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Published: 01 October 2011
Fig. 14.26 Effect of solution-treatment temperatures on microstructures of quenched and aged α alloy Ti-8Al-1Mo-1V. All specimens were solution annealed at indicated temperatures for 1 h, quenched in oil, stabilized at 580 °C (1075 °F) for 8 h and air cooled. (a) Fine α-β structure after β More
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Published: 01 October 2011
Fig. 14.27 Effect of solution treatment on ductility and creep rupture of alloy Ti8Al-1Mo-1V More
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Published: 01 October 2011
Fig. 14.28 Effect of solution treatment on tensile properties of Ti-6Al-4V. (a) Tensile properties after solution treatment. (b) Tensile properties after solution treatment and aging. Source: Ref 14.10 More
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Published: 01 March 2002
Fig. 12.7 Influence of solution heat treatment temperature on rupture life of Nimonic 80A nickel-base superalloy at 234 MPa (34 ksi) and 750 °C (1380 °F), showing effect of 1000 °C (1832 °F) intermediate heat treatment before aging. Open datapoints are SHT for 4 h. Cool to IHT and IHT for 16 h More
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Published: 01 March 2002
Fig. 12.11 Effect of solution heat treatment and aging on X-40 (HA-31) cobalt-base superalloy showing increase in strength resulting from carbide precipitation More
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Published: 01 December 2004
Fig. 7.5 Characteristic residual stress distribution after solution heat treatment and quench. t , thickness More
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Published: 30 June 2023
Fig. 5.16 Solution heat treatment. (a) Batch vertical SHT furnace. (b) Load about to enter quench tank More
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Published: 01 December 2000
Fig. 6.11 Comparison of smooth axial fatigue behavior of Ti-6Al-4V investment castings subjected to various heat treatments (see Table 6.1 ). BUS, broken-up structure; HTH, high-temperature hydrogenation; BST, beta solution treatment; ABST, alpha-beta solution treatment; CST, constitutional More
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Published: 01 October 2012
Fig. 5.16 Schematic diagram of a conventional forging and subsequent heat treatment sequence for producing an α-β structure. Typical temperatures during processing would be 955 °C (1750 °F) for the forging and solution treatment, 730 °C (1350 °F) for annealing, and 540 °C (1000 °F) for aging More
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Published: 01 June 2008
Fig. 28.11 Typical thermomechanical processing sequence for alpha-beta titanium forgings. Typical temperatures during processing would be 955 °C (1750 °F) for the forging and solution treatment, 730 °C (1350 °F) for annealing, and 540 °C (1000 °F) for aging. Typical times during processing More
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Published: 30 September 2024
Fig. 7.13 Microstructures of Ti-5Fe alloy after (a) sintering, (b) extrusion at 900 °C (1650 °F), (c) extrusion at 850 °C (1560 °F), (d) extrusion at 800 °C (1470 °F), (e) after solution treatment and aging at 550 °C (1020 °F) for 4 h, and (f) after solution treatment and aging at 650 °C (1200 More
Book Chapter

Series: ASM Technical Books
Publisher: ASM International
Published: 01 March 2002
DOI: 10.31399/asm.tb.stg2.t61280135
EISBN: 978-1-62708-267-9
... such changes are required. It describes several types of treatments, including stress relieving, in-process annealing, full annealing, solution annealing, coating diffusion, and precipitation hardening. It discusses the temperatures, holding times, and heating and cooling rates necessary to achieve the desired...
Book Chapter

Series: ASM Technical Books
Publisher: ASM International
Published: 01 December 2000
DOI: 10.31399/asm.tb.ttg2.t61120039
EISBN: 978-1-62708-269-3
.... However, because HIP itself is a heat treatment and, in turn, is usually followed by a high-temperature solution treatment at or above the HIP temperature, stress relief may not have any significant effect on final mechanical properties of hot isostatically pressed titanium castings. Heat treatment after...
Book Chapter

Series: ASM Technical Books
Publisher: ASM International
Published: 01 December 2000
DOI: 10.31399/asm.tb.ttg2.t61120055
EISBN: 978-1-62708-269-3
... (annealing) To increase strength by solution treatment and aging To optimize special properties, such as fracture toughness, fatigue strength, and high-temperature creep strength Various types of annealing treatments (e.g., single, duplex, mill, beta, and recrystallization) and solution treating...
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Published: 01 March 2006
Fig. 3 Part of the aluminum-copper phase diagram. The kappa phase, bounded by ABC, is a solid solution of copper in aluminum; CuAl 2 precipitates from this phase on slow cooling or on aging after solution treatment. Source: Ref 5 More
Series: ASM Technical Books
Publisher: ASM International
Published: 01 January 2015
DOI: 10.31399/asm.tb.tpmpa.t54480075
EISBN: 978-1-62708-318-8
... (a) Quenched from above beta transus. (b) Beta phase is mechanically unstable and can transform to martensite with application of stress. Also, a thermal omega may be present. When referring to beta phase stability, note that if the solution treatment is carried out below the beta transus...
Series: ASM Technical Books
Publisher: ASM International
Published: 01 October 2011
DOI: 10.31399/asm.tb.mnm2.t53060333
EISBN: 978-1-62708-261-7
... that can be hardened by heat treatment. Some of the common nonferrous alloys that can be hardened through heat treatment include: Solution-treated and aged aluminum alloys (e.g., aluminum-copper alloys) Solution-treated and aged cobalt alloys Solution-treated copper alloys (such as beryllium...
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Published: 01 January 2015
Fig. 8.14 Cast Ti-6Al-4V broken-up structure, the result of a 1025 °C (1880 °F) solution treatment followed by an 815 °C (1500 °F) aging for 24 h. B, grain-boundary alpha More
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Published: 01 March 2006
Fig. 5 Beryllium-copper phase diagram. The alpha phase holds about 1.55% Be at 605 °C (1121 °F) and about 2.7% at 865 °C (1590 °F). Decreasing solubility of the beryllium causes precipitation of a hard beryllium-copper phase on slow cooling or on aging after solution treatment. Source: Ref 4 More
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Published: 01 March 2002
Fig. 12.14 Micrographs of IN-718 nickel-base superalloy after receiving a high solution treatment at 1038 °C (1900 °F) for differing times. (a) 20 min at 1038 °C, showing presence of prior δ-phase grain boundary precipitates (arrows). 550×. (b) 1 h showing absence of prior δ phase particles More