CN107427907A - Use the manufacture method of the ingot casting of continuous casting machine - Google Patents
Use the manufacture method of the ingot casting of continuous casting machine Download PDFInfo
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- CN107427907A CN107427907A CN201580078104.7A CN201580078104A CN107427907A CN 107427907 A CN107427907 A CN 107427907A CN 201580078104 A CN201580078104 A CN 201580078104A CN 107427907 A CN107427907 A CN 107427907A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/051—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds into moulds having oscillating walls
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/124—Accessories for subsequent treating or working cast stock in situ for cooling
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Abstract
The manufacture method of the ingot casting using continuous casting machine is provided, even if in the case where molten steel has defined constituent, the ingot casting for the face crack that can also be inhibited is without reducing productivity ratio.The manufacture method of the ingot casting of the present invention has：In the mould to containing C：Below the mass % of more than 0.13 mass % 0.20, Mn：The process that more than 0.50 mass % molten steel is once cooled down；The process for pulling out ingot casting from the mold with more than 1.0m/ points of pull-out speed；And the process that secondary cooling is carried out to the ingot casting, in the process of secondary cooling is carried out to the ingot casting, including the surface temperature of the ingot casting is compared Ar3Transformation temperature is low, thereafter returns to and compares Ac3The high temperature of transformation temperature, the vibration condition of the mold meet that the negative slip time (Tn) is less than 0.20 second more than 0.08 second, negative slip time ratio (RNS) be less than more than 0.30 0.38 condition, up to the surface temperature of the ingot casting reaches Ar from the ingot casting is by the mold3Time untill transformation temperature was more than 60 seconds.
Description
Technical field
The present invention relates to the manufacture method of the ingot casting using continuous casting machine.
Background technology
In order to keep the surface quality of the product after rolling ingot casting well, the table of ingot casting is prevented in the continuously casting of steel
Facial cleft line is extremely important.Here, in the secondary cooling process of ingot casting, the crystallization group in ingot casting is made by using γ → α phase transformations
Austenite crystal miniaturization in knitting, so as to suppress the face crack of ingot casting, as this technology, patent document 1~3 is known
's.By making austenite crystal granular, increase the surface area of relatively fragile austenite grain boundary, make correction (top correction,
Correct bottom) ingot casting on the correction belt of continuous casting machine when act on ingot casting the stress of austenite grain boundary disperse, so as to difficult
To produce face crack.In addition, if austenite crystal is small, even if once cracking, crackle is also difficult to spread.
Following technology has been recorded in patent document 1：In the casting using flexure type or the continuous casting machine of vertical bending type
In the secondary cooling process of ingot, from mold out after within 2 minutes during the surface temperature of ingot casting is compared Ar3Transformation temperature
It is low, hereafter, more than 850 DEG C are returned to, so as to prevent the transversal crack of ingot casting.
Following technology has been recorded in patent document 2：In the casting using flexure type or the continuous casting machine of vertical bending type
In the secondary cooling process of ingot, ingot casting is temporarily cooled down so that the surface temperature of ingot casting compares A3Transformation temperature is low, hereafter, with 0.003~
0.015 liter/cm2The Slow cooling that the water yield density divided is carried out 0.5~2.0 minute compares A so that the surface temperature of ingot casting returns to3
The high temperature of transformation temperature, so as to prevent the face crack of ingot casting.
Following technology has been recorded in patent document 3：It is continuous in the continuous casting machine using flexure type or vertical bending type
The carbon equivalent Cp that casting crack is recipient, is defined with following (1) formulas is more than the 0.10 low-alloy carbon steel less than 0.18
When, make the concave meniscus portion of the molten steel out of mold play mold lower end untill ingot casting pull-out the time required to be 1 minute within
Ground carries out 2 coolings, the surface temperature of ingot casting is reduced to A within 1 minute at once after mold pull-out3Below transformation temperature,
So as to prevent the face crack of ingot casting.
Cp=[C]+[Mn]/33+ [Ni]/25+ [Cu]/44+ [N]/1.7 (1)
Wherein, Cp represents the interior content (quality %) for representing each element in steel of carbon equivalent, [].
