WO2021256243A1

WO2021256243A1 - Continuous casting method

Info

Publication number: WO2021256243A1
Application number: PCT/JP2021/020838
Authority: WO
Inventors: 智也小田垣; 則親荒牧; 恭寛重歳; 義陽大場; 貴史丸子
Original assignee: Ｊｆｅスチール株式会社
Priority date: 2020-06-18
Filing date: 2021-06-01
Publication date: 2021-12-23
Also published as: TWI784570B; TW202200290A

Abstract

Proposed is a continuous casting method for reliably suppressing a surface crack of cast slab and, in particular, manufacturing a high-quality slab without corner cracks. This continuous casting method is for performing continuous casting of steel. In the continuous casting method, a casting mold in which a chamfering shape of a casting mold corner part satisfies a relationship of 0.09≤C/L≤0.20 (in formula, C represents a corner chamfering amount (mm), L represents a cast slab short-side length (mm)) is used, and an average secondary cooling water amount density to lower straightening from directly under the casting mold at the cast slab corner part is set to 20-60L/(min•m²). In particular, it is preferable that the steel has a compositional makeup containing, in mass%, 0.05-0.25% of C and 1.0-4.0% of Mn, and further optionally containing at least one selected from 0.01-0.1% of Nb, 0.01-0.1% of V, and 0.01-0.1% of Mo.

Description

Continuous casting method

The present invention relates to a continuous steel casting method that suppresses the occurrence of surface cracks in slabs in continuous casting.

In recent years, the required specifications for high-strength steel have become stricter, and the content of alloying elements such as Cu, Ni, Nb, V and Ti has increased for the purpose of improving the mechanical properties of steel sheets. When such alloy steel is cast using, for example, a vertical bending type continuous casting machine, the four corners of a rectangular cross section orthogonal to the casting direction of the slab at the straightened portion and the bent portion of the slab (hereinafter referred to as slab corner portions). Stress is applied to the surface cracks, especially at the corners of the slab. This corner crack is likely to cause a surface defect of the thick steel sheet, and causes a decrease in the yield of the steel sheet product.

That is, the hot ductility of the alloy steel slab is significantly reduced at the temperature near the _{Ar 3} transformation point where the solidified structure is transformed from the austenite phase to the ferrite phase.

Therefore, in the continuous casting process, in order to prevent the above-mentioned corner cracking, the surface temperature of the slab is controlled by secondary cooling to correct the temperature above the transformation point, or the solidified structure of the slab is controlled to a structure that is hard to crack. Is commonly done.

In order to keep the slab surface temperature high, the spray pipe near the corner of the slab is generally closed and the spray width is cut without cooling.

As a method of controlling the solidification structure, for example, Patent Document 1, to start the secondary cooling of the slab immediately after withdrawal of the slab from the rectangular mold, once Ar ₃ transformation of the surface temperature of the slab The time and slab surface to keep the slab surface temperature below the _{Ar 3} transformation point when cooling to a temperature below the point and then reheating to a temperature above the _{Ar 3 transformation point and then straightening the slab.} A technique has been disclosed in which the solidified structure from the surface of the slab to a depth of at least 2 mm is made into a mixed structure of ferrite and pearlite with an unclear austenite grain boundary by setting the minimum temperature at which the temperature reaches to an appropriate range. Is

Japanese Unexamined Patent Publication No. 2002-307149

However, the above-mentioned prior art has the following problems.
That is, the technique of spray width cutting is to stop the spray from the spray near the corner of the slab and prevent the corner temperature from dropping. However, since the width of the slabs is wide in response to various needs in recent years, there is a problem that a large amount of capital investment is required to properly spray the corners of the slabs of all sizes. In addition, when the casting speed is slowed down, the corners of the slab are cooled from the two sides of the slab on the long side and the short side, so that supercooling is likely to occur. In addition, since the staying time in the continuous casting machine is increased, there is a problem that the corner temperature is lowered by radiative cooling even if the cooling spray is not sprayed.

Further, in the technique described in Patent Document 1, there is a concern about the influence of dripping water flowing along the slab after being sprayed onto the slab from the secondary cooling spray. In particular, when the casting speed is slowed down, the dripping water affects the cooling of the slab surface, so that it may be difficult to quantitatively control the slab surface temperature, for example, by heat transfer calculation.

