…”

Section: Effects Of Welding and Pwht On The Ductilitymentioning

confidence: 91%

Effects of welding and post-weld heat treatments on nanoscale precipitation and mechanical properties of an ultra-high strength steel hardened by NiAl and Cu nanoparticles

et al. 2016

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The effects of welding and post-weld heat treatment (PWHT) on nanoscale coprecipitation, grain structure, and mechanical properties of an ultra-high strength steel were studied through a combination of atom probe tomography (APT) and mechanical tests. Our results indicate that the welding process dissolves all pre-existing nanoparticles and causes grain coarsening in the fusion zone, resulting in a soft and ductile weld without any cracks in the aswelded condition. A 550 °C PWHT induces fine-scale re-precipitation of NiAl and Cu coprecipitates with high number densities and ultra-fine sizes, leading to a large recovery of strength but a loss of ductility with intergranular failure, whereas a 600 °C PWHT gives rise to coarse-scale re-precipitation of nanoparticles together with the formation of a small amount of reverted austenite, resulting in greater recovery in both strength and ductility. Our analysis indicates that the degree of strength recovery is dependent mainly upon the re-precipitation

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“…1 In addition, tungsten and molybdenum (to a lesser extent) is added because it lowers the grain boundary embrittlement potential when in solution because it ties up tramp elements. 7,8 Eglin steel typically has a quenched and tempered microstructure consisting of tempered martensite with a variety of carbide sizes and morphologies. Paules et al 9 have reported M 3 C, M 6 C and MC carbides that form after heat treatment with sizes of 180, 250 and 10-20 nm respectively.…”

Section: Introductionmentioning

confidence: 99%

Development of a continuous cooling transformation diagram for Eglin steel

Leister

DuPont

2015

Materials Science and Technology

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Eglin steel is a new ultrahigh strength steel that has been developed at Eglin Air Force Base in the early 2000 s. This steel could be subjected to a variety of processing steps during fabrication, each with its own thermal history. This article presents a continuous cooling transformation diagram developed for Eglin steel to be used as a guideline during processing. Dilatometry techniques performed on a Gleeble thermomechanical simulator were combined with microhardness results and microstructural characterisation to develop the diagram. The results show that four distinct microstructures form within Eglin steel depending on the cooling rate. At cooling rates above ,1uC s 21 , a predominately martensitic microstructure is formed with hardness of y520 HV. Intermediate cooling rates of 1 to 0?2uC s 21 produce a mixed martensitic/ bainitic microstructure with a hardness that ranges from 520 to 420 HV. Slower cooling rates of 0?1 to 0?03uC s 21 lead to the formation of a bainitic microstructure with a hardness of y420 HV. The slowest cooling rate of 0?01uC s 21 formed a bainitic microstructure with an apparent carbide constituent at the prior austenite grain boundaries.

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Temper embrittlement

Cited by 13 publications

References 58 publications

Experimental assessment of thermal grain boundary embrittlement after tubeplate failure in a petrochemical heat exchanger

Experimental assessment of thermal grain boundary embrittlement after tubeplate failure in a petrochemical heat exchanger

Effects of welding and post-weld heat treatments on nanoscale precipitation and mechanical properties of an ultra-high strength steel hardened by NiAl and Cu nanoparticles

Development of a continuous cooling transformation diagram for Eglin steel

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