Citation
Patent document
Patent document 1：Japanese Unexamined Patent Publication 9-225607 publications
Patent document 2：Japanese Unexamined Patent Publication 11-197809 publications
Patent document 3：Japanese Unexamined Patent Publication 9-47854 publications
The content of the invention
The invention problem to be solved
The technology of patent document 1~3 is all following technology：Ingot casting temperature is controlled in secondary cooling, makes the knot in ingot casting
Austenite crystal miniaturization in crystalline substance tissue, so as to prevent the face crack of ingot casting.
In recent years, seek to increase the pull-out speed of the ingot casting from mold for large-duty requirement is proposed, if but
Increase pulls out speed, then ingot casting easily produces face crack.Moreover, according to the research of the present inventor etc., following situation has been distinguished：
C is being contained with more than 1.0m/ points of pull-out speed continuously casting：Below the mass % of more than 0.13 mass % 0.20, Mn：0.50 matter
In the case of the high Mn steel of high C for measuring more than %, the technology of patent document 1~3 can not be substantially prevented from the transversal crack of ingot casting and indulge
To face crack as crackle.
Although that to be carbon equivalent Cp for above-mentioned more than the 0.10 low-alloy carbon steel less than 0.18 still fall within is as described above
In the case of the high high Mn steel of C, even if the control of the surface temperature of ingot casting as carrying out patent document 3, also produces table sometimes
Facial cleft line.In addition, for the carbon equivalent Cp steel bigger than 0.18, in the case of the high high Mn steel of C as described above, certainly
Face crack is produced sometimes.
In view of above-mentioned problem, it is an object of the invention to provide a kind of manufacture method of the ingot casting using continuous casting machine,
Even if molten steel have it is above-mentioned as defined in the case of constituent, the ingot casting of the face crack that can also be inhibited without
Reduce productivity ratio.
For solving the scheme of problem
In order to solve above-mentioned problem, the present inventor found after attentively studying：Dividing the pull-out speed of the above with 1.0m/
Continuously casting contains C：Below the mass % of more than 0.13 mass % 0.20, Mn：The situation of more than the 0.50 mass % high Mn steel of high C
Under, by meeting two following conditions simultaneously, split so as to surface as being substantially prevented from transversal crack and longitudinal crack
Line.
[1] only austenite crystal miniaturization is made to be inadequate, it is necessary to make by secondary cooling as patent document 1~3
Surface temperature up to ingot casting from ingot casting is by mold reaches Ar3Time untill transformation temperature was more than 60 seconds.
[2] it is inadequate only by appropriateization of secondary cooling condition, it is also desirable to make once to cool down (initial in mold
Solidification) condition suitably change.That is, the vibration condition as mold is, it is necessary to make negative slip time Tn and negative slip time ratio
RNSIn defined number range.
The present invention is completed based on above-mentioned opinion and design.That is, flexure type or vertical bending type are used in the present invention
Continuous casting machine ingot casting manufacture method in, it is characterised in that have：
In the mould to containing C：Below the mass % of more than 0.13 mass % 0.20, Mn：More than 0.50 mass % molten steel
The process once cooled down；
The process for pulling out ingot casting from the mold with more than 1.0m/ points of pull-out speed；And
The process that secondary cooling is carried out to the ingot casting, in the process of secondary cooling is carried out to the ingot casting, including make
The surface temperature of the ingot casting compares Ar3Transformation temperature is low, thereafter returns to and compares Ac3The high temperature of transformation temperature,
The vibration condition of the mold meets that negative slip time Tn is less than 0.20 second more than 0.08 second, negative slip time ratio
Rate RNSFor the condition below more than 0.30 0.38,
Up to the surface temperature of the ingot casting reaches Ar from the ingot casting is by the mold3Time untill transformation temperature
More than 60 seconds.
The effect of invention
According to the manufacture method of the ingot casting using continuous casting machine of the present invention, even if there is above-mentioned defined group in molten steel
In the case of composition, the ingot casting for the face crack that can also be inhibited is without reducing productivity ratio.
