ballististen materiaalien mallinnusavusteinen kehittäminen
TRANSCRIPT
TEKNOLOGIAN TUTKIMUSKESKUS VTT OY
Ballististen Materiaalien
mallinnusavusteinen
kehittäminen - BalMa
MATINE Tutkimusseminaari 17.11.2016
Tomi Lindroos, Matti Lindroos, Anssi
Laukkanen
211.11.2016 2
Projektin perustiedot
Ballististen Materiaalien mallinnusavusteinen kehittäminen – BalMa,
projektikoodi 2500M-0047
Projekti on suunniteltu kaksivuotiseksi alkaen 1.1.2015 ja päättyen
31.11.2016.
Rahoitus 2016: MATINE 51 500 €, VTT 16 662 €, 68 162 €
Ohjausryhmä:
Tomi Lindroos, VTT
Paavo Raerinne, PVTUTKL
Jukka Kemppainen, Exote Oy
Pekka Lintula, Nammo Lapua Oy
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Tausta, lähtökohdat ja kytkennät aiempiin tutkimuksiin
Suojauskyvyn kasvattaminen ja samanaikainen painon alentaminen edellyttävät yhä
kehittyneempien ja suorituskykyisempien materiaalien ja materiaaliyhdistelmien käyttöä
Hyödyntämällä uusia, kehittyneitä mallinnus- ja simulointityökaluja on mahdollista
ymmärtää paremmin monimutkaistenkin materiaalien ja rakenteiden käyttäytymistä,
nopeuttaa kehitysprosessia ja päästä lähemmäs optimaalista ratkaisua.
Perinteisesti mallinnusaktiviteetit ovat rajoittuneet rakenteiden ja ballistisen iskun
karkeahkoon FE mallinnukseen. Makroskooppisilla rakennemalleilla ei kuitenkaan
pystytä kuvaamaan kaikkia vuorovaikutuksia, joista tutkittavan komponentin
suorituskyky muodostuu.
Monitasomallinnuksen (multi-scale modelling) avulla malliin voidaan luoda
yksityiskohtaisempia piirteitä aina elektroni- ja atomitasolle asti riippuen kuvattavan
ilmiön mittakaavasta.
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TAVOITTEET
Projektin kokonaistavoitteena on kehittää työkaluja, jotka mahdollistavat entistä
tehokkaampien (suorituskyky = suojaustaso + neliöpaino) suojausmateriaalien
ja rakenteiden kehittämisen nopeammin ja kustannustehokkaammin.
Projektissa luodaan perusteet materiaalien ja rakenteiden
mallinnusavusteiselle suunnittelulle ja lisätään tätä kautta ymmärtämystä
materiaalien käyttäytymisestä ballistisessa iskussa.
TEHTÄVÄT Selvittää monitasomallinnuksen tämän hetkiset mahdollisuudet ja rajoitukset
entistä tehokkaampien ballististen suojamateriaalien kehittämiseksi. (task 1)
Kehittää mikrorakennetason malleja, jotka mahdollistavat iskuenergian
jakautumisen visualisoinnin mikrorakenteessa ja tätä kautta ymmärtää miten
mikrorakennetta tulisi muokata suorituskyvyn kasvattamiseksi. (task 2)
Suorittaa kokeellista testausta (mekaaniset ominaisuudet, ampumakokeet)
mallien verifioimiseksi ja mallinnuksen materiaaliparametrien määrittämiseksi.
(task 3)
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Multi-scale modelling
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Material and Structure
Test structure for ballistic testing
against 7.62-51 FFV AP (M993) and
cross-section of structure after
impact
Microstructure informed modeling
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Deformation at microscale
Computational microstructure
Loading axis
(compression)
strain rate�ε = 𝟏𝟏 𝟏
Simplified compression of the microstructure
to reveal local stress-strain behavior and its
relationship to failure
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Deformation at microscale Uniaxial deformation in compression, strain rate 𝟏𝟏 𝟏
Equivalent stress Strain Carbide damage
At damage
initiation
Stress relief after
material damage
(material stiffness
degraded)
Strain
localization in
matrix and
failed carbides
Damage network
inside carbides
(damage also prevails
in the matrix along the
shear bands)
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Understanding the failure process
Damage
(local scale facture process)
Displacement field
(macroscopic understanding of the fracture)
Fragments
Fractured material
cannot withstand
tensile loads, but
resists compression
Degradiation of
strength chosen
for TiC
Strength of the matrix (Ni) rate-dependent
Strength degraded with JC-damage
because of more ductile nature of Ni
Tensile cut-off
JH-2
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Deformation at microscale (visualization)
Peak strength
Damage initiates
throughout the
microstructure
Damage
developed
in RVE Damaged strength
(compression)
Intact material with
very little damage
Strain rate 20 000 1/s -- Homogenized curve (macroscopic behavior)
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Strain, stress, carbide and matrix damage evolutions
Strain Carbide damage
Eqv. stress Matrix damage
Compression
axis
Shear bands
Damage
accumulation
in the matrix
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Upscaling the microstructure RVE
Larger scale allows to investigate the failure propagation in the
microstructure closer to the macroscopic scale
The transition from microscale (um) to mm, or even larger is
easier to establish when the microstructure is in mm-scale
256 µm
~17
0 µ
m
SEM-based model (green = TiC, light = Ni) Larger representative volume element (RVE)
2.048 mm
1.3
28m
m
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Deformation and failure at larger scaleStress Strain
Carbide damage Strain (Failed material removed)2.048 mm
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Deformation and failure at larger scaleStress
Strain
Damage
At damage initiation Evolution Degraded/Failed
Stress
concentrations
assisting cracking
Strain localization
to failed regions
Secondary crack networks develop
Strength of the material mostly lost
(stress levels are decreased)
𝟏 ≤ 𝟏 ≤ 𝟏
2.048 mm
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Material behavior at different strain rates ( Current material structure)
• Material strength increases as a function of strain rate
