Hot deformation behavior and flow stress modeling of a Ni-based superalloy

Detrois, Martin; Antonov, Stoichko; Tin, Sammy; Jablonski, Paul D.; Hawk, Jeffrey A.

doi:10.1016/j.matchar.2019.109915

Cited by 59 publications

(17 citation statements)

References 32 publications

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“…Zhang et al [ 28 ] used the Artificial Neural Network model and the strain‐compensated Arrhenius model to describe the hot deformation behavior of FGH98 superalloy near the γ′ solvus. In this study, the constitutive modeling of flow stress, the relationship of the peak stress on deformation parameters (temperature and strain rate) can be described as follows [ 5,7 ]

\overset{false˙}{ε} = A_{1} σ^{n_{1}} \exp (\frac{- Q}{R T})

\overset{false˙}{ε} = A_{2} [\sinh (β σ)] \exp (\frac{- Q}{R T})

\overset{false˙}{ε} = A {[\sinh (α σ_{p})]}^{n} \exp (\frac{- Q}{R T})

Z = \overset{false˙}{ε} \exp (\frac{Q}{R T}) = f (σ)

where

\overset{ε}{true}

is the strain rate (s −1 ), σ p is the peak stress (MPa), A (s −1 ) and α (MPa −1 ) are materials constants, n is the stress exponent, R is the universal gas constant (8.314 J K −1 mol −1 ), T is the deformation temperature (K), Q is the apparent activation energy for deformation (J mol −1 ), Z is the Zener–Holloman parameter. Taking natural logarithm of both sides of Equation ()–()

\ln \overset{false˙}{ε} = \ln A + n_{1} \ln σ_{normalp} - \frac{Q}{R T}

\ln \overset{false˙}{ε} = \ln A + β σ_{normalp} - \frac{Q}{R T}

…”

Section: Resultsmentioning

confidence: 99%

“…Zhang et al [28] used the Artificial Neural Network model and the strain-compensated Arrhenius model to describe the hot deformation behavior of FGH98 superalloy near the γ 0 solvus. In this study, the constitutive modeling of flow stress, the relationship of the peak stress on deformation parameters (temperature and strain rate) can be described as follows [5,7]…”

Section: Arrhenius-type Constitutive Modelingmentioning

confidence: 99%

“…Nickel-based superalloys have been found the widespread use of the aeronautical and aerospace industry, [1][2][3] due to their excellent high-temperature strength, [4] fatigue capability, creep resistance, corrosion, and oxidation resistance. [5,6] For disk superalloys, Inconel 718, strengthened by the Ni 3 Nb phase known as gamma double prime (γ 00 ), is still widely used at temperature up to %650 C caused by the thermodynamically unstable γ 00 precipitate at higher temperatures. To meet the need of turbine disks in the next-generation engine, several novel superalloys have been developed in previous studies, such as Allvac 718Plus, [7] Udimet 720Li, [8,9] AD730, [10] FGH100L, [11] GH4151, [12] and GH4065.…”

Section: Introductionmentioning

confidence: 99%

See 2 more Smart Citations

Hot Deformation Characteristics and Dynamic Recrystallization Mechanisms of a Novel Nickel‐Based Superalloy

Jia

et al. 2020

Adv Eng Mater

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The hot deformation characteristics of a novel nickel‐based superalloy is investigated via the isothermal compression test in temperature range of 1000–1150 °C and strain rate of 0.001–10 s−1 under the true strain of 0.8. The hot deformation characteristics of GH4065 alloy are studied here for the first time. Based on the flow stress data, it is observed the typical features of flow curves exhibit the occurrence of dynamic recrystallization (DRX) during the hot deformation process. The constitutive equation in the Arrhenius‐type model is established, and activation energy (Q) is determined as 844.787 kJ mol−1. The microstructure evolution and DRX mechanism are investigated by electron backscatter diffraction (EBSD) and transmission electron microscopy (TEM) technique. The results reveal that the fraction of low angle grain boundaries (LAGBs) decrease gradually with the increase in deformation temperature, whereas the fraction of Σ3 boundaries increase first and then decrease. For γ + γ′ dual‐phase region, the particle‐induced DRX (PIDRX), characterized by the generation of sub‐grains accelerated by γ′ precipitates pinning dislocations, and discontinuous dynamic recrystallization (DDRX) are the dominant nucleation mechanism of DRX. For γ quasi‐phase region and γ single‐phase region, the occurrence of bulged grain boundaries with twins further illustrates that DDRX plays a more significant role.