Brief description of the drawings
Fig. 1 is the schematic diagram of the continuous casting machine of the vertical bending type used in one embodiment of the present invention.
Fig. 2 is that the casting direction of the ingot casting pulled out in the continuous casting machine of the vertical bending type shown in Fig. 1 from mold cuts open
View.
Fig. 3 is being pulled out from mold in the continuous casting machine of the flexure type used in another embodiment of the present invention
The casting direction sectional view of ingot casting.
Fig. 4 is the solid for the ingot casting being shown to transversal crack caused by the surface in ingot casting and longitudinal crack
Figure.
Embodiment
Hereinafter, it is explained with reference to one embodiment of the present invention.
First, to the continuous casting machine of the vertical bending type of twisted-pair type used in one embodiment of the present invention
100 structure illustrates.Continuous casting machine 100 has：Casting ladle 10, tundish 11, mold 12, nozzle 13, more two pairs of rollers 14, cut
Disconnected device 15 and electromagnetic mixing apparatus 16.
Molten steel M is contained in the casting ladle 10 of the topmost positioned at continuous casting machine.Molten steel M is noted from the bottom of casting ladle 10
Enter to the tundish 11 positioned at the lower section of casting ladle 10.Hereafter, molten steel M is injected into from the bottom of tundish 11 via submersed nozzle
To mold 12, the once cooling of molten steel is carried out in mold 12.
In order to which the ingot casting pulled out from mold 12 S is guided from vertical to horizontal direction and prevents from being drawn by ferrostatic pressure
The ingot casting S risen deformation, more two pairs of rollers 14 are along curved arrangements such as circular arc, hyperbolas.A part for roller 14 has as drawing
Go out the function of ingot casting S pinch roll.Reference picture 2, from mold 12 to vertical lower section pull out ingot casting S by belt 20A it
Afterwards, it is bent at the correction belt 20B of top, the state of bending is kept at curved bel 20C, afterwards at the correction belt 20D of bottom
Go back to tabular and by horizontal stripes 20E.Up to horizontal stripes immediately below from mold, molten steel be present not in ingot casting S inside
Solidification portion, the substantially total length that roller 14 is configured to throughout horizontal stripes immediately below mold support to ingot casting S surface.Nozzle 13
Between roller adjacent in the casting direction, the secondary cold of ingot casting is carried out from these nozzles 13 to ingot casting S spray coolings water
But.In addition, nozzle is actually configured with multiple between each roller, but in Fig. 1, illustrated with the line segment for connecting multiple nozzles
Represent one part to property.
It is provided with the downstream of horizontal stripes and fills the cut-out of the gas torch of the ingot casting S cut-outs of solidification, hydraulic cutting etc.
Put 15.The ingot casting (slab, steel ingot or steel billet) cut off using shearing device 15, which is discharged and is transported to from continuous casting machine 100, to be rolled
Device processed.
Reference picture 2, at top correction belt 20B and bottom correction belt 20D, bending stress acts on ingot casting S.Because this is curved
Transverse stress and cause at the correction belt 20B of top tensile stress act on ingot casting S lower face side, at the correction belt 20D of bottom
Tensile stress acts on ingot casting S upper surface side.Because above-mentioned reason, as shown in Figure 4 in the upper surface of ingot casting S (slab)
Side or lower face side (mainly corner) produce transversal crack C sometimes1." transversal crack " refers in this manual as described above
Be along direction, ingot casting the face crack vertical with casting direction.
On the other hand, if being cooled down by force to the surface of ingot casting after the pull-out of mold 12 just, because of solidified shell
It is uneven, produce longitudinal crack C on ingot casting S (slab) as shown in Figure 4 sometimes2.It is " longitudinal in this manual as described above
Crackle " refers to the face crack of ingot casting approximately along casting direction.
One embodiment of the present invention is related to the face crack of ingot casting when preventing continuously casting, more particularly to prevents peritectoid
The transversal crack of steel (the low-alloy carbon steel of sub- peritectoid~mistake peritectoid) and the method for longitudinal crack.
