prof. a k lahiri -plenary lecture- some aspects for clean steel production
TRANSCRIPT
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Some aspects for clean steel production
A K lahiri
Former Professor IISc, Bangalore, [email protected]
Abstract: Often large number of small Al2O3inclusions are formed in the
tundish. As such these are not detrimental to steel but they clog the nozzle
resulting asymmetric flow in mold and mold flux entrapment. Proper tundish
slag along with electromagnetic break can help to overcome this problem.
Introduction
Steel with desired low value of impurities like Phosphorus, Sulfur, total
oxygen, Nitrogen, Hydrogen and in some grade even carbon is known as
clean steel. Among these impurities the behavior of oxygen is different in
two ways. After Ladle refining, the other impurities remain almost
unchanged but oxygen may increase due to absorption from air or pick up
from refractory and slag. Secondly other impurities remain in solution but a
significant part of oxygen is present as oxide inclusion so oxygen content is
always specified as total oxygen. Since significant part of oxygen is present
as inclusion, liquid steel is not homogeneous with respect to oxygen.
For number grades both total oxygen and inclusion size should be within a
limit. For sheets in tin plate, total oxygen
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Oxygen Pick up from air
During liquid steel pouring of from ladle to tundish, the shroud preventsexposure of metal stream to atmosphere in the steady state operation. But
during initial filling up or during ladle change over, metal is exposed to
ambient air. This leads to pick up of oxygen and nitrogen from atmosphere.
Fig. 1 shows the change in oxygen level as observed by Solhed1. When
pouring starts, there is significant oxygen pick up by metal, which leads to
overall increase in oxygen level in tundish. At the outlet oxygen decreases
Figure 1: Variation of total oxygen content at the inlet, middle and outlet
with time. Ladle was changed at 40th
and 83rd
minute.
monotonically from ~50ppm at the start to ~15ppm at the time of ladle
change over. Again immediately after ladle change over, it increases to a
high value and then monotonically decreases. This trend is present for
second change over as well confirming significant oxygen pick up from
ambient air. This leads to more inclusion in first slab and immediately after
ladle change over. It sometimes leads to cluster of iron oxide, Fig2.
0
2 5
5 0
7 5
1 0 0
1 2 5
1 5 0
1 7 5
0 2 0 4 0 6 0 8 0 1 0 0T i m e ( m i n )
O
(ppm)
I n l e t
M id d l e
O u t le t
0
50
100
150
200
0 4 8 12
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Fig.2 Cluster of Iron oxide in the first slab
Tundish covering slag
Figure 3 schematically shows that covering slag in contact with steel is
liquid but that in contact with atmosphere is solid. The liquid slag prevents
oxygen transfer from air and readily absorbs oxide inclusion. So the ideal
tundish slag should cover steel surface with a liquid slag from the beginning
Fig.3 Schematic diagram of tundish covering slag in a tundish
so that it prevents oxygen diffusion from atmosphere and can absorb the
inclusion. But in reality this is rarely the case. If liquid slag is formed by the
end of first ladle tapping, it is considered as a good covering slag sincesometimes it is formed only during tapping of third or fourth ladle. Besides
slag should have high dissolution rate and solubility for the inclusions and
should not react with the dissolved elements present in steel. Because of
these requirements recently Hollappa et al2used thermodynamic modeling
along with laboratory experiment to develop chemistry of active tundish
slag. Although the technique is useful to design the chemistry of ideal
tundish covering slag but its usage may be limited due to two reasons: firstly
it has to be cost effective and secondly number of factors including particle
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size distribution of the powder controls the liquid slag formation. So it will
require practical modification. Both acidic as well as basic fluxes are used
as covering slag. Kijac et al3
showed that basic slag is more effective thansilico aluminate type slag in removing Al2O3inclusions but even basic slag
eventually gets saturated with Al2O3 .
