SIandAII StressCorrCracking Lecture
Transcript of SIandAII StressCorrCracking Lecture
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Stress Corrosion Cracking and Fatigue:
mechanical load (tension)+
Corrosive environment
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Material
EnvironmentStresses - Aggressive media- Temperature- Potential /Current- Microfluidics
- Design- Mechanical bulk stresses- Internal stresses Production
When does Stress Corrosion Cracking (SCC) occur ?
° Simultaneous influence of tensile stresses and aggressiveenvironment
° Only one of these parameter does not induce crack growth
SCC is a system not a materialproblem Fatigue Corrosion
SCC
- Composition- Heat treatment- Microstructure- Surface condition
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Stress Corrosion Cracking: process steps
Definition: Stress Corrosion Cracking is the initiation and slow growth of cracks under the simultaneous influence of tensile stresses and aggressive environment
SCC processes is divided in three phases:
1. Incubation2. Crack growth 3. Breaking
° Incubation time is the most important aspect for the life time of a component
° SCC is from all the corrosion attack, the one resulting in the fastest damage of materials 3
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Type of crack propagation
Intergranular: Transgranular:
Attack at the grain attack through theboundary grains
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SCC: important features
° Materials breakdown happens at macroscopic scale, without deformation and perpendicular to the stress direction
° No measurable material removal
° No visible corrosion products
° In most of the SCC failure, corrosion initiation is difficult to detect
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Types of SCC corrosion attack° There is a whole range of attack ranging from: at one end the purely intergranular attack and on the other end the brittle fracture
Inte
rgra
nula
r cor
rosi
on
Brit
tle fr
actu
re
Corrosion Tension
Stress – deformation inducedMetal dissolution
Adsorption induced brittle fracture
Steel
NO-3
Al-Zn-Mg
Cl-Brass
NH3
18/8 CrNi
Cl-
Mg-Al
Cr2-4/ Cl-
Ti
CH3OH
SteelHigh strength
H2O
small crack propagation rate large
Defined Crack direction
Crack evolutionControlled by deformation
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SCC: 2 main mechanisms° For small until medium crack propagation rates:
Type 1: anodic metal dissolution accelerated by stress
It is an electrochemically controlled processes with following model:
crackpropagation
metalactivecrack tip
passivecrack wall
Passive oxide
elec
trol
yte
Cathodic partial reaction
Plasticdeformation
Crack electrolyte
diffusion, convection
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Type 2: adsorption induced brittle fracture° For fast crack propagation rates, the cathodic reactions plays a larger role (anodic dissolution is too slow)
°At the crack tip, adsorbed or speciesdiffused in the metalweaken the metallicbinding forces
° the most dangerousspecies: hydrogen
causes embritlementHIC (hydrogen inducedcracking)
electrolyte
metal
Adsorbed anions
shear plane
crevice plane
From adsorption weakened metal bounds
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SCC: summary of mechanisms
Anodic SCC
° Dominated by anodic metal dissolution
° Crack propagates through accelerated dissolution due to applied stress
Stainless Steel
° Cracks are propagating from the surface
Cathodic SCC
° Dominated by H2 production (also for example from cathodic deposition of protecting layers)
°Crack propagates because of hydrogen embritlement due to hydrogen diffusion
High strength steel
°Crack are also generated inside the material
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° Not a single clearly defined crack !Near the surface:
Secondary crack with ramification
ca. 2 mm
Ramified crack propagation observed on the metallographic cross section
ca. 50 µm
SCC: typical crack evolution
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- Sem investigation of the fracture surface
Empa unterwegs – Sion, 09. 11. 2006
Example: fractographic analysis of broken cable
Ductile
Brittle (fragile)
Intergranular
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Damaged surface eloxal layer
Intergranular attack
SCC: metallographic investigation° Example of SCC on coated (thick oxide) aluminum
- Presence of intergranular attack near the main crack- Detection of Cl- in the material by EDX
EDX analysis of internal
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Model experiments: aspects of fracture mechanics
° Fracture mechanics can give useful information on crack propagation rates in technical application
° It is based on consideration of macroscopic parameterslike crack length, applied tensile stress (S), sample geometry
° Assumption: test are alwaysperformed on notched(depth:d) specimens (width:w)
° Initial crack geometry + environment
critical applied stress
SS
S
W
Wd
d
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Experimental characterization of SCC° Crack propagation rate as a function of applied stress intensity
Domain 1:When the critical load for SCCis reached (KIscc) , a fast increaseof the crack propagation rateIs observed
Domain 2:Constant SCC propagation rate typical for the influence of electrochemical control
