JP2008062249A - Method for reducing central segregation of bearing steel in continuous casting of large cross section bloom - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a continuous casting method of bearing steel, which method can reduce central segregation based on specific operational conditions. <P>SOLUTION: The central segregation of the bearing steel containing 0.93 to 1.10 wt.% of C. 0.15 to 0.35 wt.% of Si, 0 to 0.50 wt.% of Mn, and 1.30 to 1.60 wt.% of Cr is reduced as follows. The thickness D of a casting mold is set to 350 to 410 mm. The casting speed Vc is set to 0.50 to 0.65 m/min. The specific water content Wt is set to 0.25 to 1.00 L/kg<SB>Steel</SB>. The degree ΔT of super heating is set to 10 to 45°C. The gradient GRD of a roll in a meniscus length M of 10.0 to 22.3 m is set to 0.0 to 5.0 mm/m. The gradient GRD of the roll in a meniscus length M of 22.3 to 25.9 m is set to 0.0 to 1.0 mm/m. The gradient GRD of the roll in a meniscus length M of 25.9 to 27.5 m is set to 1.0 to 2.0 mm/m. The gradient GRD of the roll in a meniscus length M of 27.5 to 32.3 m is set to 0.5 to 2.0 mm/m. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

  The present invention relates to a method for improving the center segregation of bearing steel in continuous bloom bloom casting.

  As this type of technique, Patent Document 1 discloses a technique of lightly reducing the slab from the time when the calculated solid phase ratio at the center of the slab thickness reaches a predetermined value to the time when it completely solidifies.

JP 2001-259810 A (Claim 3, paragraph numbers 0013, 0036, 0037)

  In the method disclosed in the above-mentioned Patent Document 1, since the reduction condition is set according to the solid phase rate inside the slab, it is necessary to grasp the solid phase rate inside the slab sufficiently accurately. is there. Since this solid phase ratio is extremely difficult to measure in an actual continuous casting process, it is generally obtained by solidification heat transfer calculation. (It will be understood from the description of “Calculation” solid phase ratio ”in Patent Document 1 above.)

In order to accurately perform the solidification heat transfer calculation in this continuous casting process, at least the physical property data (for example, solidification latent heat / thermal conductivity / specific heat) of the steel grade and the external heat removal conditions (inside the mold) It is necessary to accurately grasp calculation conditions such as heat removal at the heat / heat transfer coefficient by spray or mist cooling in the secondary cooling zone / heat transfer coefficient by roll cooling).
Among the above-mentioned calculation conditions, the ones that greatly affect the calculation results are: (1) (physical property data) solidification latent heat and (2) (external heat removal conditions) heat transfer coefficient / roll in the secondary cooling zone And a heat transfer coefficient by cooling.

  The former (1) solidification latent heat generally has a value of about 55 to 65 cal / g, but it is extremely difficult to accurately determine the solidification latent heat of steel containing many elements.

The heat transfer coefficient in the secondary cooling zone of the latter (2) is generally estimated based on experimental results of temperature changes when steel is cooled at a predetermined spray flow rate. ing.
However, it has been reported that the heat transfer coefficient of spray / mist cooling in the secondary cooling zone is expressed as a complicated function in which various parameters are linked (Mitsuka et al .: Iron and Steel, 69 (1983), 262. / Mitsuka: Iron and steel, 91 (2005), see 1). The parameters are, for example, spray flow rate / water droplet size and momentum / air amount and pressure / slab surface temperature.
And, even if these parameters are appropriately determined, the present condition is that the heat transfer coefficient varies greatly depending on the measurement conditions.
In addition, in the above experiment, (a) the difference in cooling capacity between the upper and lower surfaces of the slab, the change caused by the movement of the slab, (b) the effect of clogging of the immersion nozzle, (c) the accumulation between the guide rolls Naturally, it is impossible to estimate various effects that can occur in actual machines, such as the effects of water, (d) the effects of cooling from low-temperature rolls, and (e) the effects of slab oxidation (scale adhesion thickness).