Slag metal interaction
Slag and metal form two separate layers but slag metal interface may not be
smooth and a mixed domain may exist close to interface because of highly
turbulent flow due to Kelvin-Helmholtz interfacial instability. The stability
condition for the present system is given by4,5
.
sm
smsm
sm
sm
gUU
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region above the metal phase. The thickness of mixing zone is about 100m
close to inlet but in other areas, the size is smaller. The thickness of mixedzone in Fig.4 is about 30. Mixed zone is layered with Al2O3inclusions in
the upper part. Most of the inclusions present here are less than 10m.
Similar observation was reported by Solhed6 earlier. Fig.5 shows the
interface. It shows that in microscopic scale the interface is not flat and
. Figure 5 slag metal interface1
inclusions are present at the interface. Small globular slag lumps and
inclusions could be seen close to interface. Fig.6 shows that these inclusions
are CaO, Al2O3 and CaO.Al2O3. The presence of CaO.Al2O3 inclusions
suggest that at the interface Al2O3 reacts with CaO present in slag to form
these inclusions. Small Al2O3inclusions might have formed by the reaction
of aluminum with FeO in slag or dissolved oxygen. Since the sizes of
globular slag lumps are very small, and no big lump was observed, the origin
of these lumps could be interfacial instability or due to the impact of highenergy small eddies present in the metal. Solhed et al
7 showed by
mathematical modeling that the recirculation flow at the inlet region can also
lead to slag entrapment in metal and metal entrapment in slag. However only
small fraction of these can reach the outlet.
It is well known that ladle slag infiltrates into the tundish. This leads to
increase in CaO even in silico aluminate type tundish covering slag besides
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it increases FeO content of tundish slag resulting in formation of Al2O3
inclusions.
Fig.6 Inclusions close to interface. Whitish ones are Al2O3and black ones
are CaO and partly whitish and partly blackish ones are CaO.Al2O31.
Table 2 shows inclusion count of samples from ladle furnace and twolocations of tundish. The increase of small size inclusion
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Refractory metal interaction
Refractory is another source of oxygen pick up. MgO based refractories usedin tundish contain olivine which is a solid solution of fayalite (Fe2SiO4) and
forsterite (Mg2SiO4). These can react with de-oxidized steel according to
following reactions:
Fe2SiO4= 2Fe + 2O + SiO2
Mg2SiO4+ SiO2= 2(MgSiO3)
2Al + 3O = Al2O3
MgO + Al2O3= MgAl2O4
Pack et al8studied used tundish refractory by electron probe micro analysis,
TEM and back scattered electron images. They found olivine where its
faylite component is reduced, Fig.7 Besides they observed Mg2SiO3 and
MgAl2O4and concluded that all the above mentioned reactions take place in
the tundish.
Fig.7 TEM of olivine in contact with liquid steel containing 0.04%Al8
Mould
Although under ideal operating condition, inclusions particularly Al2O3should get removed in the mould but in reality sometimes a significant
amount of exogenous inclusion gets trapped into metal. Fluid flow
characteristic in the mould has a major role in it.
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Absorption of inclusion
Mold flux picks up about 4% Al2O3. Part of it is de-oxidation product andpart of it is formed by the reaction:
1.5 SiO2(flux) + [Al] = Al2O3+ 1.5 [Si]
However in case of special steel which contains high Al, pick up of Al2O3is
much higher and thereby the resulting flux will have different property
compared to original flux.
SEN clogging
It is well established that Al2O3 inclusions deposit on inner wall of nozzle
and clog it. Fig.8 shows original as well as clogged nozzle as reported by
Rodl et al9. It shows that inclusions deposit primarily at the discharge end of
the nozzle and blocks the port partly.
Fig 8 Nozzle clogging9
Fig 9 shows that discharge from the port of clogged nozzle and flow in the
mold is highly asymmetric and complex. Asymmetry is very significant
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Fig 9 Computed result of clogged nozzle9
on the top surface where a region on one side has a high velocity. Longs10
model showed that only inclusions below 15m can deposit on the nozzle.
