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ICG – EFONGA Spring School Montpellier 4-5 May 2009 1
Chemical & Physical Processes
in Glass Melting
Quality of glass
melting process
Ruud Beerkens
TNO Glass Group
Eindhoven, The Netherlands
Glass Service
Buchmayer
ICG – EFONGA Spring School Montpellier 4-5 May 2009 2
Contents
• Overview of processes essential for glass melting
• Tools of analysis of industrial glass melting
• Melting-in of Raw materials
• Kinetics of Sand Dissolution
• Removal of Gas bubbles & Dissolved gases
• Evaporation processes
• Homogenisation
ICG – EFONGA Spring School Montpellier 4-5 May 2009 3
ICG – EFONGA Spring School Montpellier 4-5 May 2009 4
foaming
water infiltration
evaporation:
NaOH, KOH,
HBO2,
PbO, NaCl,
HF, SO2 etc.
refractory corrosion
refractory corrosion
fining and redox
deposition and
dust formation
emissions: Na2SO4, Na2B4O7 and PbO dust
HCl, HF, SO2, SO3 , SeO2, HBO2, H3BO3 etc.
NOx and
heat transfer
flue gas
chemistry
1. Overview
Chemistry & Physics
of Glass
Melting Processes
melting kinetics
ICG – EFONGA Spring School Montpellier 4-5 May 2009 5
Raw materials mixed
Furnace
Or
Crucible
Homogeneous molten glass
Melting-in of batch – chemical reactions/endothermic effects
Sand* grain dissolution
Removal of bubbles/gases
Dissolution of seed (fine bubbles) residue
Homogenisation
- Diffusion (slow)
- Velocity gradients – stretching of inhomogeneities
Side-effects
• Evaporation from melt
• Refractory corrosion
• Combustion & heating
• Emissions from evaporation & combustion
ICG – EFONGA Spring School Montpellier 4-5 May 2009 6
Parameters for processes in melting
Important parameters:
• Heat transfer �Temperature � viscosity, surface tension,
chemical activity, reaction kinetics, gas evolution..
• Flow characteristics – convection in melt, stirring
• Residence time: time-temperature history
• Exposure of melt to (reactive) atmosphere and refractory
lining
How to assess:
Temperatures and flows in glass melt ?
ICG – EFONGA Spring School Montpellier 4-5 May 2009 7
• Discretize total volume of furnace in small volume cells (> 1 million)
cells LxBxH: (1-10) x (1-10) x (1-10) cm
– GRID / mesh
• Input data process: pull, batch composition, fuel distribution, air
number
• Input furnace:
– Design
– Wall construction, including insulation
• Input glass: viscosity, heat conductivity, density, thermal
expansion, electric conductivity, solubility sand, solubility gases,…
• For each volume cell in tank & combustion chamber
– Energy conservation
– Momentum conservation
– Mass conservation (continuity) for melt and each chemical element
– Respect electro-neutrality
2. Tools: CFD Simulation Models Glass Furnaces
ICG – EFONGA Spring School Montpellier 4-5 May 2009 8
CFD Simulation Models
example: local conservation of energy
Energy equation, conservation law for
energy in each volume element
increase sensible convection heat conduction local
heat of heat boosting or
cooling
( ) ( ) ( ) qT Tct
Tc+λ+ρ−=
∂
ρ∂ grad divv div p
p r
ICG – EFONGA Spring School Montpellier 4-5 May 2009 9
Results of CFD simulation models
• Temperatures at all possible positions
– Combustion space
– Glass melt
– Refractory
• Glass melt and Combustion gas velocities
• Trajectories (particle tracing) in tank
– Thousands of different paths can be identified from charging end to throat or
spout
• Redox and dissolved gases
– Redox state of melt at each position (pO2 or Fe2+/Fe3+)
• Residence time distribution
– Minimum residence time is of importance for melting process
• Glass melt quality indices per trajectory
– Trajectory with minimum melting or fining index is decisive for glass
ICG – EFONGA Spring School Montpellier 4-5 May 2009 10
Application of CFD models
• For furnace design (lowest energy, highest glass quality)
– Optimum depth of tank
– Position bubblers or dam or burners
– Size and design of throat
– Design combustion chamber (LowNOx, less evaporation)
• For optimum process settings
– Optimum fuel-boosting ratio
– Temperature profile (energy distribution)
– Bubbling rate
– Creation of distinct spring zone to avoid short cut
• Time-transient (time dependent) for colour or pull change
– Optimize colour change process: reduce transition time
• Time-transient for process control (rMPC)
