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Use Cases: Inorganic Systems
G. B. Olson
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Cohen’s Reciprocity
Cohen’s Reciprocity
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System chart
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Hierarchy of Design Models
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Example: Parametric Design with CMD Matrix + Strengthening Dispersion Design
Grain Pinning Dispersion Design
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Hard Material Use-Case Groups
• Cobalt alloys • Nanodispersion-strengthened shape
memory alloys • Si-based insitu composites • Leveraging: Steel Research Group
projects
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Cobalt Alloy Designs G. Olson (NU), D. Dunand (NU), D. Seidman (NU), P. Voorhees (NU),
M. Stan (NAISE, ANL) C. Wolverton (NU)
• Motivation: – Need turbine blade alloys that exceed
the use temperatures of Ni-based superalloys
– Wear resistant ambient temperature applications to replace Be-Cu
• Goals: – Near-term: Ambient temperature
bushing alloy – Long-term: High-temperature
aeroturbine superalloy
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PH Cobalt System Chart
VIM/VAR melting
Homogen-ization
Hot working >4” dia.
Solution treatment
Machining
Tempering
Processing Structure
Solidification structure
- Inclusions- Eutectic
Grain Structure- Grain size- GB chemistry- pinning particles- Avoid cellular reaction
Nanostructure- Low-misfit L12- Size & fraction- Avoid embrittlingphases
Matrix- FCC (avoid HCP transformation)- Low SFE- Solid solution strengthening
Properties
Non-toxic
Strength-120 to 180 ksicompressive YS- CW not required for strength
Wear- Low CoF- Galling/fretting resistance
Toughness-Highly ductile after solution treat- High toughness fully hardened
Corrosion Resistant
Environmentally Friendly
Bearing Strength
Wear Resistance
Damage Tolerant
Formable
Performance
Corrosion Resistant
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700C
γ γ’
B2
Laves
L12 Stability in Ni vs Co Systems
Ni
Co
γ γ’
B2
Liq.
γ
Liq.
η B2
γ γ’
η
B2
700C
Ni-Al Ni-Ti Ni-Al-Ti
Co-Ti Co-Al Co-Ti-Al
Liq.
γ γ’
B2 Laves
γ
Liq.
B2
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CALPHAD Step Diagram
γ' γ
L
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Validation of design with LEAP characterization LEAP validation of alloy nanostructure after tempering at ~780°C:
FCC (Co-rich) matrix and γ’ [L12 crystal structure, (Co,Ni)3(Ti,V)-type] strengthening nanoprecipitates
• Precipitate is enhanced in Co, Ti; slightly enhanced in Ni, V
• Matrix is enhanced in Fe, Cr
Matrix
Precipitate is enhanced in Co, Ti;
slightly enhanced in Ni, V
Matrix is enhanced in Fe, Cr
Precipitate
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Approach • Years 1 and 2:
– Accelerated expansion of Co system multicomponent solution thermodynamics, molar volume, and diffusivity databases (high throughput theory and experiment) to incorporate Nb, Mo, Ta, Re and B for FCC, L12 and L phases.
– LEAP microanalytical calibration and validation. • Years 3 and 4
– Prototype alloy validation and preliminary process optimization
– PrecipiCalc calibration and application to detailed process optimization
– Solidification and homogenization modeling for scale-up – Continuum modeling of creep deformation dynamics – Neutron and X-ray diffraction evaluation of load
partitioning
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G. Olson (NU), D. Dunand (NU),W-K. Liu (NU) D. Seidman (NU),
A. Umantsev (FS), C. Wolverton (NU)
Nanodispersion-‐Strengthened Shape Memory Alloys
• Motivation: – Widely used in medical, aerospace and
automotive sectors – Current alloys are susceptible to
instability after many cycles
• Goals: – Near-term: Pd-stabilized alloys for
medical devices – Long-term: High-temperature
aeroturbine & automotive actuators
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Processing
Aging
Solution treatment
Hot working
Properties
Strength
Af Temperature
Transformation Range (ΔTR=Af-As)
Hysteresis (ΔTH=Af-Ms)
Toughness Ductility
Structure
Nanodispersion (Ni,Pd,Pt)2 (Ti,Zr,Hf) Al
Heusler Phase Low Misfit
Dispersion Particle Size Volume Fraction
B2 Matrix (Ni,Pd,Pt) (Ti,Zr,Hf,Al)
Al (Substitution for Ti)
Zr/Hf (Substitution for Ti)
Performance
Longer Cyclic Life
Operating Temperature
Faster Response
Higher Output Stress
Grain refining oxides Arc-melting Ti4Ni2O, Y2O3
Pd/Pt (Substitution for Ni)
Powder Consolidation
SMA System Chart
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20nm
1hr 3.5hr 7.5hr 16hr 50hr