Domain 3 and 4:If the KIc is reached, the standard brittle fracture is taking place as in absence of aggressive environmentalinfluence Applied stress K
Log
(cra
ck p
ropa
gatio
n ra
te
d /
t)
Schematic evolution of crack propagation for SCC
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Important parameters for the evolution of SCC° Incubation (crack formation)
Chemical or mechanical damage of the passive layer
Critical factors are electrochemical nature (temperature, electrochemical potential, aggressive ion concentration)and the influence of stresses on the passive film
° Crack propagation
Metal dissolution followed by repassivation
Critical factors is the ratio of the tensile deformation and the repassivation rate at the crack tip
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SCC: influencing parameters1) Materials
° Susceptibility can be controlled
inadequate heat treatment resulting in sensitization (chrome depletion at grain boundaries) for example is extremely detrimental
° Alloying of nickel is beneficial(around 20 %)
Example:
CrNi wires in boiling MgCl2 (154°C)
Austenitic structure is moreresistant then ferritic
Tim
e to
failu
re (
h)Weight % Nickel 16
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SCC: influencing parameters II° Molybdenum decrease the SCC susceptibility in the critical Ni concentration domain mainly in increasing the critical KISCCthreshold
Example:
CrNiMo Steel
With 15.5 – 21% Ni22 %Cr
In aerated NaCl solution (105°C) Weight % molybdenum
Crit
ical
KIS
CC
(MN
/ m
1.5 )
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SCC: influencing parameters III° TemperatureAt room temperature, SCC is usually not observed in chloride containing environment (seawater or similar environment )
Be careful with acidic environments (crevice condition)where SCC is occurring also at room temperature
° Aggressive ions
CrNi SteelsChloride anions
Cl- concentration in aqueous electrolyte (ppm)
Tem
pera
ture
(°C
)SCC (initiated at pits)
No SCC after 10’000 hours exposure
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Measures to avoid SCC
° Avoid stresses on the material
- Internal stresses can be reduced with adequate heat treatment
- External stresses are often decreased just by design consideration (avoid having applied stresses on welds !)
° Remove aggressive environment (special care have to be taken to crevice conditions)
To avoid right design
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Corrosion - Fatigue: cyclic loading
° Special case of Stress Corrosion Cracking (SCC)
° Applied stress is not constantbut experiences cyclic variations
aggravated SCC attack
° Much more materials and environments are concerned
Transgranular crack propagation
Metallographic
cross section
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Corrosion – Fatigue: mechanisms
° Factors influencing corrosion-fatigue processes are similar toSCC
- The cyclic loading caninduce constantdepassivation
- Interaction between glidingplanes and electrolyte playsa key role
- At the induced micro notches,additional gliding and acceleratedcorrosion is induced
Gliding plane
Corrosion susceptible area
Passive layer
Initiation sites for corrosion fatigue
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Wöhler curves in the case of corrosion - fatigue° Corrosion rate is dependent on the cycle number and amplitude
This has to be taken intoaccount for fatigue-corrosion
The Wöhler curves display the failure time in relation tocycle number and stress amplitude
Important to note:surface defects (notches) plays a tremendous role in the life of a componentexposed to fatigue condition
Cycle number
Stre
ss a
mpl
itude
1. smooth surfaceAir, RT2. notched surfaceAir, RT3. smooth surfaceConc. NaCl4. notched surfaceConc. NaCl
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Fatigue: experimental setups° The specimens used were CT-specimens (CT: compact tension)° The geometry of the specimen is given as relative dimensions of the width W
° The specimen made from 7075-T651 had a width of 60 mm and a thickness of 10 mm ( with W = 40 mm and B = 3.63mm). The initial notch depth a0 was 17 mm or 32 mm.
° The specimen were loaded by a pair of pin loads at x=0, y=0, z=±0.225W in the z direction. The loading was a sinusoidal constant amplitude history with a frequency of 83 or 54 Hz.
° The CT-specimen was equipped with a clip gauge at the mouth of the notch. The crack length was monitored optically by two traveling microscopes, fixed to the test bed and allowing to measure both surface crack lengths, on the front and on the back face. 23
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a crack length, crack depth, crack sizea0 original crack size, initial crack length
Keff effective stress intensity factor range
da/dN fatigue-crack-growth rate measured in constant amplitude tests
R load ratio := Pmin/Pmax or Kmin/Kmax
Pmax maximum load on the C(T) specimenPmin minimum load on the C(T) specimen
Kmax maximum stress-intensity factorKmin minimum stress-intensity factor
Some important parameters and relations
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• The T651 temper is a solution heat-treated, quenched, 1.5 to 3% controlled stretched, and artificially aged condition with a maximum static strength.