In addition, the continuous casting machine of the flexure type shown in Fig. 3 can also be used for this invention.Continuously cast in vertical bending type
Make in machine, in order to which from mold to vertical, lower section pulls out ingot casting, the internal face of mold 12 is flat.It is but continuous in flexure type
In the case of casting machine, bending mold 21 is used in order to pull out ingot casting S in arc-shaped from mold.Due to the inwall of mold 21
Face is bent, and therefore, the ingot casting of bending is sent, and is turned back and is corrected at the correction belt 20D of bottom.In the situation of flexure type
Under, it is different from the situation of vertical bending type, in the absence of the bending process at the correction belt of top.
Then, the constituent of molten steel is illustrated.
In the case where the carbon equivalent Cp defined with above-mentioned (1) formula is more than 0.10 and the steel less than 0.18, most of
In the case of substantially observed with the austenite grain boundary of ferrite film just analysed in the surface part of slab.When in this state
When lower Fig. 2 and tensile stress as shown in Figure 3 act on ingot casting, easily produce the crackle at austenite grain boundary and simultaneously produce horizontal stroke
To crackle.For such case, the surface of the ingot casting immediately below mold to being drawn out carries out cooling by force so that the surface of ingot casting
Temperature compares Ar3Transformation temperature is low, hereafter, is returned to more than 850 DEG C or compares Ac3Transformation temperature high temperature is so that ingot casting skin section
Austenite crystal miniaturization, so as to be reduced the effect of transversal crack.
But containing C：Below the mass % of more than 0.13 mass % 0.20, Mn：The situation of more than 0.50 mass % steel
Under, following tendency be present.
(A) depth of chatter mark deepens, and stress concentration easily produces transversal crack in the depressed part of oscillation mark.
(B)Ar3Transformation temperature and Ac3Transformation temperature is tended to reduce, in the case where increasing pull-out speed, it is intended to difficult
With show by the strong cooling zone of slab Lai ductility improve effect.
(C) even identical carbon equivalent, compared with the steel of low C content or low Mn contents, also easily in larger temperature
Scope is brittle, and the sensitivity of crackle is strong.
(D) because the thickness that is uneven and causing solidified shell of cooling becomes uneven, longitudinal direction is also easy to produce in mold content
Crackle.
Therefore, shown in embodiment as be described hereinafter, C is being contained with more than 1.0m/ points of pull-out speed continuously casting：0.13 matter
Measure below the mass % of more than % 0.20, Mn：In the case of more than the 0.50 mass % high Mn steel of high C, even if having distinguished as above institute
The control for the surface temperature for carrying out ingot casting is stated, the transversal crack of ingot casting can not be substantially prevented from, surface is split as longitudinal crack
Line.
As described above, the constituent as the molten steel of the object of the present invention contains C：0.20 matter of more than 0.13 mass %
Measure below %, Mn：More than 0.50 mass %.In C content less than situation of 0.13 mass % or the Mn content less than 0.50 mass %
Under, face crack can be substantially prevented from by carrying out the control of the surface temperature of ingot casting as prior art, in the absence of the present invention's
Problem.In addition, in the case where C content is more than 0.20 mass %, Ar3Transformation temperature and Ac3Transformation temperature reduces, and is difficult to reality sometimes
The secondary cooling condition in present embodiment is applied, i.e.,：In the lower end of the mold out of continuous casting machine to the correction belt of top
Belt at, the surface temperature of ingot casting is compared Ar3Transformation temperature is low, hereafter, is returned to and compares Ac3The high temperature of transformation temperature.
In the case where Mn contents are more than 2.5 mass %, in the same manner as the increased situation of C content, Ar3Transformation temperature and Ac3
Transformation temperature reduces, and the secondary cooling condition being difficult to carry out sometimes in present embodiment, being additionally, since MnS becomes easily to separate out, institute
Also tend to strengthen with crackle sensitivity.Therefore, Mn contents are preferably below 2.5 mass %.