As described in (1) and (2) above, as long as the calculation conditions for solidification heat transfer calculation include many uncertain factors, the solid phase ratio inside the slab is accurately predicted according to each steel type / casting condition. This is extremely difficult at present.
As a reference, an example of the calculation result of the solidification heat transfer calculation is shown in FIG. This figure is calculated by using the prediction formula described in the above-mentioned Mitsuka et al. Literature and setting the latent heat of solidification to 55 or 65 cal / g. In this figure, the solid line is calculated with the latent heat of solidification as 65 cal / g, and the broken line is calculated with 55 cal / g. As can be seen from the figure, in the present situation in which the latent heat of solidification is determined almost subjectively, as a result, a large shift of, for example, several m order occurs in the relationship between the solid phase ratio and the meniscus distance. is there. In addition, it is difficult to think that Mitsuka et al.'S prediction formula described above is suitable for all casting conditions, and depending on which prediction formula is used, there will be a large shift in the relationship between the solid phase ratio and the meniscus distance. Is easily guessed.

  Therefore, in the method disclosed in Patent Document 1 above, even the solid phase ratio, which is the setting criterion for the reduction condition, cannot be predicted with high accuracy, so whether the effect of reducing the center segregation is really a problem of probability. . In fact, it has been found that there is a large variation in the effect of reducing the center segregation, and it is extremely difficult to cast a good slab even if the steel type composition and operating conditions vary.

  In addition, although the said patent document 1 has described the point in which the light pressure lower belt is provided in the range of 20-32m from the molten steel surface in a mold, this description is that the light pressure lower belt was provided for the time being. It merely represents the facts, and no technically useful information has been newly disclosed (see paragraph 0034).

  The present invention has been made in view of such various points, and its main object is to provide a method for improving the center segregation of bearing steel that can reduce the center segregation based on the specific operating conditions dominant to the solidification rate. There is to do.

Means and effects for solving the problems

  The problems to be solved by the present invention are as described above. Next, means for solving the problems and the effects thereof will be described.

According to an aspect of the present invention, the C content C [wt%] is 0.93 to 1.10, the Si content Si [wt%] is 0.15 to 0.35, the Mn content Mn [wt%] is 0 to 0.50, Improvement of the center segregation of bearing steel with Cr content Cr [wt%] of 1.30 to 1.60 is performed by the following method.
The mold thickness D [mm] at the upper end of the mold is set to 350 to 410.
・ Casting speed Vc [m / min] is set to 0.50 to 0.65.
-Set the specific water amount Wt [L / kg _Steel ] to 0.25 to 1.00.
-The molten steel superheat degree ΔT [° C.] is set to 10 to 45.
-Roll gradient GRD [mm / m] in the 1st path | route part Int1 as a casting path | route whose meniscus distance M [m] is 10.0-22.3 shall be 0.0-5.0.
The roll gradient GRD [mm / m] in the second path portion Int2 as the casting path having the meniscus distance M [m] of 22.3 to 25.9 is set to 0.0 to 1.0.
-Roll gradient GRD [mm / m] in the 3rd path | route part Int3 as a casting path | route whose said meniscus distance M [m] is 25.9-27.5 shall be 1.0-2.0.
The roll gradient GRD [mm / m] in the fourth path portion Int4 as the casting path having the meniscus distance M [m] of 27.5 to 32.3 is set to 0.5 to 2.0.

  According to this, center segregation of bearing steel can be improved.

(Definition of terms: roll gradient GRD, roll gap G)
First, “roll gradient GRD [mm / m]” used in this specification is defined as follows. FIG. 1 is a schematic diagram for explaining the definition of the roll gradient.
That is, among a plurality of roll pairs arranged side by side along the casting path, an arbitrary roll pair, and a roll pair disposed adjacent to the downstream side of the casting path with respect to the roll pair, The roll gradient GRD _1-2 [mm / m] between the roll gap G ₁ [mm] of the former roll pair, the roll gap G ₂ [mm] of the latter roll pair, and the roll pitch L _{1− of} both roll pairs ₂ and the following formula.
GRD _1-2 = (G ₁ −G ₂ ) / L _1-2
The roll gap G [mm] is the shortest distance [mm] between the surfaces of both rolls provided with a pair of slabs.

(Definition of terms: Meniscus distance M)
Next, the definition of “meniscus distance M [m]” used in this specification will be described. In the present specification, the “meniscus distance M [m]” refers to the molten steel surface contained in a mold for cooling the poured molten steel to form a solidified shell of a predetermined shape. And the distance [m] to be considered along the casting path.

  Embodiments of the present invention will be described below.

  First, the continuous casting machine 100 used for the center segregation improving method for bearing steel according to the present embodiment will be outlined with reference to FIG. FIG. 2 is a schematic view of a continuous casting machine according to an embodiment of the present invention.

