An Atom-Probe Tomographic Study of Arc Welds in a Multi-Component High-Strength Low-Alloy Steel

Hunter, Allen H.; Farren, Jeffrey D.; DuPont, J. N.; Seidman, David N.

doi:10.1007/s11661-012-1518-5

Cited by 17 publications

(4 citation statements)

References 43 publications

Supporting

Mentioning

Contrasting

Order By: Relevance

“…Revealing the microstructure-property relations that are characteristic of the different types of AHSS requires the use of advanced microstructure characterization tools, applied over a wide range of length scales [12][13][14][15][16][17][18][19][20][21][22][23][24] and with high chemical sensitivity. [25][26][27][28][29][30] Therefore, some of the latest progress in the field of the characterization of AHSS will be highlighted as well.…”

Section: Introductionmentioning

confidence: 99%

Current Challenges and Opportunities in Microstructure-Related Properties of Advanced High-Strength Steels

Raabe

Sun

Silva

et al. 2020

Metall Mater Trans A

141

View full text Add to dashboard Cite

This is a viewpoint paper on recent progress in the understanding of the microstructure–property relations of advanced high-strength steels (AHSS). These alloys constitute a class of high-strength, formable steels that are designed mainly as sheet products for the transportation sector. AHSS have often very complex and hierarchical microstructures consisting of ferrite, austenite, bainite, or martensite matrix or of duplex or even multiphase mixtures of these constituents, sometimes enriched with precipitates. This complexity makes it challenging to establish reliable and mechanism-based microstructure–property relationships. A number of excellent studies already exist about the different types of AHSS (such as dual-phase steels, complex phase steels, transformation-induced plasticity steels, twinning-induced plasticity steels, bainitic steels, quenching and partitioning steels, press hardening steels, etc.) and several overviews appeared in which their engineering features related to mechanical properties and forming were discussed. This article reviews recent progress in the understanding of microstructures and alloy design in this field, placing particular attention on the deformation and strain hardening mechanisms of Mn-containing steels that utilize complex dislocation substructures, nanoscale precipitation patterns, deformation-driven transformation, and twinning effects. Recent developments on microalloyed nanoprecipitation hardened and press hardening steels are also reviewed. Besides providing a critical discussion of their microstructures and properties, vital features such as their resistance to hydrogen embrittlement and damage formation are also evaluated. We also present latest progress in advanced characterization and modeling techniques applied to AHSS. Finally, emerging topics such as machine learning, through-process simulation, and additive manufacturing of AHSS are discussed. The aim of this viewpoint is to identify similarities in the deformation and damage mechanisms among these various types of advanced steels and to use these observations for their further development and maturation.

show abstract

Section: Introductionmentioning

confidence: 99%

Current Challenges and Opportunities in Microstructure-Related Properties of Advanced High-Strength Steels

Raabe

Sun

Silva

et al. 2020

Metall Mater Trans A

141

View full text Add to dashboard Cite

show abstract

“…In particular, the precipitation of coherent nanoparticles, such as body-centered cubic (bcc) Cu-rich nanoclusters [2][3][4][5][9][10][11][12] and B2-ordered NiAl intermetallic nanoparticles [13][14][15][16][17], is very appealing, because they can precipitate on a sufficiently fine scale (less than 5 nm in diameter), providing an extremely high strengthening response. Currently, research is starting to emerge on the weldability of this class of high-strength steels, mostly of Cu-rich nanoclusters strengthened steels [18][19][20][21][22][23]. Previous welding studies showed that the hardness of heat-affected zone (HAZ) and fusion zone (FZ) of Cu-strengthened steels was undermatched to the base metal (BM), which was considered to be due to the partial dissolution of preexisting Cu-rich nanoclusters within the HAZ and full dissolution of nanoclusters within the FZ, as characterized by atom probe tomography (APT) [18][19][20][21].…”