– Sensors give model continuous new information: model tracking
– Model continuously gives recommendation for input parameter changes to
follow optimum process path (low energy, high glass quality, constant T)
ICG – EFONGA Spring School Montpellier 4-5 May 2009 11
Geometry & Grid
for computational fluid dynamics (CFD)
analysis of glass furnace
Deep Refiner
Port Necks
Batch Boosting electrodes
tankBurner port
crown
ICG – EFONGA Spring School Montpellier 4-5 May 2009 12
Example result CFD computation
Temperature contours
ICG – EFONGA Spring School Montpellier 4-5 May 2009 13
NOxEnd-port fired furnace horizontal cross section at level of burners
Base case
4 inch higher crown
ICG – EFONGA Spring School Montpellier 4-5 May 2009 14
NOxEnd-port fired furnace vertical cross section at 25 % from furnace length from port
Base case
4 inch
higher crown
NOx scaling in mole fraction
Lower NOx-concentration in exit
Burner port Exit port (flue gas)
ICG – EFONGA Spring School Montpellier 4-5 May 2009 15
Glass melt path with lowest ‘temperature‘ index
Temperature course of glass (melt) in typical float glass furnace with
minium temperature index
0
200
400
600
800
1000
1200
1400
1600
1800
0 2 4 6 8 10 12 14
Time in hours
Temperature in oC
dtT
indexeTemperaturcanal
doghouse
ipath ∫ η=
ICG – EFONGA Spring School Montpellier 4-5 May 2009 16
Sensors (short overview)• Combustion gases
• gas composition: • laser optics
• electrochemical sensors (oxygen)
• Glass melt
• chemical composition
• LIBS = laser induced breakdown spectroscopy
• redox / colour parameters• Potentiometry
• Voltammetry
t/c
Type B
(mV)
Alumina rod
Pt measuring
electrode
Ni/NiO-
reference mix
Zirconia cell
emf
(mV)
Pt / Ni-NiO // ZrO2 // pO2 (glass) / Pt
O)(ref.Ni/NipO
(glass)pOln
nF
RTEMF
2
2⋅=
ICG – EFONGA Spring School Montpellier 4-5 May 2009 17
3. Melting-in of batch
• In glass furnaces (industrial)
– Kinetics determined by heat transfer through
batch blanket
• In small crucibles:
– Kinetics determined by contact between
different batch constituents and temperature
ICG – EFONGA Spring School Montpellier 4-5 May 2009 18
Day hopper
Spring zone& primary fining
Return flow from working end
Batch melting• 40-60 minutes• 80-90 % of net heat flux
Zone for sand grain dissolution
Hot spot &evaporation
Return flowfor batch heating
Generation blisters from refractory
RefiningBubble absorption
Conditioning of meltThermal homogeneity
ICG – EFONGA Spring School Montpellier 4-5 May 2009 19
Scheme of melting process of batch blanket, charging velocity vg(m/s)
heat transfer
gas release
combustion space
reaction zone
thick-
ness normal batch
temperature
profile
reaction zone
glass melt layer
figure 1b
glassmelt
flowheat
transferred
figure 1c
glass
levelZipfel
ICG – EFONGA Spring School Montpellier 4-5 May 2009 20
Detailed re-presentation of the batch melting process
in glass furnace
batch
b. top of batch blanketc. bottom side of batch
blanket
glass melt 1400 oC
meltingreactionsmelting
reactions
Dissolutionsand grains sand
grains
carbonates(soda/lime)
dissolution sandgrains
sandgrains
gas
gas
melts
Layerglassmelt
loose batch
1500 oC
ICG – EFONGA Spring School Montpellier 4-5 May 2009 21
Example:
Melting reactions of soda lime (dolomite) silica batch
• De-hydratation (100 oC physical bonded water & > 100 oC hydrates) – Important for energy consumption: water evaporation is energy intensive
• Solid state reactions, formation of silicates, e.g.:
Carbonate route < 900 oC at fast heating rate
Na2CO3 + CaCO3 � Na2Ca(CO3)2 (melts at ±820 oC) (550-850 oC)
Na2Ca(CO3)2 +2SiO2 � Na2SiO3/CaSiO3 + 2CO2↑ reaction enhances > 820 oC
Na2CO3 + 2SiO2 � Na2SiO3 + CO2↑ (790-850 oC)
• Formation of primary melt phases (alkali rich carbonates), e.g.:
Tm Na2CO3 = 850 oC
Tm Na2Ca(CO3)2 = 820 oC
Tm K2CO3 = 890 oC
High amount of
heat required
ICG – EFONGA Spring School Montpellier 4-5 May 2009 22
• Decomposition reactions of (Ca- and Mg-) carbonates:
• Dissolution reactions of SiO2, e.g. (coarse limestone)
Melting reactions of soda lime silica batchlimited kinetics may shift some reactions to higher temperatures
heat required
CaCO3 + heat � CaO + CO2↑ (910 oC at pressure 1 bar)
MgCO3 + heat � MgO + CO2↑ (540 oC at pressure of 1 bar)
MgCO3·CaCO3 + heat � MgO + CaCO3 + CO2↑ (650 oC, 1 bar)
MgO still present up to 1150 oC.