• Second phase particles in these alloys are usually categorized into three groups:- Large (approx. 1 to 30 m) intermetallic particles formed during solidification by combination of impurities (Fe, Si) and solute elements: Al12(Fe,Mn)3 Si and Al7Cu2Fe- Smaller (approx. 0.3 m) dispersoid particles formed by solid state precipitation of Cr and Mn at temperatures above 425°C: Al20Cu2Mn3
- Fine (0.5 nm - 10 nm) precipitates, containing solute elements. Formed during quenching or aging: Al2CuMg
Measurementsin weight %
Specificationin weight-%
Remarks
Element A B averageSi Silicon 0.06 0.06 0.06 0.40Fe Iron 0.30 0.30 0.30 0.50Cu Copper 1.70 1.70 1.70 1.2 - 2.0Mn Manganese 0.03 0.03 0.03 0.30Mg Magnesium 3.10 3.10 3.10 2.1 - 2.9 *Cr Chromium 0.18 0.18 0.18 0.18 - 0.28Zn Zinc 5.60 5.60 5.60 5.1 - 6.1Ti Titanium 0.03 0.03 0.03 0.20Ni Nickel <0.01 <0.01 <0.01 0.05Others, each <0.01 <0.01 <0.01 0.05Others, total 0.15Al Aluminum Balance Balance Balance Balance
Used aluminum alloy: 7075
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- Oxide film growth will occur very rapidly (formation of the 5-6 nm passive film in a few millisecond in air) in air with a slight humidity related acceleration
- Even in Nitrogen atmosphere, a nm-thick oxide will form in millisecond- In fine vacuum (high vacuum), the formation is then obviously hindered and
only monolayers of oxygen will be chemisorbed on the surface
Al oxidation process as function of atmosphere
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7075-T651: crack propagation in vacuum
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crack growth rate in 7075-T651 in fine vacuum
0.001
0.010
0.100
1.000
10.000
100.000
1'000.000
10'000.000
1 10 100Delta K eff [MPam^0.5]
da/d
N [n
m/c
ycl
SCVA, R = 0.1, Delta K upSCVF, R = 0.1, Delta K upSCVA, R = 0.1, Delta K dwSCVB, R = 0.1, Delta K dwSCVB, R = 0.3, Delta K upSCVD, R = 0.3, Delta K upSCVB, R = 0.3, Delta K dwSCVC, R = 0.5, Delta K dwSCVC, R = 0.5, Delta K dwSCVC, R = 0.5, Delta K upSCVC, R = 0.5, Delta K upSCVE, R = 0.5, Delta K dwSCVE, R = 0.5, Delta K upmodel with slip
The experimentally measured results (with the fitted parameters) for 7075-T651 are shown below with the propagation rates (da/dN) and the onset ofunder critical crack growth
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7075-T651: crack propagation in nitrogen
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crack growth rate in 7075-T651 in purified nitrogen
0.001
0.010
0.100
1.000
10.000
100.000
1'000.000
10'000.000
1 10 100Delta K eff [MPam^0.5]
da/d
N [n
m/c
ycl
SCNC, R=0.1, f = 54 Hz
SCND, R=0.3, f = 54 Hz
SCNE, R=0.3, f = 83 Hz
SCNF, R=0.5, f = 54 Hz
SCNG, R=0.5, f = 54 Hz
SCNF, R=0.5, f = 83 Hz
model with d_ox
- In nitrogen, the critical stress intensity Keff to initiate fatigue crack growth is decreased and the propagation rates in the undercritical domain is also faster
- There is clearly a material-environment combination in this process
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7075-T651: crack propagation in air
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crack growth rate in 7075-T651 in humid air
0.001
0.010
0.100
1.000
10.000
100.000
1'000.000
10'000.000
1 10 100Delta K eff [MPam^0.5]
da/d
N [n
m/c
ycl
S0LA, R=0.1, Delta K upSCVA, R=0.15, Delta K dwSCLB, R=0.3, Delta K upSCLB, R=0.3, DeltaK dwSCLC, R=0.5, Delta K upSCLC, R=0.5, Delta K dwnew model with d_oxnew model without d_ox
- In air, the critical stress intensity Keff to initiate fatigue crack growth is similar to nitrogen but the propagation rate is then slightly higher
- The environmental component is related to the presence and thickness of passive film that is constantly broken at every cycle and reforms
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Summary: role of passive oxide film on fatigue
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Crack Growth in 7075-T651 in Different Environment
0.001
0.010
0.100
1.000
10.000
100.000
1'000.000
10'000.000
1 10 100Delta K_eff [MPam^0.5]
da/d
N [n
m/c
ycle Vacuum
Purified Nitrogen
Laboratory Air
- The fatigue crack propagation rate increase as function of stronger oxidizing conditions can be seen by overlapping the curves measured in different environments
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Passivation process and stress distribution
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• The empirically found crack growth rates are understood as the superposition of these mechanisms:
- In vacuum near threshold a partly non-reversible cyclic slip mechanism results in crack propagation. For higher loads after this cyclic slip mechanism the crack tip begins to blunt and after each fatigue cycle a fatigue striation is left on the crack surface
- In air and nitrogen, near threshold, the crack growth increment is given by the oxide film thickness build-up after each half cycle. For higher loads the crack tip is blunted and fatigue striations occur o the crack surface
- The main outcome of these experiments was to proof the hypothesis that the crack growth increment near threshold in air and nitrogen is the oxide film thickness. Corrosive liquids would result in further acceleration of the processes
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Short summary: Al Fatigue-corrosion
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How to avoid Corrosion Fatigue° Same measures than for Stress Corrosion Cracking
Further indicated is:
° Decrease of the stress amplitude under a critical value (look at the Wöhler’s curve parameters)
° Try to have a smooth surface (avoid notches or localized corrosion attack) in the areas where stress is expected
° Try to avoid resonance frequencies of the structure (design consideration)
° Improve the passivation of the surface. Brittle coating do not help, organic coating is better in this case 33