The constituent of molten steel can also arbitrarily contain Si：Below 0.8 mass %, P：Below 0.10 mass %, S：
Below 0.05 mass %, Al：Below 0.05 mass %, Cu：Below 0.5 mass %, Ni：Below 1.0 mass %, Cr：0.6 matter
Measure below %, V：Below 0.14 mass %, Nb：Below 0.09 mass %, Ti：Below 0.4 mass %, N：Below 0.02 mass %
One or more, remainder is Fe and inevitable impurity.
The manufacture method of the ingot casting of one embodiment of the present invention has：The process for once cooling down molten steel in the mould；With
The process that more than 1.0m/ points of pull-out speed pulls out ingot casting from the mold；And the work of secondary cooling is carried out to the ingot casting
Sequence, include making the surface temperature of the ingot casting to compare Ar in the process for carrying out secondary cooling to the ingot casting3Transformation temperature is low, hereafter
It is returned to and compares Ac3The high temperature of transformation temperature.In the case where pulling out underspeed 1.0m/ points, carry out as prior art
The control of the surface temperature of ingot casting can be substantially prevented from face crack, in the absence of the problem of the present invention.Pull out the upper limit of speed simultaneously
It is not particularly limited, 2.5m/ points can also be set to.For the pull-out speed more than 2.5m/ points, this implementation is difficult to carry out sometimes
Secondary cooling condition in mode, i.e.,：In the lower end of the mold out of continuous casting machine to the belt the correction belt of top
Place, makes the surface temperature of ingot casting compare Ar3Transformation temperature is low, hereafter, is returned to and compares Ac3The high temperature of transformation temperature.
In a refrigerating work procedure, mold is in vertical with constant cycle up-down vibration.Here, the one of the present invention
In embodiment, the vibration condition of mold meets that following condition is critically important, i.e.,：Negative slip time Tn is 0.20 second more than 0.08 second
Hereinafter, negative slip time ratio RNSFor less than more than 0.30 0.38.In Tn more than 0.20 second or RNSIn the case of 0.38,
Oscillation mark deepens, and is worked on ingot casting surface as otch (notch), and the generation of transversal crack becomes notable.In Tn less than 0.08
In the case of second, the lubrication between mold and solidified shell is insufficient, causes fluctuation of service and then causes bleedout.In RNSDeficiency
In the case of 0.30, the influx and consumption of moulded powder reduce, and cause to cause bleedout.So, by meeting that Tn is
Less than 0.20 second more than 0.08 second and RNSFor the condition below more than 0.30 0.38, bleedout will not be produced, horizontal stroke can be prevented
To crackle.In addition, it is less than 0.20 second and R in TnNSUnder conditions of less than 0.38, with Tn more than 0.20 second or RNSExceed
0.38 situation is compared, and the particle diameter of the old γ grains of formation at initial stage after solidification diminishes.The phenomenon is it is also contemplated that help to reduce
Transversal crack.
Here, during the decrease speed of mold period more fireballing than the pull-out of ingot casting is negative slip, in a cycle
The time of this period is referred to as " negative slip time Tn (second) ".On the other hand, the decrease speed of mold is the pull-out speed of ingot casting
During during being below positive slip, the time of this period is referred to as " positive to slip time Tp (second) " in a cycle.To
When the vibration frequency of mold is set to f (Hz), Tn+Tp=1/f.Negative slip time ratio RNSIt is defined as Tn/ (Tn+Tp).In addition,
The waveform of vibration does not limit, and whether sinusoidal waveform or nonsinusoidal waveform can.
Then, in one embodiment of the present invention, as secondary cooling condition, up to ingot casting from ingot casting is by mold
Surface temperature reach Ar3Time untill transformation temperature, this was critically important more than 60 seconds.In the case where the time is less than 60 seconds,
Ingot casting is sharp cooled after just being pulled out from mold, as a result, solidified shell becomes uneven, produces longitudinal crack.It is logical
Crossing makes the time to prevent transversal crack more than 60 seconds.