Al2O3 inclusions deposited on SEN sometimes get dislodged and gets
entrapped in metal as large inclusion. Figure 10 shows one such case. It isinteresting to note that inclusions in the cluster are
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Longs result. This along with the observation of Rodl9 that number of
inclusions, not total inclusions, play a major role in clogging suggest that
Al2O3 formed in tundish due to oxygen influx has a major role in clogging.
Flux entrapment
Fig. 11 shows schematically shows top surface of mold. The wave shown on
the top is not a standing wave but it oscillates. Because of the shear force
Fig 11 Schematic diagram of flux metal interface in the mould
at the slag metal interface liquid flux can get entrained either because of
wave instability or vortex formation as shown in Fig 12(a) and (b)respectively. These happen only at high metal velocity at the meniscus.
(a) (b)
Fig 12 Flux entrainment by sharing and vortex formation11
Possibility of slag entrapment by these mechanism becomes less for high
viscosity of mold slag.
Besides the above two mechanisms of slag entrainment, solid flux gets
entrained in the metal if amplitude of wave is more than the liquid slag layer
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thickness. In this case part of meniscus metal becomes bald as shown in Fig
13(a) thereby when solid flux is added there, it directly gets entrained in
metal, Fig 13(b)12
. This can be avoided by maintaining proper thickness ofliquid flux layer.
(a) (b)
Fig 13 Flux entrainment due to balding of meniscus (a) balding (b) Flux
entrainment
It has been pointed out earlier that nozzle clogging leads to asymmetric flow
and can lead to significant disturbances in meniscus. This could lead to flux
entrapment. Sometimes it is found that even at the apparently steady casting
condition strand quality is below par. This could be attributed to asymmetric
flow through the ports due to nozzle clogging.
Flux can get entrapped in metal due to Kelvin Helmoltz instability although
there is no direct evidence for it.
Discussion
Improved tundish design helped in reducing large inclusion from the steel.
But due to various mechanisms of oxygen input in the tundish, a large
number of fine Al2O3 inclusions
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with high Al2O3absobing capacity. Basic slag satisfy these requirements but
more research is needed to see that slag formation is early enough.
Ca treatment is widely used to prevent the nozzle clogging. But investigation
of Rodl9
showed that some CaO form CaO.2Al2O3which has melting point
of 1705C and these inclusions deposit on SEN.
The deposition of inclusion on SEN makes the fluid flow in the meniscus
complex and leads to high meniscus velocity which may lead to flux
entrainment. Only reduction of velocity at the meniscus can prevent flux
entrainment. So electro-magnetic break and SEN design to give swirling
flow are the available options. A simpler option of course is the increase of
port diameter but there is practical limitation to this.
Conclusion
Suitable tundish flux development which will lead to early liquid slag
formation in tundish along with high Al2O3absorption capacity will go long
way in producing cleaner steel.
References
1. Henrik Solhed, Pranesh Dayal, A.K.Lahiri : Int Conf on Continuous
Casting Past, Present & Future, Jamshedpur, 24- 25th October 2005
2. L. Hollappa et al : Steel Res Int. published on line on 18thFeb.2013
3. J. Kijac et al : Metalurgija vol 43 2004 p 59
4. S. Chandrasekhar: Hydrodynamics and Hydromagnetic stability, Dover
Pub. N.Y.,1961 p485
5. Y.Chung and A.W.Cramb: Metall Mater. Trans. Vol.31B (2000) p957
6. H.Solhed, L. Jonsson and P.Jonsson : Metall Mater. Trans. Vol.33B
2002 p17
7. H.Solhed, L. Jonsson and P.Jonsson : Steel Res. Int. 2008 vol 79 p 348
8. A. Pack, S.Hoernes and Th Walther: Proc. 6th
Int. congress on Applied
Mineralogy, Gottingen, Germany, 17-19 July 2000 p518
9. S. Rodl et al : New strategies for clogging prevention for improved
productivity of Steel, EU report 2012
10.M. Long et al ISIJ Int. 2010 vol 50 p712
11.D Gupta and AK Lahiri: Ironmaking- Steelmaking 1996, vol 23 p361
12.D Gupta and AK Lahiri:Metall Trans.B, 1996 vol 27B p 695