Reactive calcination: Na2CO3 + 2SiO2 � Na2O·2SiO2 + CO2↑ T > 790 oC
� forms with SiO2 an eutectic melt
Or at further heating � fast Na2O·SiO2 formation (850 oC) –
limestone decomposes and:
2CaO + (SiO2 + Na2O·2SiO2 )eutectic melt � Na2O·2CaO·3SiO2 (> 900 oC)
Silicate route: Silicate melt + SiO2 � silica enriched melt T > 1000-1100 oC
Eutectic melt phases are formed above ±800-840 oC
ICG – EFONGA Spring School Montpellier 4-5 May 2009 23
Phase diagram for the system Na2O – SiO2 showing
eutectic sodium silicate melt phases
100 % SiO2
ICG – EFONGA Spring School Montpellier 4-5 May 2009 24
Scheme of melting reactions of soda lime glass batch
1080 oC: T
s Na
2SiO
3
910 oC : CaCO
3 ���� CaO + CO
2 (gas)
850 oC : T
s Na
2CO
3
820 oC : T
s Na
2Ca(CO
3)2
790 oC : T
eut Na
2O.2SiO
2 + SiO
2
740 oC : T
eut Na
2Ca(CO
3)2 + Na
2CO
3
650 oC : MgCO
3.CaCO
3 ���� MgO+CaCO
3+CO
2 (gas)
540 oC : MgCO
3 -> MgO + CO
2 (gas)
0 200 400 600 800 1000 1200 1400
� temperature in oC
volatilisation of water
solid state reactions
decomposition
carbonates
primary melts
Dissolution of SiO2, CaO,
MgO, Al2O3 e.d. in melt phases
ICG – EFONGA Spring School Montpellier 4-5 May 2009 25
-2
0
2
4
6
8
10
600 650 700 750 800 850 900 950 1000
Temperature [°C]
Chemical energy consumption rate [kJ·kgbatch-1·K
-1]
Overall chemical energy demand
MgCO3·CaCO3(s) -> MgO(s) + CO2(g) + CaCO3(s)
CaCO3(s) -> CaO(s) + CO2(g)
Na2CO3(s) + SiO2(q) -> Na2O·SiO2(s) + CO2(g)
Na2CO3(s) -> Na2CO3(l)
Na2CO3(l) + SiO2(q) -> Na2O·SiO2(s) + CO2(g)
Na2O·SiO2(s) + SiO2(q) -> NS(l)
CaO(s) + melt
Chemical enthalpy of batch reactions for float glass
from soda-sand-dolomite and limestone (positive: endothermic effects)
ICG – EFONGA Spring School Montpellier 4-5 May 2009 26
4. Dissolution of ‘refractory’ type raw material
in silicate melt
example: sand grains
ICG – EFONGA Spring School Montpellier 4-5 May 2009 27
Glass meltSand grain
100
CSiO2
Ce (T)
Ce(T) = saturation level SiO2 in melt
Cb = bulk SiO2 level in melt
(depends on amount
dissolved sand)
Cb
Diffusion of SiO2 in melt
Moving boundary
ICG – EFONGA Spring School Montpellier 4-5 May 2009 28
Dissolving material
One-dimensional dissolution in multi-component liquid
dissolution
Multi-component liquid
Dissolution front
a x
Mass fraction SiO2 in saturated melt: we
w
ax
w
∂∂
we
)1(2
eeA
a
e
SiOwV
x
w
Ddt
da
⋅⋅−
∂∂
⋅⋅−=⋅
ρρρρ
ρρρρρρρρ
w is mass fraction SiO2 in melt
ICG – EFONGA Spring School Montpellier 4-5 May 2009 29
Mathematical description(Ready & Cooper 1966)
- Spherical symmetry – diffusion in 3 dimensions
- Assuming constant diffusion coefficient in melt
- Ideal solution, partial molar volume of SiO2 in melt is constant
- Convection (term u) due to change of partial molar volume of SiO2 in sand versus in melt
- Moving boundary: dissolving sand is partly staying in volume it came from
J = mass flux of SiO2
D = diffusion coefficient of SiO2 in silicate melt (m2/s)
r = radial co-ordinate (distance from sand grain centre) (m)
R = radius sand grain (m)
t = time (s)
ρ = density of melt (kg/m3)
C = local SiO2 mass concentration (kg/m3)
u = mass average velocity radial direction due to expansion by dissolution
(change in molar volume) (m/s)
Mass flux (j) of dissolved SiO2
ICG – EFONGA Spring School Montpellier 4-5 May 2009 30
Solution dissolution sand grain
without forced convection
a = actual grain size radius (m)
VA = partial specific volume of SiO2 in molten glass (m3/kg)