0.0 1 10 1000.0
2
4
6
Particle Radius(nm)
Ageing time at 550C(hr)
1023
1024
1025
NumberDensity (m-3)
0
2
4
6
8
10
Phase fraction(%)
0 2 4 6 8 10
0
200
400
600
800
1000
1200
1400
1600
1800
Δσ/f1/
2
Precipitate radius (nm)
Precipitation strengthening in (Pd,Ni)50(Ti,Al)50 alloys
Ageing at 550°C
Optimal particle radius=2.3nm
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0
350
0 0.018StrainS
tress
(MP
a)0
1200
0 0.06Strain
Stre
ss (M
Pa)
-0.4
0.4
-50 -30 -10 10Temperature (C)
Hea
t Flo
w (W
/g)
SMA Cyclic Stability
-0.16
0.16
-55 -35 -15 5 25Temperature (°C)
Hea
t Flo
w (W
/g)
hea4ng
cooling
hea4ng
cooling
Af + 25°
Yield stress and hysteresis width decrease and permanent elonga4on increases
Nemat-‐Nasser2006
Thermal cyclic stability
Mechanical cyclic stability (compression)
Af + 63°
Ti49.3Ni50.8 Ni20Pd30Ti46Al4
Aged 600°C, 5h
N=5
0.6% permanent set
N=6
< 0.2% permanent set
1 4 2 3
1 4 2 3
30 cycles
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TiNi Fatigue Life Prediction: Effect of Increased B2 Strength
Increased life (N) of strengthened alloy compared typical life (No)
• 50% increase in matrix strength results in increase in fatigue limit (at 109 cycles) from 0.27% to 0.39%
• Benefit of B2 strengthening increases as applied strain decrease
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Approach
• Years 1 and 2: – Accelerated expansion of solution thermodynamics, molar
volume, and diffusivity database (high throughput theory and experiment) of Ti-Zr-Hf-Ni-Pd-Pt-Fe-Co-Ni-Al-O-C system for B2, L21, M(O,C), M6O, and martensitic phases
– LEAP microanalysis calibration and validation – D3D characterization of fatigue nucleants and ABC continuum
modeling of fatigue nucleation
• Years 3 and 4 – Prototype evaluation and preliminary process optimization – PrecipiCalc calibration and application to process optimization – ABC continuum modeling of oxide and carbide evolution during
deformation processing – Solidification and homogenization modeling for process scale-up
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In-Situ Si Composite Materials P. Voorhees (NU), J. De Pablo (UC), W. Chen (NU),
S. Davis (NU) , C. Wolverton (NU)
Si-CrSi2 composite (Fischer and Schuh, J. Am Ceram. Soc, 2012)
• Motivation: – Corrosion resistant, tough alloys – Avoid the complications of
classical ceramic processing, such as sintering
– Employ insitu Si-composites
• Goals: – Near-term: A multicomponent
eutectic growth model – Long-term: A tough, castable Si
alloy
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Design Approach
• Primary mechanism of toughening is the delamination of interphase interfaces
• Composites are produced via eutectic solidification • Industrial partner: Dow Corning
Processing Structure Properties
Melting
Eutectic solidificat
ion
Thermal treatmen
t
CrSi2 reinforcement
Si matrix
Matrix / reinforcement
interface
Toughness
Strength
Corrosion resistance
Performance
Castable
Strength in compressio
n
Wear resistance
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Growth of Si Composites
Due to the anisotropy of the solid-liquid interfacial energy, Si alloys can grow as irregular eutectics
Isotropic Anisotropic
Al-Si
L L
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Approach
• Years 1 and 2: – Use multicomponent thermodynamics to inform eutectic growth
models – Generalize eutectic growth models to multicomponent systems,
use existing corrections for anisotropic interfacial energy – Predict solidification paths, and thus volume fractions of phases,
and length scales of the solidified morphologies • Years 3 and 4
– Phase field models for systems with highly anisotropic solid-liquid interfacial energy
– Develop descriptors of the microstructure – Using these descriptors, and models of the toughening process,
design optimal microstructures – Using models for the multicomponent eutectic solidification
process develop optimal microstructures – Characterization using X-ray tomography
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2014 SRG Design Projects
• ONR Cyberalloys (Olson, Freeman) - CMD of Fe & Ti alloys for blast and fragment protection • DOE/GM Lightweighting Initiative (Olson, Wolverton,
Voorhees) - CMD of cast aluminum for cylinder heads • DOE/CAT Lightweighting Initiative (Olson, Liu) - CMD of cast steels for crankshafts • ArcelorMittal AHSS (Olson) - CMD of high-strength automotive Q&P TRIP steels • NIST/NIU MSAM Additive Manufacturing (Olson, Liu, Cao) - CMD of Fe & Ti alloys for additive manufacturing DARPA/Honeywell Open Manufacturing (QuesTek) - ICME for SLM additive manufacturing of Ni 718+