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\overset{false˙}{ε} = A_{1} σ^{n_{1}} \exp (\frac{- Q}{R T})

\overset{false˙}{ε} = A_{2} [\sinh (β σ)] \exp (\frac{- Q}{R T})

\overset{false˙}{ε} = A {[\sinh (α σ_{p})]}^{n} \exp (\frac{- Q}{R T})

Z = \overset{false˙}{ε} \exp (\frac{Q}{R T}) = f (σ)

where

\overset{ε}{true}

\ln \overset{false˙}{ε} = \ln A + n_{1} \ln σ_{normalp} - \frac{Q}{R T}

\ln \overset{false˙}{ε} = \ln A + β σ_{normalp} - \frac{Q}{R T}

…”

Section: Resultsmentioning

confidence: 99%

Section: Arrhenius-type Constitutive Modelingmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

See 1 more Smart Citation

Hot Deformation Characteristics and Dynamic Recrystallization Mechanisms of a Novel Nickel‐Based Superalloy

Jia

et al. 2020

Adv Eng Mater

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show abstract

“…The true compressive stress–strain data obtained from the isothermal hot compression tests under different strain rates and temperatures can be used to determine the material constants used in the constitutive equation. The Arrhenius equation has been widely employed to describe the relationship between the strain rate, flow stress and temperature, especially at high temperatures, as follows:

Z = \overset{ε}{true} \exp ((), \frac{Q}{italicRT})

\overset{ε}{true} = A_{1} σ^{m} \exp ((), - \frac{Q}{RT}) ((), for low stress level)

\overset{ε}{true} = A_{2} \exp ((), βσ) \exp ((), - \frac{Q}{RT}) ((), for high stress level)

\overset{ε}{true} = A {[\sinh (italicασ)]}^{n} \exp ((), - \frac{Q}{RT}) ((), italicfor italicall italicstress level)

where Z is the Zener–Hollomon parameter,

\overset{ε}{true}

is the strain rate (s −1 ), n, m, α, β, A 1 , A 2 , and A are constants of the material, α = β/m , σ is the flow stress (MPa), Q is the activation energy of deformation (J/mol), R is the universal gas constant (8.314 J/mol K), and T is the absolute temperature (K).…”

Section: Resultsmentioning

confidence: 99%

Hot deformation behavior of A390 alloy produced by semi‐continuous cast

Huang

Sun

Cao

et al. 2020

Mat Design & Process Comms

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A390 alloy is characterized by lightweight, low coefficient of thermal expansion and excellent mechanical properties, making it appealing for the automotive and aerospace industries. In this study, the hot deformation behavior of a direct‐chill A390 alloy produced by semi‐continuous cast was investigated. The flow stress was found to be substantially sensitive to the applied strain rate and the temperature. A series of constitutive equations coupling flow stress with strain, strain rate and temperature were established and the material constants as the functions of strain were determined. The relationship between predicted stresses and the experimental results were discussed. In addition, the predictability of the developed constitutive equation was quantified and the processing map was established, which would provide guidance for the optimized processing parameters of deformation behavior for A390 Alloy.

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“…A processing map is an effective way to optimize the hot‐working parameters and analyze the mechanisms under different deformation conditions, and the processing map has been widely adopted during the hot‐working processes of a variety of metallic materials. [ 8–14 ] Prasad [ 15 ] first presented a processing map, which can be used to predict and analyze the deformation mechanism of materials and optimize reasonable hot deformation parameters to avoid material defects.…”

Section: Introductionmentioning

confidence: 99%

Study on Flow Behavior and Processing Maps of High‐Ti Low‐C Microalloyed Steel during Hot Compression

Song

Gao

Wang

et al. 2021

steel research int.

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Deformation behavior of a high‐Ti low‐C microalloyed steel is studied by isothermal compression tests at temperatures of 800–1100 °C and strain rates of 0.1–10 s−1. The results indicate that the lower the strain rate and higher the temperature of steel, the more likely is the dynamic recrystallization. The stress–strain predicted by the constitutive model, which is established based on the experimental data, are in good agreement with the experimental results. It is noted from the processing maps of steel at various strains that there is instability zone which should be avoided during thermal processing at strain rate less than 1 s−1. The range of 850–1100 °C and 5–10 s−1 strain rate is more conducive to the processing of experimental steel. The movement of grain boundaries, subboundaries, and dislocations is hindered by precipitates in steel. In addition, the mean grain size of austenite at 0.1 s−1 is larger than 5 s−1. This is mainly because low strain rate provides more time for growth of grains.

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Hot deformation behavior and flow stress modeling of a Ni-based superalloy

Cited by 59 publications

References 32 publications

Hot Deformation Characteristics and Dynamic Recrystallization Mechanisms of a Novel Nickel‐Based Superalloy

Hot Deformation Characteristics and Dynamic Recrystallization Mechanisms of a Novel Nickel‐Based Superalloy

Hot deformation behavior of A390 alloy produced by semi‐continuous cast

Study on Flow Behavior and Processing Maps of High‐Ti Low‐C Microalloyed Steel during Hot Compression

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