The present invention has been made in view of such circumstances, and an object of the present invention is to prevent surface cracks in a slab which has not been sufficiently eliminated by controlling the temperature of the slab by secondary cooling alone. The purpose is to propose a continuous casting method that surely suppresses and produces high quality slabs without corner cracks in particular.

The inventors have found that surface cracking of a slab can be suppressed by suppressing a temperature drop at a corner of a slab during secondary cooling while using a mold having a casting space having an appropriate shape, and have conceived the present invention. ..

The continuous casting method of the present invention that advantageously solves the above problems is a method of continuously casting steel, using a mold in which the chamfered shape of the mold corner portion satisfies the following equation (1), and the slab corner portion. It is characterized in that the average secondary cooling water amount density from directly under the mold to the lower straightening is 20 to 60 L / (min · m ^2).
0.09 ≤ C / L ≤ 0.20 ... (1)
Here, C: corner chamfer amount (mm),
L: Short side length of slab (mm)
Represents.

In the continuous casting method according to the present invention, the component composition of the steel is C: 0.05 to 0.25% and Mn: 1.0 to 4.0% in mass%, and further Nb: A more preferable solution is to optionally have at least one selected from 0.01 to 0.1%, V: 0.01 to 0.1%, and Mo: 0.01 to 0.1%. It is thought that it can be.

According to the present invention, the temperature of the corners of the slab is controlled by secondary cooling while using a mold in which a casting space having an appropriate shape is partitioned, so that corner cracking of the continuously cast slab is prevented and high quality is achieved. It will be possible to provide slabs.

It is a top view which shows the mold which concerns on one Embodiment of this invention. It is a graph which shows the influence which the chamfer shape has on the temperature of a slab corner part.

The steel continuous casting method (steel piece manufacturing method) according to the embodiment of the present invention includes a step of casting while supporting the slabs drawn from the continuous casting mold by a plurality of pairs of rolls facing each other. First, the molten steel is primarily cooled with a mold. Then, the slab is withdrawn from the mold at a predetermined drawing speed, and the slab is secondarily cooled while being supported by a plurality of pairs of rolls arranged in the casting direction to obtain a steel slab. For example, in the case of a curved continuous casting machine, there are one or more pairs of rolls for straightening curved slabs in the vicinity of the exit side, and these rolls straighten the bending and pull out in the horizontal direction. At that time, in order not to induce surface cracking at the corners of the slab during straightening, a mold in which a casting space having an appropriate shape is partitioned is used, and it is appropriate in the cooling zone from directly under the mold to the bending back straightening point (lower straightening). It is important to go through a proper cooling pattern. The continuous casting machine used in the present embodiment is not particularly limited as long as it includes bending or bending back straightening from directly under the mold to carrying out the slab.

Here, the inventors observed surface cracks in the slabs cast by the curved continuous casting machine. Surface cracks in the slab were concentrated in and near the top corners. This is because tensile stress is generated during bending back correction. The upper surface side of the slab means the inside of the bending of the curved band of the curved continuous casting machine, that is, the long side surface side which is the upper surface of the horizontal band.

When the cracks were etched, the cracks propagated along the old austenite grain boundaries, so it was considered that the cracks occurred in the temperature range where the ferrite transformation started from austenite (generally called the embrittlement temperature), and the secondary cooling conditions were set. Experiments with various changes were conducted.

That is, when an experiment using heat transfer analysis was conducted under various secondary cooling conditions, the secondary cooling spray applied to the vicinity of the slab corner portion from directly under the mold to entering the lower (bending) straightening portion was found. It was found that if the average water volume density is ^{controlled to less than 20 L / (min · m 2} ) and the surface temperature is _{controlled so that it does not fall below Ar 3} points before bending straightening, cracking at the corners of the slab can be reduced. ..

However, as mentioned above, the temperature at the corners of the slab tends to drop compared to the surroundings, so it is necessary to significantly reduce the amount of cooling spray, and insufficient cooling has occurred on the surface of the slab other than the corners. As a result, slab bulging (a phenomenon in which the slab swells between the support rolls due to the static pressure of molten steel) occurs due to insufficient solidification shell thickness, and cracks occur inside the solidification shell.

