superhard coatings for advanced vehicle systems applications
DESCRIPTION
coatingsTRANSCRIPT
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SUPERHARD COATINGS FOR ADVANCED
VEHICLE SYSTEMS APPLICATIONS
Ali Erdemir and Dileep Singh
Tribology Section
Energy Technology Division
April 19, 2006
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Rationale and Goals
Injectors
Design and develop new
coatings to reducefriction
Demonstrate their
energy saving and wear
reducing benefits
Scale-up and transfer
optimized technology to
industry
Powertrain components
Piston pins
• Nearly 10% of fuel energy
is consumed by friction in
engines (which amounts to
about one million barrels
of oil/day)
Gears
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Approach
Design superhard coating composition for intended
applications
Develop a reliable deposition protocol for the
production of superhard coatings
Characterize structure and property
Demonstrate performance
Analyze test data and examine sliding surfaces
Determine friction and wear mechanisms
Integrate superhard coatings with laser texturing
Prepare reports
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Industrial Collaborations
Burgess-Norton performing tests in fired engines
(interested in licensing the technology)
Eaton (a CRADA is underway)
Caterpillar
BorgWarner
Westport
Federal Mogul
Coating Systems Manufacturers (HauzerTechnoCoating, Ion Bond, CemeCon).
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Technical Accomplishments
Successfully produced superhard coatings in a production-
scale sputter ion plating system
Demonstrated their superhard and low-friction nature
Verified their extreme resistance to scuffing and wear
Demonstrated their compatibility with and superior
performance in EGR-contaminated oils Initiated surface analytical studies to understand lubrication
mechanisms
First measurements of residual stresses in thin coatingsmade using X-rays at the Advanced Photon Source
Collaborated with an outside company to demonstrate its
performance in piston pin applications
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Upper Surface
Lower Surface
Lubricant
BoundaryLayersAsperity Contacts
Mechanical
Seals
Boundary Lubrication
Mixed
LubricationFull Film
Lubrication
Viscosity * Speed/Load
F r i c t i o n
C o e f f i c i e n t
? ?
Schematic Illustration of Boundary Lubrication
Big Question ?:
Can we design coating systems thatare not only superhard (for wear
control) but also low-friction (forfriction control) under severe boundarylubricated sliding conditions?
In these components friction
and wear result mainly from
direct metal-to-metal contacts
which often occur under highpressures, low sliding
velocity and in low viscosityoils.
Major Causes of Friction in Lubricated Contacts
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Conventional Hard Coatings
Design and Synthesis of a Superhard,Nanocomposite Coating
Superhard nano-composite
coating
0
0.02
0.04
0.06
0.08
0.1
0.12
0 5 10 15
KTF 210
Depth
Load (mN)
E/(1-v2) = 401.23 +/- 17.18 (GPa)
Hardness = 67015 +/- 4683 (N/mm2)
Wp = 0.14 nJ (%15)
We = 0.79 nJ (%85)
Substrate
Cross-Section electron
Microscopy image of
New, nano-structured
Coating
Nano
Grains
Optimization of depositionprocess parameters is keyto the development of these
novel coatings providingsuperhardness, toughnessand exceptional friction andwear properties.
Superhard:
67GPa
Patent Pending
Two more invention disclosures filed
High-mag image
Sputter ion plating system
Hardness Behavior
SEM Cross-section Images
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0
0.05
0.1
0.15
0.2
0 2 104
4 104
6 104
8 104
1 105
Time (s)
Friction and Wear Performance UnderBoundary Lubrication Regime
Wear track
No noticeable wear
1.6X
Steel Pin/Steel Disk
Steel Pin/Superhard coated steel
Load: 20N, Velocity: 10 rpm,
10W30 Formulated Synthetic Oil
Boundary Lubrication
Mixed
LubricationFull Film
Lubrication
Viscosity * Speed/Load
F r i c t i o n
C o e
f f i c i e n t
No measurable wear
F
r i c t i o n
C o e f f
i c i e n t
More than 75% reduction in friction
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0
200
400
600
800
1000
0 500 1000 1500 2000 2500
Time (Sec)
Normal Load
Steel / Steel
SHC / Steel
SHC / SHC
SHC - Super Hard Coating
Effect of SHC on scuffing resistance of steel surfaces
Test Configuration : Block on Ring ConfigurationLubricant - PAO 10 basestock
Speed - 750 rpmTemperature - Ambient RT
L o a d
( N )
BlockOn
Ring
Could not be scuffed.
Test was terminateddue to overheating
of oil that produced
heavy smoke.
Resistance of Superhard Coatings to Scuffing
Base oil
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0.00
0.05
0.10
0.15
0.20
0 480 960 1440 1920 2400 2880 3360 3840 4320
Time (s.)
F r i c t i o n C o
e f f i c i e n t
0
200
400
600
800
1000
1200
1400
1600
1800
2000
Friction CoefficientRing Temp.Load
L o
a d ( N )
R i n g T e m p * 1 0 - 3
Mobil 1 10W30
Resistance of Superhard Coatings to Scuffing Cont’d
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Surface Analytical Studies
(Preliminary TOF-SIMS Results)
SHC coated ring vs.