Cs = density of sand grain (kg/m3)
Ca = mass concentration SiO2 in saturated melt (kg/m3)
Effect of moving boundary
ICG – EFONGA Spring School Montpellier 4-5 May 2009 31
Sand grain dissolution with convection by
glass melt velocity gradients & density
differences
h = mass transfer coefficient SiO2 into melt (m/s)
we = mass fraction SiO2 in saturated melt (depends on T, and glass) (kg/m3)
ws = mass fraction SiO2 in bulk melt (depends on dissolved sand)) (kg/m3)
VA = partial specific volume of SiO2 in molten glass (m3/kg)
a = actual radius sand grain (m)
t = time (s)
ρs = density of melt (kg/m3)
ρSiO2 = density sand grain (kg/m3)
D = diffusion coefficient of SiO2 in silicate melt (m2/s)
( ) )1/(2 eeAsseeSiO wVwwhdt
daρρρρρρρρρρρρρρρρ ⋅⋅−−⋅−=⋅
ICG – EFONGA Spring School Montpellier 4-5 May 2009 32
Mass transfer coefficient
h = mass transfer coefficient (m/s)
D = diffusion coefficient of SiO2 in the molten glass, based on concentration
profiles given in mass fraction (D in m2/s)
R = grain radius (m),
t = time (s),
Sh = Sherwood number for mass transfer from spherical grain,
≈ 2 + 0.89 {Re · Sc + (Gr · Sc)3/4}1/3 *
= 2 (no convection)
= f (R2/3 , D-1/3, (grad v)1/3) (convection flow of the glass melt)
= f (R3/4 , h-1/4 , D-1/4)
(free convection of surrounding melt relative to the sand grain: v = flow velocity of the
melt relative to the sand grain (m/s), η = viscosity (Pa.s)
⋅⋅⋅
+⋅⋅=
tDShR
DSh
h
2
11
2ππππ
ICG – EFONGA Spring School Montpellier 4-5 May 2009 33
0
5000
10000
15000
20000
25000
30000
1350 1450 1550 1650 1750 1850
T in K
Dissoltion tim
e in s
no convection
v-gradient
0.001 s-1
v-gradient
0.025 s-1
Dissolution time required for complete dissolution of sand grains in
almost static and stirred soda-lime silica glass melts (forced convection
with velocity gradient grad v) at different temperatures. Initial size Ao=100 mm.
ICG – EFONGA Spring School Montpellier 4-5 May 2009 34
Dissolution of sand and alumina grains in static and convective soda-
lime-silica glass melt at 1700 K, moving boundary effect taken into
account (not on concentration profiles)
0.00E+00
2.00E-05
4.00E-05
6.00E-05
8.00E-05
1.00E-04
1.20E-04
0 5000 10000 15000 20000 25000 30000 35000
time [s]
radius in m
alumina,
grad v = 0
sand,
grad v=0sand,
grad v=0.001 s-1
alumina,
grad v=0.001 s-1
alumina,
grad v=0.01 s-1
sand,
grad v=0.01 s-1
sand,
steady state
grad v=0.001 s-1
sand,
grad v= 0 steady state
ICG – EFONGA Spring School Montpellier 4-5 May 2009 35
5. Fining Processes
ICG – EFONGA Spring School Montpellier 4-5 May 2009 36
Seeds after batch melting
Fine sand
Seeds after batch melting
Coarse sand
ICG – EFONGA Spring School Montpellier 4-5 May 2009 37
Glass just after batch melting- sample thickness ± 5 mm
10 mm
ICG – EFONGA Spring School Montpellier 4-5 May 2009 38
0 to 8 mm
ICG – EFONGA Spring School Montpellier 4-5 May 2009 39
Bubbles & Seeds just after melting
• Many small seeds and bubbles (Blisters) in glass melt
(Mulfinger 1976 GTB)
– More than 100.000 per kg glass melt
– Most bubble diameters: 0.05 -0.4 mm
• In most glass melts (using carbonates):
– bubbles in batch melting area: contain often mainly CO2
• Large concentrations dissolved CO2 in melt
• During sand grain dissolution in melt: generation
of fine CO2 seeds (Gispen)
heat transfer
gas release
combustion space
reaction zone
thick-
ness normal batch
temperature
profile
reaction zone
glass melt layer
