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Mechanical properties of heat treated Ti-5Al-5V-5Mo-3Cr, an attempt to define critical properties of various microstructural features The properties and microstructure of Ti-5Al-5V-5Mo-3Cr were characterized under various stress states after the following heat treatments: 1) beta anneal and air cool; 2) beta anneal + solution heat treatment in the alpha-beta range; 3) beta anneal + solution heat treatment and ageing in the alpha-beta range. For each condition, the damage mechanisms and final fracture modes were evaluated and rationalized on the basis of microstructural features. The true fracture stresses for the various conditions are compared. Beta annealed material exhibits intense localized slip deformation leading to early crack formation and fracture. This mechanism is explained in relation to the presence of fine metastable phase precipitates resulting from the air cool step. Grain size dependence of the yield stress is described in terms of the Hall-Petch relationship. Authors: Roque Panza-Giosa – Goodrich Landing Gear
Dr. David Embury - McMaster University Dr. Zhirui Wang - University of Toronto Dr. Xian Wang - McMaster University
September 22, 2008 Titanium Conference Page 1
Mechanical properties of heat treated Ti-5Al-5V-5Mo-3Cr - An attempt to define critical properties of various
microstructural features
Roque Panza-Giosa
Supervisors: Dr. David Embury - McMaster University Dr. Zhirui Wang - University of Toronto
Other contributors: Dr. Xian Wang - McMaster University
Goodrich Proprietary Page 2September 22, 2008
A new β Titanium alloy for aircraft Landing Gears
• Advantages of Ti-5Al-5V-5Mo-3CrHigher mechanical properties than Ti-10V-2Fe-3Al
Higher hardenability – up to 150 mm
Easy to melt, not prone to segregation
Can be machined in the final heat treated condition
0.30 maxZr0.18 max.O4.0 - 5.5Mo4.0 - 5.5V
0.10 max.C2.5 - 3.5Cr0.30 - 0.50Fe4.4 - 5.7Al
Weight %ElementWeight %ElementWeight %ElementWeight %Element
0.30 maxZr0.18 max.O4.0 - 5.5Mo4.0 - 5.5V
0.10 max.C2.5 - 3.5Cr0.30 - 0.50Fe4.4 - 5.7Al
Weight %ElementWeight %ElementWeight %ElementWeight %Element
Chemical composition of Ti-5Al-5V-5Mo-3Cr, metastable β alloy
Goodrich Proprietary Page 3September 22, 2008
BLG Bogie BeamTi-10V-2Fe-3Al
Overall size: 167.5 x 22.4 x 27.2 inch4255.0 x 568.1 x 689.8 mm
Weight: 3210 kg
In addition to mechanical properties, we must consider the sections sizes involved and the need to achieve uniform properties in sections up to 8” (200mm).
1m
Goodrich Proprietary Page 4September 22, 2008
Microstructure of Ti-5553After β annealing, microstructure consists of re-crystallized β grains with a very fine dispersion of ω phase
After α + β solution heat treatment (starting from α + β forged), the microstructure is primary globular α and retained β matrix, no ω phase
Upon ageing – develop laths of fine α precipitating from the retained β
Goodrich Proprietary Page 5September 22, 2008
Transformation of the retained β PhaseTe
mpe
ratu
re
% β stabilizer
β
α
α + β
β transus
Pseudo-Binary Phase Diagram
●
●
ω + β β’+β
Ms
ω - hexagonal metastable phase which forms when α formation is difficult
β’ – solute lean metastable phase which forms when ωformation is suppressed, β’coherent with β. Also known as phase separation (β→ β + β’)
Possible reactionsβo → β + αβo → β + ω→ β + ω + α → β + αβo → β + β’ → β + β’ + α → β + α
Goodrich Proprietary Page 7September 22, 2008
Models to predict yield and fracture
Used to predict yield and fracture under complex stress states: Tresca, von-Mises, Mohr’s.