• Damage develops earlier due to high shock loading, but strain rate dependent
strength compensates damage process (ductility slightly increases)
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Deformation and failure at larger scaleMicroscale observations (direct SEM microstructure)
• Cracked carbides as a one source of failure,
but it absorbs energy in the process• Adibatic heating of the matrix has relatively little effect due to
rapid failure of the carbide structure at high loads
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The sources of failure during impact loading
(high strain rate conditions) – local behavior
Heavy fracture and
(slip line) network
in a carbideCrack propagation from
carbide-to-carbide’Closed’ loop
fracture in a carbide
Increasing
deformation
Fractured
material
Initiation of
local failure
• Carbides develop individual and joining
crack networks
• Strain concentrations localize damage
also in matrix (and increases its
temperature by ~100-200 C occasionally)
• Interface mistmatch between carbides
and matrix accelerates fracture initiation
(Blue=carbide)
(Light=matrix)
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Macroscopic strain ~0.013• Rate dependent model and coupling with damage, features:
• Strength is increased by viscous drag (towards shock conditions)
• The shock conditions at 100000 1/s are very different to 1000 1/s
• At lower strain rates, the local fractures develops earlier to macroscopic failure
The sources of failure during impact loading
(high strain rate conditions) – local behavior
Carbide
damage
Localized
strain
Fully developed to macroscopic fracture(s) Partially developed to macroscopic fracture(s) Early local fracture development
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Microstructure design possibilities
Microstructure A Carbide content ~0.88 Carbide content ~0.71Microstructure B
• Lowering carbide content provides slightly better local ductility, however,
strength decreased by 20%
• The capability of the microstructure to absorb (impact) energy decreases
• Optimization of the microstructure in respect to design variables is possible
Microstructure BMicrostructure A
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Visualization of impact event (task 2)
Stresses at shock front Fracture along carbide (blue)
Strain localization,
including fracture
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Stresses at shock front Fracture along carbide (blue)
Fracture process:• Material is crushed close to the
contact interface
• Circumferential crack pattern
develops, while its intensity
depends on the local strengths
• Shear develops also in the binder
phase, but carbide damage
prevails the process due to stress
concentrations generated by cracks
• Structure resists deformation under
compression relatively well
(excluding the crushed zone)
Material crushing zone
Energy absorption:• High strength carbides
temporarily store strain energy
• Cracking process consumes a
reasonable amount of energy
• Matrix is able store less strain
energy, but it retains its ability
withstand further deformation
until ductile failure
Multi-scale: From microstructure to
macroscopic material performance
Resist or
penetrate?
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Projectile deacceleration during the impact TiC-Ni
Damage of projectile and steelDamage of TiC-Ni
Stress
• TiC-Ni = 7 mm
• Steel = 4 mm
TiC-Ni
Steel
WC-Co
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Projectile deacceleration during the impact
TiC-Ni
• Nominal projectile velocity decreased by ~50
% before reaching the steel section
Energy loss = ~90%
• But, projectile degrades (fractures) during the
impact effectively when interacting with TiC-Ni
Only 10% of the original kinetic energy of the
projectile is absorbed by the steel
Residual
velocity
~50 %
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Performance at different thicknesses
Penetration
Fully blocked
Total
Thickness = 7mm
(Steel t = 4 mm)
Total
Thickness = 15mm
Total
Thickness = 11mm
Small energy
penetration possible
Residual energy
with 9mm, only ~5%
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Possibilities with multi-scale modeling
Microstructure informed modeling can be used to test alternative microstructures and establish a
relationship between structure and performance (MATERIAL DESIGN ASPECT)
Failure models acting at microstructure scale are able to produce the main damage and failure
properties of TiC-Ni material(s), such as carbide fracture, binder phase shear localization.
Distribution of (impact) energy introduced to the material by ballistic impacts can be visualized only by
microstructure based models, because of the different local behavior of phases (and interfaces).
Macroscopic impact models are able to provide a reasonable design tool for material thickness for
armouring application (COMPONENT DESIGN ASPECT)
Preliminary experiments verify that the numerical models can produce realistic material behavior and
assess the stopping-penetration ability of the composite structures
The experimental verification tests are required to adjust the final model parameters prior to wider use
of the simulation predictions
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High Speed Camera tests
Example
https://youtu.be/a5VMIvY2Uh8
Phantom v2511• 1280 x 800 resolution
• 280ns minimum exposure
with the FAST option
• 1 µs minimum exposure
standard
• Up to 677,000 fps standard or
1,000,000 fps with the FAST
• High-speed camera tests of ballistic impact 23.11.2016
Verification data for models
• Selected videos will be publishes ww.vtt.fi/powder
TEKNOLOGIASTA TULOSTA
www.vtt.fi/powder
www.vttresearch.com/propertune