figure 1b
glassmelt
flow heat
transferred
figure 1c
glass
level
from Glass Service
ICG – EFONGA Spring School Montpellier 4-5 May 2009 40
Fining
Objective of Fining:
Removal of bubbles and dissolved gases from the glass melt
Rising velocity of bubble:
ρ = Density of the glass melt [kg/m3]
η = Viscosity of the melt [Pa·s]
R = Bubble radius [m]
g = Acceleration of gravity [m/s2]
c = Factor (e.g. Stokes c = 2/9)
η
Rgρcv
2
ascension
⋅⋅⋅=
ICG – EFONGA Spring School Montpellier 4-5 May 2009 41
Fining
Time to reach glass surface (1 meter)
0
50
100
150
200
250
0 100 200 300 400 500
Bubble diameter [µm]
Time to reach glass level at 1 meter [h]
1350 OC
1400 OC
1450 OC
1500 OC
ICG – EFONGA Spring School Montpellier 4-5 May 2009 42
II. start of fining:
gases diffuse into
bubble
I. static bubble
Reaction in melt: release of fining gases
Pgases melt > pt (pt is pressure in bubble)
III. Fining gases and
other dissolved
gases diffuse
strongly into bubble
ICG – EFONGA Spring School Montpellier 4-5 May 2009 43
Two fining steps
• First step: primary fining
– High temperatures
– Bubble agglomeration and bubble size growth
– Dissolved gases diffuse from melt in to bubbles (like
bubbles in soda drinks)
– Ascension to glass melt surface
• Second step: Secondary fining/Refining (secondary fining)
– Dissolution of (small) remaining bubbles
• Only effective if bubble contains gases (CO2, O2, SO2+O2)
that dissolve in cooling melts
• Glass melt should be lean in dissolved gases
ICG – EFONGA Spring School Montpellier 4-5 May 2009 44
Mechanism sulfate primary fining
Fining process in glass melt
pSO2 · pO21/2 ·aNa2O
aNa2SO4
K =
Increasing temperatures lead to increasing K-values →
extra oxygen gas & SO2 gas release:
- oxygen & SO2 molecules diffuse into growing bubbles
- bubble ascension increases (vascension~R2)
- sulfate retention decreases
pSO2· pO21/2
K’ =[SO3]
ICG – EFONGA Spring School Montpellier 4-5 May 2009 45
Fining reaction: T > TFining onset
Na2SO4 ⇔ Na2O + SO2 (gas) +1/2 O2 (gas)
Fining (primary)
– Fining agents added to the batch to enhance the
rising velocity of bubbles
– Often used fining agent: Sodium sulphate
Dilution of N2 & CO2 in bubble by fining gases
SO2CO2
O2
N2
Stripping of CO2
and N2 from melt
Cm CO2
Cm N2
][SO
pOpSOK
3
22'⋅
=
ICG – EFONGA Spring School Montpellier 4-5 May 2009 46
Multicomponent diffusion of gases in bubbles
Shi = 1+ (1+ 2·v·R/Di )1/3
[ ] ( )
⋅⋅⋅
+⋅−⋅⋅⋅⋅Σ⋅=⋅⋅
tDShR
CCTRp
DShRTRpR
dt
d
ii
iisig
t
iigt
2
11
2 4)3/()4( i
23
ππππ
ππππππππ
ICG – EFONGA Spring School Montpellier 4-5 May 2009 47
Fining/Refining: degassing & removal of bubbles
• Mostly applied fining agents in glass industry: Na2SO4 & Sb2O5
– Na2SO4 (m) → SO2 (g) + 0.5 O2 (g) + Na2O (m)
– Sb2O5 (m) → Sb2O3 (m) + O2 (g)
• Na2SO4 added in concentrations 0.1 – 1 wt. % to batches of:
– Soda lime glass for container, float and tableware
– E-borosilicate glass for fibres
• Na2SO4 partly decomposes during batch melting & releasing SO2 in
early melting stages
• Dissociation temperature of Na2SO4 in melt:
– Between 1350 – 1480 ºC, depending on redox state
– Between 1100-1350 oC (reduced batches) Na2SO4+Na2S
reactions forming SO2 and or S2 gas.
ICG – EFONGA Spring School Montpellier 4-5 May 2009 48
0.0
0.1
0.2
0.3
0.4
0.5
0.6
-8 -7 -6 -5 -4 -3 -2 -1
Log pO2 in the melt at 1400°C (bar)
Sulfur retention (wt.%SO
3) Sulfur only in
form of S2-
Sulfur in
form of SO42-, S2-
(probably also SO32-?)