Goodrich Proprietary Page 8September 22, 2008
- We have a complex microstructure highly dependent on heat treatment cycle chosen
- Strive to understand the microstructural changes and their effect on mechanical properties
Objectives of Current Work
Characterize the microstructure after solution heat treatment in the β, α-β and after ageingObtain mechanical properties for tension, compression for each heat treat cycleRationalize the mechanical properties on the basis of microstructural features by characterizing the deformation, damage and fracture modes
Goodrich Proprietary Page 9September 22, 2008
Summary of Current WorkHeat Treatments Studied
α-β solution heat treatment at 790ºCα-β solution heat treatment + ageing at 600ºCα-β solution heat treatment + ageing at 500ºCβ annealing followed air coolingβ annealing followed by α-β solution heat treatment at 790ºCβ annealing followed by direct at 600ºC
MicrostructureOptical, SEM and TEM
Mechanical PropertiesTension Compression Shear
Fractographic AnalysisOptical and SEM
Goodrich Proprietary Page 11September 22, 2008
Etched in Kroll’s
Microstructure after β annealing at 900ºC for 1.25hr.
Ti-5553 microstructure consists of equiaxed β; average grain size is ~200 µm
As-forged Ti-5553 microstructure.
Goodrich Proprietary Page 12September 22, 2008
Etched in Kroll’s
Microstructure after solution heat treatment at 790ºC + AC
• After solution heat treatment, microstructure consists of uniformly distributed primary α in retained β matrix, primary α appears semi-coherent• Primary alpha (2-5 µm in diam.) ƒ = 16%. Sub-grain boundaries (~5 µm) are evident
Goodrich Proprietary Page 13September 22, 2008
a) Solution heat treated b) Aged 15 minutes c) Aged 60 minutes
b) Localized dark etching regions reveal non-homogeneous precipitation of α within retained βc) Complete transformation within retained β regions
Microstructural changes with ageing at 600ºC
Goodrich Proprietary Page 15September 22, 2008
Comparison of Mechanical Properties, Fracture Stress after Various Heat Treatments and Test Methods
Properties of Ti-5553 after β-annealing.
942.6834.3Compressionβ annealed at 900ºC
937.5782.6Tensionβ annealed at 900ºC
Fracture Stress (MPa)Yield Stress (MPa)TestHeat Treat Condition
1581.11244.5Tensionα-β solution treated + Aged 600ºC
1511.71289.3Tension
1454.7858.4Tensionα-β solution treated (790ºC 120 min)
α-β solution treated + Aged 500ºC
1582.21265.2Compressionα-β solution treated + Aged 600ºC
Fracture Stress (MPa)Yield Stress (MPa)TestHeat Treat Condition
Properties of Ti-5553 after α-β- ST and Ageing
Goodrich Proprietary Page 16September 22, 2008
True stress-strain curve comparison
True Stress-Strain Curves
0
200
400
600
800
1000
1200
1400
1600
0.000 0.100 0.200 0.300 0.400 0.500 0.600True Strain
True
Stre
ss (M
Pa)
Alpha-Beta ST+Aged 0 hrs - Tension Alpha-Beta ST+Aged 6 hrs - TensionAlpha-Beta ST+Aged 6 hrs - CompressionBeta Annealed - TensionBeta Annealed - Compression
Goodrich Proprietary Page 17September 22, 2008
• The α-β solution heat treated and the aged condition have roughly the same fracture stress
• The β annealed condition has much lower fracture stress and ductility
• For each heat treat condition, the fracture stress in tension and compression are the same
Above observations suggest that a shear event controls fracture process
Mechanical property observations
Goodrich Proprietary Page 19September 22, 2008
Morphology of Tensile Fracture
SEM Image of fractured tensile specimen.Note the faceted appearance and parallel ridges.