Section: Introductionmentioning

confidence: 99%

“…Currently, research is starting to emerge on the weldability of this class of high-strength steels, mostly of Cu-rich nanoclusters strengthened steels [18][19][20][21][22][23]. Previous welding studies showed that the hardness of heat-affected zone (HAZ) and fusion zone (FZ) of Cu-strengthened steels was undermatched to the base metal (BM), which was considered to be due to the partial dissolution of preexisting Cu-rich nanoclusters within the HAZ and full dissolution of nanoclusters within the FZ, as characterized by atom probe tomography (APT) [18][19][20][21]. It has been found that the reprecipitation of nanoparticles can be achieved by designing an appropriate post-weld heat treatment (PWHT) or multi-pass welding procedure, which provides a promising way to recover the mechanical properties of welds [22,23].…”

Section: Introductionmentioning

confidence: 99%

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

View full text Add to dashboard Cite

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

show abstract

“…Copper precipitation has been investigated in model binary and ternary Fe-Cu alloys (Hornbogen & Glenn, 1960;Speich & Oriani, 1965;Goodman et al, 1973aGoodman et al, , 1973bPizzini et al, 1990;Othen et al, 1991Othen et al, , 1994Phythian et al, 1992;Maury et al, 1994;Osamura et al, 1994aOsamura et al, , 1994bCharleux et al, 1996;Monzen et al, 2000Monzen et al, , 2003Monzen et al, , 2004Deschamps et al, 2001Deschamps et al, , 2003, in ASTM A710 and A736 grade Fe-Cu steels (Miglin et al, 1986;Wilson et al, 1988;Thompson & Krauss, 1996;Dhua et al, 2001aDhua et al, , 2001b, and more recently in the NUCu and other experimental Fe-Cu steels (Gagliano & Fine, 2001Isheim et al, 2006b;Vaynman et al, 2008;Mulholland & Seidman, 2009;Mulholland & Seidman, 2011;Farren et al, 2012;Hunter et al, 2013). These studies focused on Cu-rich precipitates located in the matrix phase that were formed during solutionizing and quenching (interphase precipitation) or during isothermal aging.…”

Section: Introductionmentioning

confidence: 99%

Co-Precipitated and Collocated Carbides and Cu-Rich Precipitates in a Fe–Cu Steel Characterized by Atom-Probe Tomography

Kolli

Seidman

2014

Microsc Microanal

Self Cite

View full text Add to dashboard Cite

The composition of co-precipitated and collocated NbC carbide precipitates, Fe3C iron carbide (cementite), and Cu-rich precipitates are studied experimentally by atom-probe tomography (APT). The Cu-rich precipitates located at a grain boundary (GB) are also studied. The APT results for the carbides are supplemented with computational thermodynamics predictions of composition at thermodynamic equilibrium. Two types of NbC carbide precipitates are distinguished based on their stoichiometric ratio and size. The Cu-rich precipitates at the periphery of the iron carbide and at the GB are larger than those distributed in the α-Fe (body-centered cubic) matrix, which is attributed to short-circuit diffusion of Cu along the GB. Manganese segregation is not observed at the heterophase interfaces of the Cu-rich precipitates that are located at the periphery of the iron carbide or at the GB, which is unlike those located at the edge of the NbC carbide precipitates or distributed in the α-Fe matrix. This suggests the presence of two populations of NiAl-type (B2 structure) phases at the heterophase interfaces in multicomponent Fe-Cu steels.

show abstract

An Atom-Probe Tomographic Study of Arc Welds in a Multi-Component High-Strength Low-Alloy Steel

Cited by 17 publications

References 43 publications

Current Challenges and Opportunities in Microstructure-Related Properties of Advanced High-Strength Steels

Current Challenges and Opportunities in Microstructure-Related Properties of Advanced High-Strength Steels

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

Co-Precipitated and Collocated Carbides and Cu-Rich Precipitates in a Fe–Cu Steel Characterized by Atom-Probe Tomography

Contact Info

Product

Resources

About