As described above, the continuous casing of steel according to an embodiment of the present invention, can be inhibited transverse direction
The ingot casting (slab, steel ingot or steel billet) of the high-quality of crackle and longitudinal crack.The result is that, it is not necessary to the finishing on ingot casting surface
Process, the situation that the crackle in rolling process hinders operation is also not present, therefore, yield rate improves., can by improving yield rate
Using cut down until by iron ore as raw material come it is in the great energy consumption required for the iron-smelting process untill manufacturing steel,
It is industrially and in terms of energy-conservation effective with the corresponding part of yield rate raising.
Embodiment
Using the continuous casting machine shown in Fig. 1, according to the continuously casting condition continuously casting shown in table 2 shown in table 1
The steel of each constituent (remainder is Fe and inevitable impurity).Underscore portion in table 2 is represented in the present invention
Scope outside.In table 1, according to each constituent, the carbon equivalent ce calculated by following (2) formulas and by following (3)
Carbon equivalent Cp that formula calculates, the Ar calculated by following (4) formulas3Transformation temperature and the Ac calculated by following (5) formulas3
Transformation temperature is also shown in the lump.
CE=[C]+[Mn]/33 (2)
Cp=[C]+[Mn]/33+ [Ni]/25+ [Cu]/44+ [N]/1.7 (3)
Ar3=910-273 × [C] -74 × [Mn] -16 × [Cr] (4)
Ac3=937-476.5 × [C]+56 × [Si] -19.7 × [Mn] -4.9 × [Cr]+124.8 × [V] -19 × [Nb]
+198×[Al] (5)
Here, content (quality %) of each element in steel is represented in [].Steel B, C and D carbon equivalent ce and Cp ratio
0.18 is big, and the carbon equivalent ce and Cp of other steel are in 0.10~0.18 scope.
In table 2, " chilling temperature " of secondary cooling condition is represented from mold lower end to vertical the correction belt of top
The minimum of the surface temperature of the ingot casting taken, " until Ar3Time needed for untill point " represents straight from ingot casting is by mold
Surface temperature to ingot casting initially reachs Ar3Time untill transformation temperature, " backheat temperature " represent to reach from the surface temperature of ingot casting
The peak of the surface temperature of the ingot casting during untill reaching top correction belt is played to above-mentioned minimum.In each test bar
Under part, it is distributed by adjusting the pull-out speed (casting speed) of ingot casting and the water yield density of secondary cooling water, on changing
State chilling temperature, until Ar3Time and backheat temperature needed for untill point.In addition, the surface temperature of above-mentioned ingot casting refers to
By solidification described later, Analysis of Heat Transfer and the surface temperature in corner calculate, ingot casting.
The passage of the surface temperature of ingot casting by it is disclosed in Japanese Unexamined Patent Publication 4-231158 publications, based on numerical computations
Two-dimentional solidification, Analysis of Heat Transfer and obtain.That is, the heat transfer coefficient obtained by each nozzle is obtained by off-line testing to be distributed
, data dependent on cooling water inflow and ingot surface temperature.Cooling water inflow with each nozzle, the ingot casting table at a distance of each nozzle
The position in face and each moment, position ingot casting surface temperature matchingly, set the ingot casting on secondary cooling band
The boundary condition on surface.In the same manner as the method disclosed in Japanese Unexamined Patent Publication 4-231158 publications, heat transfer coefficient is set, to logical
The cooling that the contact with backing roll is carried out is crossed to be evaluated.The boundary condition on ingot casting surface as described above is according on casting direction
Position and change, therefore, in the two-dimentional solidification, Analysis of Heat Transfer on the section vertical with casting direction, by will casting
Position on direction divided by pull out speed and be converted to the elapsed time, so as to set the boundary condition in each elapsed time.Respectively
The Temperature Distribution on the section vertical with casting direction in elapsed time obtains as analysis result, therefore, by that will draw
Go out speed to be multiplied with the elapsed time and be converted to the position on casting direction, so as to obtain the optional position on casting direction
Temperature Distribution on the section vertical with casting direction at place.According on the section vertical with casting direction obtained as described above
Ingot surface temperature distribution with the passage of the position on casting direction, can obtain " chilling temperature " shown in table 2,
" until Ar3Time needed for untill point ", " backheat temperature ".