  As shown in the figure, in the present embodiment, the continuous casting machine 100 cools the molten steel to be poured to form a solidified shell having a predetermined shape, and pours molten steel into the mold 1 at a predetermined flow rate. The tundish (not shown) provided for this purpose, and a plurality of roll pairs 2, 2,... Arranged in parallel along the casting path from directly below the mold 1 are provided. In the present embodiment, the casting path is, in order from the upstream to the downstream, (1) an arc path portion having a predetermined arc radius and extending in an arc shape, and (2) on the downstream side of the arc path portion. A horizontal path portion provided in the horizontal direction, and (3) provided between the arc path portion and the horizontal path portion, and by smoothly increasing the arc radius, the arc path portion and the horizontal path portion are provided. And a straightening path portion that connects smoothly. In short, the continuous casting machine 100 according to the present embodiment is a so-called curved continuous casting machine.

  Further, each of the roll pairs 2, 2... Is composed of a pair of rolls 2a, 2a for holding a bearing steel as a casting object between both wide surfaces. The roll gap G (see FIG. 1) of the pair of rolls 2a and 2a is configured to be adjustable by appropriate means.

  Further, along the circular arc path portion, cooling sprays 4, 4... Spraying the cooling water at a predetermined flow rate on the solidified shell formed in the mold 1 and pulled out from the mold 1 are appropriately provided. Is provided. In general, the mold 1 is referred to as a primary cooling zone, and in this sense, a path portion in which the cooling sprays 4, 4,... Are provided is referred to as a secondary cooling zone.

  Further, the solidified shell pulled out from the mold 1 and conveyed along the casting path is further cooled and contracted by natural heat dissipation, the cooling sprays 4, 4. Accordingly, each of the roll gaps G of the roll pairs 2, 2,... Is generally adjusted so that it gradually becomes smaller (that is, narrower) as it goes downstream of the casting path. In other words, in principle, the roll gradient GRD is always set to be zero or more over the entire casting path.

  Next, the operation of the continuous casting machine 100 will be outlined.

1. Before starting the continuous casting of the bearing steel, a dummy bar (not shown) is appropriately inserted into the continuous casting machine 100 in advance.
2. Molten steel is poured from the tundish (not shown) into the mold 1 at a predetermined flow rate.
3. When a predetermined amount of molten steel is poured into the mold 1, the dummy bar is pulled out at a predetermined speed toward the downstream side of the casting path.
4). The dummy bar is recovered by an appropriate means at a predetermined meniscus distance, and the bearing steel starts to be continuously cast.

In this embodiment, the casting speed Vc [m / min] as the speed for casting the bearing steel is set to 0.50 to 0.65.
The mold thickness D [mm] at the upper end of the mold 1 is 350 to 410 (however, the aspect ratio determined by the mold thickness D [mm] and the mold width [mm] at the upper end of the mold 1 is 2). And below.)
Further, the so-called specific water amount Wt [L / kg _Steel ] as the amount of cooling water sprayed by the plurality of cooling sprays 4 · 4... Provided in the secondary cooling zone is set to 0.25 to 1.00. .
Also, the so-called molten steel superheat degree ΔT [° C.] is 10 to 45 (the definition and measurement method will be described later (Document 1)).
The so-called in-mold molten steel stirring strength M-EMS [gauss] is 600 to 800 (the definition and measurement method will be described later (Document 2)).

Next, the main components (main elements) of the bearing steel that is the subject of continuous casting in the present embodiment will be described in detail.
That is, the C content C [wt%] of the bearing steel is set to 0.93 to 1.10. The following is a brief description.
・ Si [wt%]: 0.15-0.35
・ Mn [wt%]: 0 to 0.50
・ Cr [wt%] ： 1.30 ～ 1.60

For reference, other components (additive elements) and characteristics of the bearing steel are briefly exemplified below.
・ Cu [wt%]: 0 ~ 0.50
→ Improve corrosion resistance and reduce toughness.
・ Al [wt%] ： 0 ～ 0.08
・ Ni [wt%] ： 0 ～ 1.0
→ Improves hardenability and suppresses low temperature embrittlement. Improve corrosion resistance. Residual austenite structure is generated to reduce the strength.
・ Mo [wt%] ： 0 ～ 0.60
→ Improves the yield strength after low-temperature annealing and reduces workability.
・ V [wt%]: 0 ~ 0.10
→ Improve toughness and decrease workability.
・ Nb [wt%]: 0 ~ 0.05
→ Improve toughness and decrease workability.
・ Ti [wt%] ： 0 ～ 0.10
→ Improve environmental resistance. Nitrides are deposited to reduce the lifetime.
・ B [wt%] ： 0 ～ 0.002
・ Ca [wt%] ： 0 ～ 0.002