Sulfur only in
form of SO42-
-30 -20 -10 0 +10 +20
redox number
Fe2+/Fetotal 80 70 60 40 25 15 %
1400 oC
1500 oC
ICG – EFONGA Spring School Montpellier 4-5 May 2009 49
30 mm
Synthetic gas
Mass
Spectrometer
ICG – EFONGA Spring School Montpellier 4-5 May 2009 50
High temperature test facility
ICG – EFONGA Spring School Montpellier 4-5 May 2009 51
Fining/Refining: degassing & removal of bubbles
1. Primary fining
– Removal of bubbles by rising of bubbles to melt
surface
– Bubble growth under influence of fining agents
– Stripping of dissolved gases by growing of gas bubbles
(dilution)
Fining
ICG – EFONGA Spring School Montpellier 4-5 May 2009 52
Enhanced Sulfate Fining by
Dissolved Water in Melt
SO2
H2O
O2 In oxygen-fired glass furnace:
peH2O = 0.25-0.40 bar
Fining only if:
peSO2 + peO2 > 0.70 - 0.75 bar
In air-fired furnace:
peH2O = 0.10-0.15 bar
Fining only if :
peSO2 + peO2 > 0.9 barSO2
H2OO2
CO2
SO2
H2ON2
O2
SO2
CO2
Oxy-case
Air case
O2
N2
ICG – EFONGA Spring School Montpellier 4-5 May 2009 53
Gas evolution during sulfate fining of soda lime glass
melt - effect of water vapor level -
0
10
20
30
40
50
60
1300 1400 1500 1600
Temperature in oC
Volume of gas in
m3/batch
0 bar
0.20 bar
0.60 bar
water vapor pressure
Evolution of fining gas: water lean & rich melts
ICG – EFONGA Spring School Montpellier 4-5 May 2009 54
Stripping of dissolved gases from melt
ICG – EFONGA Spring School Montpellier 4-5 May 2009 55
Pressure in melt before and during fining & cooling
0.0
0.2
0.4
0.6
0.8
1.0
1.2
1200 1300 1400 1500 1600
Temperature in oC
Total internal pressure in melt
bar
[S]initial= 0.3 mass% SO3 300 mgr water/kg [Fe2+]/ [Fetotal] = 20 %
ICG – EFONGA Spring School Montpellier 4-5 May 2009 56
1.E-05
1.E-04
1.E-03
1.E-02
1.E-01
1.E+00
1250 1350 1450 1550
Temperature in oC
Partial pressure in float glass m
elt
in bar
O2
SO2
H2O
N2
CO2
Partial pressure in float glass melt during heating
[S]initial = 0.3 mass% SO3 300 mgr water/kg [Fe2+]/ [Fetotal] = 20 %
ICG – EFONGA Spring School Montpellier 4-5 May 2009 57
CO2
O2fining gas
Modeling dissolved gas distribution in glass melt tank
mol/m3
mol/m3
ICG – EFONGA Spring School Montpellier 4-5 May 2009 58
Fining/Refining: degassing & removal of bubbles
2. Secondary fining (refining)
– Re-absorption of residual gases during controlled cooling
• Chemical solubility SO2 and O2 increases with
decreasing temperature: gases will be re-absorbed
during cooling.
• Physical solubility of dissolved gases increases slightly
with decreasing temperature: these gases will also be re-
absorbed during cooling
Refining
ICG – EFONGA Spring School Montpellier 4-5 May 2009 59
Fining at low pressure
- Same amount of gas needs large volume
- Low partial pressures in bubble will stimulate gas diffusion
from melt into bubble
ICG – EFONGA Spring School Montpellier 4-5 May 2009 60
6. Evaporation processes
ICG – EFONGA Spring School Montpellier 4-5 May 2009 61
Multi-component glasses
• Different oxides
• Oxides in glass with high chemical activity or vapour
pressure:
– React at glass melt surface with combustion gases
– Evaporate from glass melt surface
– Show depletion at surface layer
INCONGRUENT EVAPORATION
ICG – EFONGA Spring School Montpellier 4-5 May 2009 62
Evaporation mechanisms
• Direct evaporation of volatile glass components from the surface of the melt,
e.g. volatilization of PbO from lead crystal melts;
• Evaporation of components by reactions in the melt itself, forming volatile
compounds; generally such volatile compounds exhibit high activity coefficients
and weak bonding with other glass melt species.
– An example: formation of alkali borates in alkali borosilicate melts,
subsequently evaporation of alkali meta-borates/tetra-borates takes place,
Na2O(melt) + B2O3 (melt) ⇔ 2NaBO2 (melt) ⇒ 2 NaBO2 (vapor)
• Evaporation by reactions of certain glass melt components with gas
species at the surface of the melt.
The evaporation rate & vapor pressure depends on the composition of
the gas atmosphere above the melt.
B2O3 (glass melt) + H2O ⇒ 2HBO2 (vapor)
Na2O (glass melt) + H2O (gas) ⇒ 2NaOH (vapor)
Na2O(glass melt) + CO (gas) ⇒ 2Na (vapor) + CO2
ICG – EFONGA Spring School Montpellier 4-5 May 2009 63
Kinetics of evaporation
The volatilization rate is often determined by:
• mass transport of the relevant species from the
melt interior (bulk) to the surface;
• the vapor pressures of the volatile components at the
surface of the melt, dependent on the glass composition,
temperature and gas atmosphere;
• the mass transfer of evaporated species from the surface
of the melt into the main gas stream above the melt.