Therefore, the inventors focused on the shape of the slab. Since the conventional slab is rectangular and the corners are cooled from two surfaces, supercooling of the corners of the slab is likely to occur. We considered that changing the shape of the slab would change the cooling structure and suppress supercooling, and examined the appropriate slab shape by thermal stress analysis.

As a result of examination by thermal stress analysis, the slab has a chamfered shape with the four corners of the rectangular cross section orthogonal to the casting direction removed, resulting in supercooling at the slab corners and stress load. It was found that the stress can be reduced. Then, in order to make the four corners of the slab into a chamfered shape, casting using a mold in which the four corners (right-angled portions) of the casting space, which is rectangular like a mold having a rectangular cross section, is removed into a right-angled triangular shape to form a chamfered shape. It is important to do. Hereinafter, a mold having a casting space having such a chamfered shape is also referred to as a chamfer mold.

As a result of diligent studies to clarify the chamfered shape of the mold that fits the object of the present invention, it was found that the following shape definition is necessary. The chamfered portion 4 of the chamfer mold is shown in the top view of the chamfer mold of FIG. When chamfering is performed to remove the right-angled portion of each corner of the rectangular casting space in the shape of a right-angled triangle, the ratio of the right-angled triangle to the length a on the long side 2 side of the mold is the ratio b / a of the length b on the short side 3 side of the mold. A thermal analysis was performed on the effect of this ratio b / a on the overcooling of the corners of the slab. The calculation result is shown in FIG. 2 after standardizing the temperature of the rectangular mold (b = a = 0 in FIG. 1) before chamfering at 750. Here, a was fixed in the range of 2 to 20 mm and b was fixed in the range of 20 mm for the investigation. The temperature of the corners of the slab in the chamfer mold was set to the lowest temperature between the two corners formed by chamfering. As shown in FIG. 2, it can be seen that the temperature of the slab corner portion is higher than that of the rectangular mold by first using the chamfer mold. In particular, when the ratio b / a = 1, the temperature at the corner of the slab becomes maximum. In the present embodiment, the chamfering amount C (= a = b) is set under the condition of b / a = 1 where the effect is the largest, and the continuous casting mold 1 is designed.

As described above, this embodiment is suitable for application to steels having high embrittlement susceptibility to austenite to ferrite transformation. For example, the composition of steel has C: 0.05 to 0.25% and Mn: 1.0 to 4.0% in mass%, and further Nb: 0.01 to 0.1%, V. It can be suitably applied when one or more selected from: 0.01 to 0.1% and Mo: 0.01 to 0.1% are arbitrarily possessed. Hereinafter, unless otherwise specified, the component composition is simply expressed as% in "mass%".

C: 0.05-0.25%
When the C content is 0.05 to 0.25%, the austenite grains are particularly liable to become coarse. Therefore, it is preferable to apply this embodiment in the case of a steel composition having a high embrittlement sensitivity and a C content of 0.05 to 0.25%.

Mn: 1.0 to 4.0%
If the Mn content is less than 1.0%, MnS, which is an embrittlement factor, is unlikely to be generated, so that there is no problem. If it is 1.0% or more, the embrittlement sensitivity becomes high, but if it exceeds 4.0%, the product becomes too strong, which is not desirable. Therefore, it is preferable to apply this embodiment in the case of a steel composition having a high embrittlement sensitivity and a Mn content of 1.0 to 4.0%.

One or more selected from Nb: 0.01 to 0.1%, V: 0.01 to 0.1% and Mo: 0.01 to 0.1% Nb, V and Mo contribute to the improvement of steel strength. However, if the content of each element is less than 0.01%, it is difficult to form carbonitride which is an embrittlement factor, so that there is no problem. On the other hand, if it exceeds 0.1%, the price of the alloy becomes high and the cost rises, and the performance becomes excessive more than necessary. Therefore, it is not desirable to add more than 0.1%.

