Research Papers

Mechanical Properties and Structure of Laser Beam and Wide Gap Brazed Joints Produced Using Mar M247–Amdry DF3 Powders

[+] Author and Article Information
Alexandre Gontcharov

Liburdi Turbine Services, Inc.,
400 Hwy 6 North,
Dundas, ON L9H 7K4, Canada
e-mail: agontcharov@liburdi.com

Yuan Tian

Liburdi Turbine Services, Inc.,
400 Hwy 6 North,
Dundas, ON L9H 7K4, Canada
e-mail: tianyuan19880212@gmail.com

Paul Lowden

Liburdi Turbine Services, Inc.,
400 Hwy 6 North,
Dundas, ON L9H 7K4, Canada
e-mail: plowden@liburdi.com

Mathieu Brochu

McGill University,
Wong Building, 3610 University, Room 2140,
Montreal, QC H3A 0C5, Canada
e-mail: mathieu.brochu@mcgill.ca

Manuscript received June 26, 2018; final manuscript received July 10, 2018; published online December 7, 2018. Editor: Jerzy T. Sawicki.

J. Eng. Gas Turbines Power 141(4), 041031 (Dec 07, 2018) (7 pages) Paper No: GTP-18-1367; doi: 10.1115/1.4041009 History: Received June 26, 2018; Revised July 10, 2018

The microstructure and mechanical properties of materials produced by wide gap brazing (WGB) and laser beam (LBW) cladding with different blends of Mar M247 and Amdry DF-3 brazing powders were studied. It was shown that LBW Mar M247-based materials comprised of 0.6 to 1 wt % B were weldable. The weld properties were superior to WGB deposits with the same bulk chemical composition, due to the formation of a dendritic structure typical for welded joints, and the precipitation of cuboidal borides of Cr, Mo, and W in the ductile Ni–Cr based matrix. Both materials were found to have useful properties for three-dimensional (3D) additive manufacturing (AM) and repair components manufactured from high gamma prime precipitation hardened superalloys.

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Fig. 1

Formation of WGB materials depicting: (a) M247 powder in the original condition, (b) formation of scale in the surface of M247 filler powder particles, (c) solid state sintering of M247 at 1200 °C, and (d) WGB material after infiltration and sintering in the liquid state for 2 h

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Fig. 2

The typical sample produced by multipass laser beam cladding in the annealed and aged condition using 100:25 powder blend

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Fig. 3

Typical cracking of LBW welds produced using standard M247 powder: (a) weld metal cracking occurred in the M247 weld and (b) heat-affected zone cracking of the IN738 substrate

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Fig. 4

The micrograph of the defect free LBW weld produced using the powder blend ‘B’ depicting (a) epitaxial grain growth through clad welds and healing of solidification of microcracks in the HAZ of IN738 substrate and (b) formation of the interconnected framework of the high temperature dendrites and eutectic matrix

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Fig. 5

Tensile properties of M247-DF3 materials produced by WGB and LBW: (a) yield strength, (b) ultimate tensile strength, and (c) elongation (AWM refers to “all weld metal” samples; ABM refers to “all braze metal” samples; BJ refers to “braze joint” samples)

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Fig. 6

Typical EDS of the WGB material A in the heat treat condition depicting a formation of bulky Cr–Mo–W borides

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Fig. 7

Energy dispersive spectroscopy of the LBW weld metal ‘B’ depicting precipitation of Cr–Mo–W borides depleted with Ni in “as-welded” condition

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Fig. 8

Microstructure of the LBW weld produced using the powder blend A after postweld annealing at 1200 °C, wherein (a) optical micrograph and (b) SEM micrograph

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Fig. 9

Energy dispersive spectroscopy of the LBW metal produced using the powder blend B after annealing and aging heat treatment depicting dissolution of the continuous interdendritic Ni–B based eutectics and precipitation of Cr–Mo–W borides

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Fig. 10

The typical microstructure of the Mar M247-DF3 material after annealing at 1200 °C for 2 h and 843 °C for 24 h depicting the precipitation of gamma prime phase in the LBW weld metal produced using the powder blend B

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Fig. 11

Restoration of abutment faces of low pressure turbine NGV by welding: (a) vane manufactured of Mar M247 and (b) micrograph of the repaired by welding area



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