SHC coated blockIn Mobil 1 10W-30
Total Ion PO2
FeS SBlue FeS
Red S
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Tests were run at high
speed (hence high
temperature) for
100 hours in a V8engine.
Field Test Results:Superhard Coatings on Piston Pins
Control pin
Superhard-coated
pin
We had four coated pins in one bank of a V8 engine.
The other 4 cylinders only had manganese phosphate
coated pins (control pins).
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Summary
A family of superhard coatings was successfully
developed
Their superior friction, wear, and scuffing
performance was demonstrated
Their resistance to EGR-contaminated diesel
engine oils was confirmed
Fundamental surface analytical studies and x-ray
stress measurements were initiated
Excellent results were obtained from limited field
tests and more work is underway
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Future Plans
Perform bench-top life and field tests
Determine the effects of oil viscosity on friction and wear
Perform more tests in EGR contaminated oils; explorecorrosion/erosion related degradation
Elucidate lubrication mechanism(s) using surfacesensitive techniques (UIUC, ANL-APS).
Elucidate the extent of internal stresses and correlatefindings with performance and durability.
Integrate superhard coatings with laser surface texturing
to further enhance performance/durability Increase collaboration with industry, establish programs,
transfer technology (potential customers; Caterpillar,
Eaton, Federal Mogul, Burgess-Norton, Ford).
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Rationale: Residual Stress Measurements inThin Coatings
Reduction of friction and wear in drive trains and
engine components, and consequently, reduction in
parasitic energy losses can result in >6% fuel savings
Performance of low friction and wear coatings is
strongly dependent on the residual stress profiles
Currently, no technique is available to profile residual
stresses in thin coatings
This is a new program in FY 06
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Objectives
Develop and refine high-energy X-ray technique(s) at the
Advanced Photon Source (APS) to measure residual
strains/stresses for super-hard, nanocrystalline low-friction
coatings as a function of coating thicknesses
Correlate residual stresses in coatings systems to processing
technique and variables, material properties, and adhesionenergies
Compare experimentally measured residual stresses to calculated
stresses from finite element modeling
Develop an optimized coating processing protocol for a specific
coating system and applications
Diff ti l A t X R Mi
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Differential Aperture X-Ray Microscopy(DAXM)
Residual strains measured by comparing
shift in diffraction spot positions from grains
at specific coating depth with those of
unconstrained grains
X-ray absorbing wire allows depth profiling
Depth resolution of ~0.5 µm is achievable
CCD
X-ray beam
Wire
Substrate
Film
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Cross-Section Depth Resolved X-RayMicroscopy (CDRXM)
Samples fractured to expose cross-section
Depth of X-ray penetration dependent on
energy (~ 5-10 µm)
Sample moved in steps of 0.25 µm to scan
surface of the film to substrate
Invention report filed
CCD
X-ray beam
FilmSubstrate
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Coating Systems Investigated
SHC on Si SubstrateMo on Si Substrate
Samples fabricated by O. Eryilmaz (ANL)
Sputter deposition
200-300°C deposition temperature
Ar pressure and sputtering bias
Coating thicknesses ~ 3-5 µm
Residual strains measured on as-fabricated and annealed (500
C for 1 h) samples
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Diffraction Data from CDRXM
R id l t i d b
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Residual strains measured byCDRXM: Mo coating
x
z
y
Si
Mo
Mo-large
grains
bond coat
SiCTE = 2.6 ppm/K
MoCTE = 4.8 ppm/KX-Rays
Residual strains measured by CDRXM:
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Residual strains measured by CDRXM:SHC on Si substrate
x
z
y
Si
SHC
Mo-large
grains
bond coat
SiCTE = 2.6 ppm/K
SHCCTE = ? X-Rays
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Summary
For the first time, depth resolved residual strains in thin coating
systems has been measured using CDRXM technique
CDRXM technique, with sub-micron resolution, allows strainmeasurements even in the bond coat
In-plane strains for Mo and SHC coatings are tensile and for the
Mo bond coat they are compressive Magnitude of in-plane strains in SHC coating is significantly higher
than in Mo coating and decrease from surface to the interface
Annealing significantly decreases the in-plane strains for SHC,however, for Mo films, decrease in in-plane strains is relatively
smaller
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Future Plans
Compare residual strain measurements obtained from DAXM and
CDRXM techniques (FY 06)
Characterize coating adhesion properties using mechanical testssuch as nano-indentation (FY 07)
Compare strain measurements with FEM (FY 07)
Measure residual strains/stresses in thin coatings fabricated undervarious processing conditions (FY 07)
Correlate coating performance & adhesion with residual stresses
& processing (FY 08) Develop a protocol for developing coatings with optimal properties
(FY 08)
Establish industrial collaborations to transfer the technology
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Contributors
O. Eryilmaz
G. Chen
B. Larson (ORNL)
J. L. Routbort
Weijin Liu