Goodrich Proprietary Page 20September 22, 2008
Optical image of fractured tensile specimen; slip bands and transgranular cracks throughout deformed region
Cross Section of Tensile Fracture
Goodrich Proprietary Page 21September 22, 2008
Damage Process During Plastic Deformation
Localized slip bands, leading to transgranular cracks within grains
Goodrich Proprietary Page 22September 22, 2008
Fracture stress is a function of the grain size
β annealed condition follows Hall-Petch relationship; the friction stress is of the order of 780MPa.
σ = σi + K d-1/2
True-Fracture Stress vs Beta Grain Size
σf =777 + 71.7 d-1/2
750
850
950
0.75 1.25 1.75 2.25
Beta Grain Size, d^-0.5 (mm-0.5)
True
-Fra
ctur
e St
ress
(MPa
)
Goodrich Proprietary Page 23September 22, 2008
Damage Process Leading to Fracture During Plastic Deformation
SEM Image of polished three point bend specimen. Note the steps and cracks due to localized slip
Goodrich Proprietary Page 24September 22, 2008
BF and DF images (foil prepared by ion milling) showing ω phaseω particles are of the order of ~20 nm
Goodrich Proprietary Page 25September 22, 2008
TEM, BF and DF images (foil prepared by ion milling)
Localized slip mechanism: 1) ω particles are cut by dislocations2) this plane (band) now offers less
resistance than adjacent planes3) further slip is localized to this plane/band
Goodrich Proprietary Page 27September 22, 2008
Fracture Morphology of Tensile Specimens - Solution Treated Cond.
Transgranular fracture consisting of uniform dimples 5 µm.
Goodrich Proprietary Page 28September 22, 2008
Mode of Fracture for α-β Solution Heat Treatment
and Aged at 600ºC
Goodrich Proprietary Page 29September 22, 2008
Transgranular fracture consisting of uniform dimples 5 µm.
Fracture Morphology of Tensile Specimens- Solution Treated + Aged
Goodrich Proprietary Page 30September 22, 2008
Tensile and Compressive Crack PropagationSEM images of secondary crack tip from compression (left) and tensile tests (bottom) – showing crack path through both GB and primary α/transformed-β interface.
Fracture occurs by shear at 45º
Nickel layer
Goodrich Proprietary Page 31September 22, 2008
Fracture Mode ObservationsFor many alloys the fracture stress in compression is significantly greater than that in tension. In Ti-5553, the fracture stress is the same in tension and in compression. This suggests the material fails when a critical shear stress isreached, hence the biaxial fracture stress envelope is an extension of the yield envelope.
σ1
σ2
σ1
σ2
Goodrich Proprietary Page 33September 22, 2008
Fig.1 [110]β zone axis pattern taken from Ti-5Al-5V-5Mo-3Cr (Left) and Ti-6Al-4V (Middle) alloys respectively and key to both patterns (Right) showing the coexistence of ω and/or α phase (foil prepared by ion milling)A comparison of selected electron diffraction (SAD) pattern in [110]β zone axis obtained from our sample with that
characterized by Z. Fan and A. P. Miodownik in Ti-6Al-4V alloy (Journal of Materials Science, 29 (1994) 6403-12) is shown in Fig.1. It can be seen that in β grain there are coexistence of both ω and α phases. Dark field (DF) image gives very fine ωand/or α particle as shown in Fig.2. Fig.3 corresponds to micrographs at high magnifications.
Goodrich Proprietary Page 34September 22, 2008
Fig.7 [001]β zone axis pattern taken from Ti-5Al-5V-5Mo-3Cr (Left and middle) and Ti-14Mol-6Al (Right) alloys respectively (foil prepared by ion milling)
Fig 7 which is similar to that of solutionzied and aged Ti-14Mo-6Al alloy (C. G. Rhodoes and J. C. Williams, Metallurgical Transaction A, 6 (1975) 2103-14). In the pattern the precipitate reflections are arced, or curved, rather than streaked in a particular crystallographic direction. This type of alpha phase is referred as Type 2 alpha phase by C. G. Rhodoes and J. C. Williams. Fig.8 is BF and DF image of this type of alpha phase in Ti-5Al-5V-5Mo-3Cr alloy.