(Example 1)
Using a curved continuous casting machine, in mass%, C: 0.18%, Si: 1.4%, Mn: 2.8%, P: 0.020% or less, S: 0.003% or less, And Ti: Steel having a predetermined composition containing 0.020% was cast. The Ar ₃ transformation point of this steel is 805 ° C. The casting conditions were in the range of a casting thickness of 220 mm, a casting width of 1000 to 1600 mm, and a casting speed of 1.20 to 1.80 m / min. The slab temperature when passing through the bent part (lower straightening) was confirmed by measuring with a thermocouple or a radiation thermometer. After casting, the slab is subjected to color check (dye penetrant inspection) after removing oxides on the slab surface by shot blasting in order to facilitate observation of cracks on the slab surface. The presence or absence of cracks in the corners was investigated. Then, the corner crack occurrence rate was evaluated by the number of corner cracked slabs / the number of surveyed slabs × 100%. For the investigation of internal cracks, a cross-sectional sample perpendicular to the casting direction of the slab was cut out, milled, and then macro-etched with warm hydrochloric acid. The presence or absence of internal cracks was investigated using macro-etched photographs.

First, a survey was conducted to determine the size of the chamfer size (chamfer amount) C [mm] that exerts its effect. Here, the average secondary cooling water density from directly under the mold to the lower straightening on the corner of the slab was fixed at ^{60 L / (min · m 2).} The results are shown in Table 1. When the short side length of the slab is L [mm], the C / L becomes smaller than 0.09. In the cases of 1 and 2, the distances from the long side and the short side are almost the same as those of the rectangular corner, and the supercooling suppressing effect is hardly obtained. On the other hand, the test No. in which the C / L is larger than 0.20. In the cases of 8 and 9, two-sided cooling occurred at the chamfered portion and the short side, or at the joint portion between the chamfered portion and the long side, and the temperature of the slab corner portion decreased. That is, it was found that the chamfering amount of the chamfer mold needs to be in the range of 0.09 ≦ C / L ≦ 0.20.

(Example 2)
Next, in order to determine the relationship between the average secondary cooling water density applied to the corners of the slab until passing through the bent portion (lower straightening), corner cracks, and internal cracks, a test was conducted under the same steel grade and continuous casting conditions as in Example 1. Was carried out. The results are shown in Table 2.

In the rectangular mold (test Nos. 10 to 16), the average secondary cooling water density is ^{less than 20 L / (min · m 2} ) (test Nos. 10 and 11), so that the corner temperature becomes Ar ₃ or more and the corner cracks. Can be seen to be reduced. However, since it is impossible to slowly cool only the corners, the thickness of the solidified shell near the corners is insufficient, causing internal cracking due to bulging. From this, it can be seen that it is not possible to suppress both corner cracking and internal cracking with a normal rectangular mold. Further, even when a chamfer mold (test Nos. 17 to 23) other than this embodiment is used, as shown in Example 1, there is almost no effect of suppressing corner supercooling, so that the average is 2 as in the rectangular mold. Corner cracking could not be suppressed unless the density of the next cooling water was reduced to less than 20 L / (min · m ² ), and internal cracking due to bulging could not be avoided. When the chamfer molds (test Nos. 24 to 31) of the present embodiment were applied, the ^{point that internal cracks occurred at less than 20 L / (min · m 2} ) (test Nos. 24 and 25) was the same. .. On the other hand, due to the effect of changing the shape of the slab, supercooling of the corners of the slab is suppressed in the average secondary cooling water density range (test No. 24 to 30) of ^{60 L / (min · m 2) or less, resulting in corner cracking.} Was able to prevent. That is, by setting the average secondary cooling water density from directly under the mold to the lower straightening on the corners in ^{the range of 20 to 60 L / (min · m 2} ) (test No. 26 to 30), corner cracking can be suppressed and the inside can be suppressed. We were able to produce slabs that were both crack-proof and crack-suppressing.

1 Continuous casting mold 2 Long side 3 Short side 4 Chamfered part

Claims

This is a method of continuous casting of steel, using a mold whose chamfering shape at the corners of the mold satisfies the following formula (1), and the average secondary cooling water volume density from directly under the mold to the lower straightening applied to the corners of the slab. Is 20 to 60 L / (min · m 2 ), which is a continuous casting method.
0.09 ≤ C / L ≤ 0.20 ... (1)
Here, C: corner chamfer amount (mm),
L: Short side length of slab (mm)
Represents.
The composition of the steel is C: 0.05 to 0.25% and Mn: 1.0 to 4.0% in mass%, and further, Nb: 0.01 to 0.1%, V. The continuous casting method according to claim 1, wherein one or more selected from 0.01 to 0.1% and Mo: 0.01 to 0.1% are arbitrarily contained.