In each test example, the generation to the tissue, crackle on slab top layer is evaluated, and result is shown in table 2.In table
In 2, " tissue on slab top layer " is observed by the tissue of the end of the slab to being reclaimed after experiment, will substantially be observed old
γ crystal boundaries and remain the tissues of thick old γ grains and be recited as " thick grain ", the situation for the tissue that old γ crystal boundaries are not known is remembered
Carry as " tissue miniaturization "." generation of crackle " by just casting after ingot casting surface visually observed, hereafter to entering
The surface of ingot casting after row rolling is visually observed, and in above-mentioned observation visual twice, will not have transversal crack and longitudinal direction
The situation of crackle is recited as "None", and situation in addition is recited as " having ".
[table 1]
[table 2]
In Tn more than 0.20 second or RNSIn experiment No.8 and No.10 more than 0.38, although secondary cooling condition is in
In the scope of the present invention, transversal crack is still generated.On the other hand, in underspeed 1.0m/ points of experiment No.12 is pulled out,
Even if Tn was more than 0.20 second and RNSMore than 0.38, transversal crack is not also produced.Accordingly understand：It is pulling out speed
In the case of more than 1.0m/ points, even if secondary cooling condition is within the scope of the invention, transversal crack is also produced sometimes,
It is less than 0.20 second and R by being set to TnNSFor less than 0.38 mold vibration condition, so as to prevent transversal crack.
In addition, even C content be it is more than 0.13 mass % below 0.20 mass % and Mn contents be 0.50 mass % with
On steel B, C, D, the tendency be also identical tendency (with reference to experiment No.16,17,21,22,26,27).On the other hand, contain in C
Measure less than in steel E, F, the G of 0.13 mass % or Mn content less than 0.50 mass %, divide the feelings of the above for 1.0m/ in pull-out speed
Under condition, even if Tn was more than 0.20 second or RNSMore than 0.38, do not produce yet transversal crack (with reference to experiment No.31,32,36,37,41,
42).Its reason is not known, it is believed that it is due to C content or Mn contents are low, therefore it is weak for the sensitivity of crackle.According to upper
Situation is stated to understand：C is being contained with more than 1.0m/ points of pull-out speed continuously casting：The mass % of more than 0.13 mass % 0.20 with
Under, Mn：In the case of more than the 0.50 mass % high Mn steel of high C, even if secondary cooling condition is within the scope of the invention,
Transversal crack is produced sometimes, is less than 0.20 second and R by being set to TnNSFor less than 0.38 mold vibration condition, so as to
To prevent transversal crack.
In addition, being below the mass % of more than 0.13 mass % 0.20 in C content and Mn contents are more than 0.50 mass %
In steel A, B, C, D, until Ar3Time needed for untill point is under conditions of less than 60 seconds, in the width center of ingot casting
Position produce longitudinal crack (with reference to experiment No.6,15,20,25).On the other hand, in C content less than 0.13 mass % or Mn
In steel E, F, the G of content less than 0.50 mass %, even in until Ar3The bar that time needed for untill point is less than 60 seconds
Part, it will not also produce longitudinal crack (with reference to experiment No.30,35,40).Its reason is not known, it is believed that be due to C content or
Mn contents are low, so as to prevent the thickness of solidified shell from becoming uneven.Accordingly understand：With 1.0m/ point with
On pull-out speed continuously casting contain C：Below the mass % of more than 0.13 mass % 0.20, Mn：More than 0.50 mass % high C
In the case of high Mn steel, longitudinal crack is produced sometimes, by making until Ar3Point untill needed for time more than 60 seconds, so as to
Longitudinal crack can be prevented.
In addition, it is Ar in chilling temperature3More than transformation temperature or backheat temperature is Ac3Experiment No.5 below transformation temperature, 7,
14th, in 19,24,29,34,39, no matter the composition of steel, old γ grains are all thick, all generate transversal crack.