ICG – EFONGA Spring School Montpellier 4-5 May 2009 64
Reactive evaporation
For reactive evaporation of a component j in the melt reacting with
a gas k and forming gaseous species i with saturation pressure
pi*, according to reaction:
n·j (melt) + m·k (gas) � q·i (gas)
Reaction equilibrium: pi*q = K · aj
n · pkm
The values of K (equilibrium constant, assuming chemical
equilibrium at the glass melt surface) and aj (activity of component j
in the molten glass at the surface) can be determined
experimentally or by thermodynamic modeling
ICG – EFONGA Spring School Montpellier 4-5 May 2009 65
Static melt and static atmosphere above the
melt (interface x = 0)Diffusion in melt of reacting glass melt component j:
dCj/dt = Dm,j·δCj2/δx2
Dm,j is the inter-diffusion coefficient of the volatile component j in the melt.
at t = 0 -∞ < x < 0 Cj = Cjbulk
at t > 0 x �−∞ Cj = Cjbulk
at t > 0 x = 0 Cj = Cjsurface(t)
For the vapor i in a static gas phase with partial vapor pressure pi,
the diffusion process in the gas phase can be described in a similar way:
δ(pi/RgT)/δt = Dg,i ·δ2(pi/RgT) /δx2
Dg,i is the diffusion coefficient of the vapor I in the gas phase.
at t = 0 0 < x < ∞ pi = pi,gasbulk
at t > 0 x �∞ pi = pigasbulk
at t > 0 x = 0 pi = pi*(t)
Time dependency: Cjsurface(t).
ICG – EFONGA Spring School Montpellier 4-5 May 2009 66
4954
4956
4958
4960
4962
4964
4966
4968
4970
0 0.01 0.02 0.03 0.04 0.05 0.06
distance from surface [mm]
Na2O concentration [mol.m-3]
5 sec.
50 sec.
250 sec.
DNa2O=3.3 10-11 m2.s -1
Calculated time dependent- Na2O concentration profiles in static melt
Situation: static conditions in semi-infinite gas phase with 0.55 bar vapor pressure
and semi-infinite soda-lime-silica melt
(13 wt% Na2O, 10 wt% CaO, 5 wt% MgO, 72 wt% SiO2).
Dg,NaOH = 2.7 10-4 m2·s-1 , Dm,Na2O = 3.3 10-11 m2·s-1
ICG – EFONGA Spring School Montpellier 4-5 May 2009 67
Evaporation in gas flow above molten glass
glass melt surfaceC j-profile
pb,i
p*i
Transport of component
j in the , Dm,j
main gas stream
velocity, vg
surface reaction:
n·j (melt)+ m·k (gas) ⇒ q·i (gas)
diffusion of gas i in
gas boundary layer, Dgi
Example:
Na2O (m) + H2O(g) ⇔ 2NaOH (g)
melt
ICG – EFONGA Spring School Montpellier 4-5 May 2009 68
Evaporation in gas flow
Average evaporation rate (over length Lg of gas flow above
melt ) of component i (formed by reaction of glass
compound j) into (turbulent) gas phase:
Qm,j =(ni/qi)·A·vg0.8·ρg
0.47·µgas-0.47·Dg
0.667·Lg-0.2· Rg
-1·T-1·B·Cj,x=0(t)
The proportionality parameter B depends on the furnace
atmosphere composition and the chemical activity of the
volatile component in the melt.
For NaOH-evaporation, the B value depends on the water
vapor pressure in the furnace atmosphere, B ∼ pH2O0.5
ICG – EFONGA Spring School Montpellier 4-5 May 2009 69
Mass transfer equations
Average evaporation rate (rate of loss of glass component j)
over length Lg from leading edge:
Qm,j = -Dm,j·(δCj/δx)x=0 = α·Cj,x=0(t)
α = (ni/qi) · A· vg0.8·ρg 0.47·µgas
-0.47·Dg0.667·Lg
-0.2· Rg-1·T-1· B
Turbulent flow of gas
v = velocity, g refers to gas phase, Rg is universal gas constant, T in K,
B ratio between vapour pressure i and surface concentration component j
A = between 0.03 and 0.04 for turbulent gas flow (Re > 300000 or for disturbed flows)
ICG – EFONGA Spring School Montpellier 4-5 May 2009 70
Solution in flowing gas and static melt
For kd defined as α/DmNa2O the solution for a single component j
Evaporating from a static melt in flowing gas phase
Assuming complete depletion at surface for t �∞
MQm.j is the total evaporation mass loss per unit surface area between
time 0 and τ
MQm.j = (Cj,0/kd)·{exp(kd2·DmNa2O·τ)·erfc[kd·(DmNa2O·τ)
0.5] -1
+ 2kd·(DmNa2O·τ/π)0.5}
Cj,x=0(t) = Cj,0· exp(kd2·DmNa2O·τ)·erfc[kd·(DmNa2O·τ)
0.5]
Cj,0 = bulk concentration compound j at t=0
ICG – EFONGA Spring School Montpellier 4-5 May 2009 71
3000
3500
4000
4500
5000
5500
0 0.5 1 1.5 2 2.5
distance from surface [mm]
Na2O concentration in
melt [mol.m
-3]
stagnant gas
Lg= 2 m, v= 2 m.s-1
Lg= 2 m, v = 5 m.s-1
Lg= 0.5 m, v= 2 m.s-1
Local concentration profile in soda-lime silica melt after 7200 seconds exposure time,
calculated for NaOH-evaporation from static melt in static or flowing gas phases,
(Lg= downstream distance from leading edge ).
