High temperature strength and failure of the Ni-base superalloy PM 3030

Nganbe, Michel; Heilmaier, Martin

doi:10.1016/j.ijplas.2008.06.005

Cited by 50 publications

(30 citation statements)

References 26 publications

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“…Particle structure and particle strengthening contribution in all other investigated batches of PM 3030 are similar; they have been thoroughly studied in previous publications. [11,12] …”

Section: Analysis and Testing Results And Discussionmentioning

confidence: 99%

“…One sample was tested for each test temperature; the results are shown in Figure 3. It should be pointed out that overall strength level and temperature dependence for PM 3030 materials are known from previous studies [12,13] . The tests performed on R50 merely helped to assess the relative strength different caused by the different recrystallization defect volume fractions.…”

Section: Impact Of Recrystallization Defects On Materials Strength As mentioning

confidence: 97%

“…This decrease can be explained by stronger diffusion and grain boundary deformation processes in recrystallization defect areas [17,18] . In the equicohesion temperature range around 650-680 8C [12,13,19] , no effect of recrystallization defects was expected because grain boundary and grain interior are supposed to have equal strength in this range. The observed relatively broad equicohesion range in contrast to a precise single equicohesion temperature may be due to slight differences in hardening particle parameters.…”

Section: Impact Of Recrystallization Defects On Materials Strength As mentioning

confidence: 99%

“…Trend lines are plotted based on knowledge of overall stress level and temperature dependence from previous publications. [12,13] The equicohesion temperature range is also shown (hatched). This plateau strength is maintained until 100 vol% recrystallization defects, which corresponds to a completely fine grain material.…”

Section: Effect Of Recrystallization Defect Volume Fraction and Grainmentioning

confidence: 99%

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Impact of Recrystallization Defects on the High Temperature Strength of PM 3030

Nganbe

2009

Adv Eng Mater

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The advantage of single crystals has been established for materials used at high temperatures. They are usually manufactured by directional solidification using a premanufactured seed crystal; however, the production of single crystals cannot only be relatively costly, but can even be impossible for some ceramic particle strengthened materials. Homogeneously incorporating thermally stable ceramic dispersoids in a metal melt is very difficult due to strong differences in densities between the two phases. Therefore, such materials are usually manufactured by powder metallurgy (PM), which generally produces ceramic dispersion strengthened alloys initially with an isotropic and fine grain structure. It is then necessary to complete a secondary recrystallization [1,2] of the initial PM material in order to achieve a coarse and elongated grain structure that has proven to show high temperature strength properties close to those of single crystals. [3,4] It should be pointed out that secondary recrystallizing such materials into a single crystal structure is generally too costly or even impossible due to pinning of grain boundaries at hardening particles or segregation of dispersoids. Furthermore, it is well known that not all grains grow into a coarse and elongated structure during secondary recrystallization. Rather, pockets of nonrecrystallized fine grains usually remain, which are then called recrystallization defects. Although the latter are readily recognized as preferred locations for initiation of high temperature damage and failure in ODS superalloys, [5,6] their effect on the actual deformation resistance and high temperature strength has barely been investigated. The present work closes this gap by assessing and quantifying the influence of recrystallization defects on the strength of an oxide dispersion and g 0 precipitation strengthened nickel base superalloy, PM 3030. It shows the dependence of this influence on temperature, recrystallization defect volume fraction, and grain size. The developed principle understanding can be very useful for economically achieving optimal properties. In fact, while completely eliminating recrysallization defects can be imperative for some critical applications, setting their maximal tolerated content too low can lead to unnecessary challenges for process control and excessive manufacturing costs for less critical applications. Materials and Their ManufactureAn incompletely secondary recrystallized batch of PM 3030, a Ni-base superalloy manufactured by Plansee GmbH (Lechbruck, Germany), was investigated. The material was manufactured by the PM route. [7,8] Mechanical alloying (MA) [9,10] of prealloyed powders produced a homogeneous alloy containing a fine oxide dispersion; the nominal chemical composition of PM 3030 is 17Cr-2Mo-3.5W-2Ta-6.6Al-1.1Y 2 O 3 -bal. nickel. The mechanically alloyed powders were then compacted using hot isostatic pressing (HIP) and underwent a company specific thermomechanical treatment including hot extrusion to a final round bar with a diameter o...