Embodiment more than：According to the present invention it is possible to rationally and efficiently same using continuous casting machine
When obtain the good ingot casting of quality of no face crack.
Industrial applicibility
According to the manufacture method of the ingot casting using continuous casting machine of the present invention, even if molten steel have defined composition into
In the case of point, the ingot casting for the face crack that can also be inhibited is without reducing productivity ratio.
Description of reference numerals
100 continuous casting machines (vertical bending type)
10 casting ladles
11 tundish
12 molds
13 nozzles
14 rollers
15 shearing devices
16 electromagnetic mixing apparatus
20A belts
20B tops correction belt
20C curved bels
20D bottoms correction belt
20E horizontal stripes
21 bending molds
M molten steel
S ingot castings
C1Transversal crack
C2Longitudinal crack
Claims (1)
1. a kind of manufacture method of ingot casting, use flexure type or the continuous casting machine of vertical bending type, it is characterised in that have：
In the mould to containing C：Below the mass % of more than 0.13 mass % 0.20, Mn：More than 0.50 mass % molten steel is carried out
The process once cooled down；
The process for pulling out ingot casting from the mold with more than 1.0m/ points of pull-out speed；And
The process that secondary cooling is carried out to the ingot casting, in the process of secondary cooling is carried out to the ingot casting, including make described
The surface temperature of ingot casting compares Ar3Transformation temperature is low, thereafter returns to and compares Ac3The high temperature of transformation temperature,
The vibration condition of the mold meets that negative slip time Tn is less than 0.20 second more than 0.08 second, negative slip time ratio RNS
For the condition below more than 0.30 0.38,
Up to the surface temperature of the ingot casting reaches Ar from the ingot casting is by the mold3Time untill transformation temperature exceedes
60 seconds.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2015-077893 | 2015-04-06 | ||
| JP2015077893A JP5896067B1 (en) | 2015-04-06 | 2015-04-06 | Method for producing slabs using a continuous casting machine |
| PCT/JP2015/002963 WO2016162906A1 (en) | 2015-04-06 | 2015-06-12 | Method for manufacturing slab using continuous casting machine |
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| Publication Number | Publication Date |
|---|---|
| CN107427907A true CN107427907A (en) | 2017-12-01 |
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| CN201580078104.7A Pending CN107427907A (en) | 2015-04-06 | 2015-06-12 | Use the manufacture method of the ingot casting of continuous casting machine |
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| Country | Link |
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| JP (1) | JP5896067B1 (en) |
| KR (1) | KR101949351B1 (en) |
| CN (1) | CN107427907A (en) |
| BR (1) | BR112015019860B1 (en) |
| WO (1) | WO2016162906A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113165060A (en) * | 2018-12-10 | 2021-07-23 | 日本制铁株式会社 | Method for continuously casting steel |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106623881B (en) * | 2016-12-28 | 2018-05-15 | 安徽工业大学 | A kind of tundish of controllable lower flexure strain |
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- 2015-04-06 JP JP2015077893A patent/JP5896067B1/en active Active
- 2015-06-12 KR KR1020177022744A patent/KR101949351B1/en active IP Right Grant
- 2015-06-12 WO PCT/JP2015/002963 patent/WO2016162906A1/en active Application Filing
- 2015-06-12 CN CN201580078104.7A patent/CN107427907A/en active Pending
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| CN113165060A (en) * | 2018-12-10 | 2021-07-23 | 日本制铁株式会社 | Method for continuously casting steel |
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| Publication number | Publication date |
|---|---|
| KR20170105075A (en) | 2017-09-18 |
| WO2016162906A1 (en) | 2016-10-13 |
| JP5896067B1 (en) | 2016-03-30 |
| KR101949351B1 (en) | 2019-02-18 |
| JP2016196035A (en) | 2016-11-24 |
| BR112015019860A2 (en) | 2017-07-18 |
| BR112015019860B1 (en) | 2021-01-12 |
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