Temperature = 1500 oC, pH2O = 0.55 bar. Dm,Na2O = 3.3 10-11 m2·s-1
Glass composition (mass %): SiO2 =72, Na2O =13, MgO = 5, CaO = 10
ICG – EFONGA Spring School Montpellier 4-5 May 2009 72
Change in Na2O-surface concentration soda-lime-silica melt at different
temperatures in flowing gas (5 ms-1), 1 meters downstream.
pH2O in gas = 0.55 bar & Na2O in glass = 13 mass%.
Dm,Na2O= 8 10-10 exp(-5655/T) in upper graph
parameter is temperature:
0
1000
2000
3000
4000
5000
6000
0 5000 10000 15000 20000 25000 30000
time [s]
Na2O-surface concentration
[mol.m
-3]
1723K
1773 K
1823 K
1873 K
ICG – EFONGA Spring School Montpellier 4-5 May 2009 73
Experimental – Set up to study
(reactive) evaporation from molten glass
Thermocouples
Gases IN:
N2, H2O,
O2
Porous
plate
Platinum
coating (30 cm)Platinum boat
Platinu
m gas
samplin
g probemelt
Platinum funnel
ICG – EFONGA Spring School Montpellier 4-5 May 2009 74
Mass transfer in gas phase during
transpiration – evaporation test
0.0E+00
5.0E-04
1.0E-03
1.5E-03
2.0E-03
2.5E-03
0 100 200 300 400Reynolds number
Re (-)
Water evaporation rate
QH2O (m
oles s
-1 m
-2)
Measurerments
CFD model
Empirical equation (2.19)
( )31
5.1
3
5.0
21 Re221
2Re
⋅⋅⋅
⋅+
+⋅⋅+= ScCSc
ScCCSh ddiontranspirat
d
DShh
igiontranspirat
ig
,
,
⋅=
Vessel with
liquid of melt
x = 0
( )bulkii
ig
ig ptpTR
hQ −⋅
⋅= *,
, )(
pi*(t) (e.g. p*NaOH or p*NaBO2)
can be derived from evaporation
(transpiration experiments)
From measured Qg,i and Sherwood
relations derived with model liquids
ICG – EFONGA Spring School Montpellier 4-5 May 2009 75
y = 0.9823x
R2 = 0.9283
1.E-09
1.E-08
1.E-07
1.E-06
1.E-09 1.E-08 1.E-07 1.E-06
Measured aNa2O (-)
Modeled a
Na2O (-)
SiO2:Na2O:CaO = 74:16:10 mol
Na2O.2SiO2
Na2O activity at glass melt surface determined by transpiration test
measuring p*NaOH: Na2O + H2O � 2 NaOH
ICG – EFONGA Spring School Montpellier 4-5 May 2009 76
Derivation chemical activity of volatile glass
component at surface of melt
K = exp(-∆G/RT) = p*NaOH2/aNa2O.pH2O
From thermodynamic tables:
∆G = GfNa2O+GfH2O- 2GfNaOH(g)
p*NaOH is measured from QNaOH and pH2O is
controlled � aNa2O (surface) can be determined
K is calculated by standard Gibbs free energy values of
products & reactants of reaction
ICG – EFONGA Spring School Montpellier 4-5 May 2009 77
Non static melt & non static gas phase
free convection by density gradients
Float glass melt with Na2O concentration differences
High Na2O
Low Na2O
Mid Na2O
Gas flow
ICG – EFONGA Spring School Montpellier 4-5 May 2009 78
6. Homogeneity of glassMicro-mixing: transfer from high to low chemical activity by diffusion
Macro-mixing: elongation of in-homogeneities exposed to velocity gradient in melt
Lo
Slow diffusion processes
C(x,t)t = 0
t = t1
t = t2
dC
dtDd C
dx= ⋅
2
2
C
C
-
L
2
o
m
o
2A= exp
. .π D t
Co
Cm (t)
ICG – EFONGA Spring School Montpellier 4-5 May 2009 79
Macro-mixingReduction of diffusion distance, Lo
y
velocity v + dv
velocity v
In the case, t dv/dy >> 1:
For macro-mixing in combination with diffusion (by approximation):
A = proportionality factor dependent on the shape of the cord
C
C
m
o
A= −.exp. . .( / )π 2 3 2
0
2
D t dv dy
L
LL
tdv
dy
=⋅
0
ICG – EFONGA Spring School Montpellier 4-5 May 2009 80
Macro versus only Micro mixing
• Small velocity gradients (> 0.01 m/s per m) enhance
homogenisation process with factor 20 to 100
• Velocity gradients by:
– Stirring
– Bubbling
– Temperature gradients � free convection
ICG – EFONGA Spring School Montpellier 4-5 May 2009 81
Thank you for your attention
What does a number tell us without the proper unit?