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“…Particle structure and particle strengthening contribution in all other investigated batches of PM 3030 are similar; they have been thoroughly studied in previous publications. [11,12] …”

Section: Analysis and Testing Results And Discussionmentioning

confidence: 99%

Section: Impact Of Recrystallization Defects On Materials Strength As mentioning

confidence: 97%

Section: Impact Of Recrystallization Defects On Materials Strength As mentioning

confidence: 99%

Section: Effect Of Recrystallization Defect Volume Fraction and Grainmentioning

confidence: 99%

See 2 more Smart Citations

Impact of Recrystallization Defects on the High Temperature Strength of PM 3030

Nganbe

2009

Adv Eng Mater

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“…For example, conventional ODS superalloys such as MA 6000 and PM 3030 [4,5] show excellent creep resistance by combination of gamma prime precipitation strengthening at intermediate temperature and dispersion strengthening at high temperature. These ODS alloys are usually manufactured by mechanical alloying (MA), in which the elemental metal and oxide powders are subjected to the high-energy ball milling to allow the nano-sized oxide particles to be homogeneously dispersed in alloy matrix powders [6].…”

Section: Introductionmentioning

confidence: 99%

Microstructure Evolution of Ni-Based ODS Superalloy Powders During Horizontal Rotary Ball Milling

Lee¹,

Kim²,

Park³

et al. 2017

Archives of Metallurgy and Materials

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Microstructure evolution of Ni-based oxide dispersion-strengthened alloy powders with milling time is investigated. The elemental powders having a nominal composition of Ni-15Cr-4.5Al-4W-2.5Ti-2Mo-2Ta-0.15Zr-1.1Y 2 O 3 in wt % were ball-milled by using horizontal rotary ball milling with the change of milling velocity. Microstructure observation revealed that large aggregates were formed in the early stages of ball milling, and further milling to 5 h decreased particle size. The average crystalline size, estimated by the peak broadening of XRD, decreased from 28 nm to 15 nm with increasing milling time from 1 h to 5 h. SEM and EPMA analysis showed that the main elements of Ni and Cr were homogeneously distributed inside the powders after ball milling of 5 h.

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Evaluation of Processing Conditions on the γ′ Morphology of an Oxide Dispersion Strengthened Ni‐Based Superalloy

et al. 2020

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Herein, the evolution of the microstructure of a newly developed oxide dispersion strengthened (ODS) Ni‐based superalloy with emphasis on γ′ morphology during different processing conditions is investigated. X‐ray analysis of severely deformed mechanically alloyed (MAed) powders shows that the as‐milled nano‐sized crystallite size increases with annealing associated with the sharp drop of dislocation density. At the same time, by annealing MAed powders γ′ precipitates above 300 °C, and depending on the aging treatment regime, Vickers microhardness changes mainly due to γ′ distribution and dislocation release. The thorough evaluation of γ′ morphology in the microscale shows that in contrast to the spherical shape of γ′, after heat treatment of solutionized MAed ODS superalloy, irregular‐shaped γ′ exist in the MAed ODS superalloy due to severe plastic deformation during mechanical alloying. However, a unique nanostructured lamellar morphology forms in the γ′ precipitates with different lamellae directions. This structure is stable in all subsequent processing steps with γ′ lamellae of (011true¯) planes and intervals of 20–30 nm. The scanning transmission electron microscopy (STEM)–high‐angle annular dark‐field (HAADF) composition analysis clarifies that the nanostructured lamellar morphology shows no partitioning of alloying elements, and its origin may be attributed to the formation of antiphase domain boundaries.

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High temperature strength and failure of the Ni-base superalloy PM 3030

Cited by 50 publications

References 26 publications

Impact of Recrystallization Defects on the High Temperature Strength of PM 3030

Impact of Recrystallization Defects on the High Temperature Strength of PM 3030

Microstructure Evolution of Ni-Based ODS Superalloy Powders During Horizontal Rotary Ball Milling

Evaluation of Processing Conditions on the γ′ Morphology of an Oxide Dispersion Strengthened Ni‐Based Superalloy

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