For reference, other components (impurity elements) generally contained in this bearing steel are also introduced below.
・ P [wt%] ： 0 ～ 0.03
・ S [wt%] ： 0 ～ 0.015

  Next, with respect to the roll gradient GRD adjusted by appropriately setting the respective roll gaps G of the roll pairs 2, 2... Arranged in parallel along the casting path, FIG. Details will be described with reference to FIG.

That is, as shown by the hatched area in FIG. 3, in this embodiment, the roll gradient GRD [mm / m] in the first path portion Int1 as the casting path having the meniscus distance M [m] of 10.0 to 22.3 is 0.0 to 5.0.
Further, the roll gradient GRD [mm / m] in the second path portion Int2 as the casting path having the meniscus distance M [m] of 22.3 to 25.9 is set to 0.0 to 1.0.
The roll gradient GRD [mm / m] in the third path portion Int3 as the casting path having the meniscus distance M [m] of 25.9 to 27.5 is set to 1.0 to 2.0.
The roll gradient GRD [mm / m] in the fourth path portion Int4 as the casting path having the meniscus distance M [m] of 27.5 to 32.3 is set to 0.5 to 2.0.

  The roll gradient GRD [mm / m] in the first to fourth path portions Int1 to Int4 may be either constant or variable as long as it is within each numerical value range.

A specific setting example of the roll gradient GRD [mm / m] in the present embodiment is as shown in FIG. FIG. 4 is a diagram illustrating an example in which all the conditions regarding the roll gradient GRD [mm / m] according to the present embodiment are satisfied, and the thick line in the drawing indicates the roll gradient GRD at each meniscus distance M [m]. Represents the setting value of [mm / m].
In contrast to this, examples (comparative examples) in which all of the conditions regarding the roll gradient GRD [mm / m] are not satisfied are illustrated in FIGS. FIGS. 5-7 is a figure which shows the example which does not satisfy | fill all the conditions regarding the said roll gradient GRD [mm / m] in this embodiment, respectively.

  Next, how to set the roll gradient GRD [mm / m] in the present embodiment will be described in detail with reference to FIG. FIG. 8 is a diagram illustrating a method for setting a roll gradient.

  Here, as shown in the figure, regarding the setting method of the roll gradient GRD [mm / m] when the plurality of roll pairs 2, 2... Are rotatably supported by a roll stand for each predetermined pair. explain. In this case, it is preferable that the roll alignment of the plurality of rolls 2a, 2a,... Supported on one roll stand is as uniform as possible.

For the convenience of explanation, among the plurality of roll pairs 2, 2... Supported by the upstream roll stand in this figure, the most downstream roll pair 2 is referred to as a roll pair 2 _i and is also the downstream roll. The plurality of roll pairs 2 · 2 ··· supported by the stand are referred to as roll pairs 2 _{i + 1} , 2 _{i + 2} , ..., 2 _{i + j-1} , 2 _{i + j} . The number of pairs of rolls 2 · 2... (2 _{i + 1} to 2 _{i + j} ) supported by the downstream roll stand is n. That is, (i + j)-(i + 1) + 1 = n.
Similarly, for convenience of explanation, the meniscus distance M of each of the roll pairs 2 · 2... (2 _i , 2 _{i + j,} etc.) is attached to the sign of each roll pair 2 · 2. It shall be indicated with a subscript. For example, the meniscus length M of the pair of rolls 2 _i is denoted as meniscus distance M _i, meniscus distance M of the roll pair 2 _{i + j} is, referred to as meniscus distance M _{i + j.}

Hereinafter, the method of setting the roll gradient GRD will be described separately in STEP 1 and STEP 2 as shown in the figure. As an example, let us set a roll gradient GRD [mm / m] of a path portion in which the meniscus distance M [m] is M _{i to} M _{i + j} . It should be noted that the most downstream pair (roll pair 2 _i ) of the plurality of roll pairs 2, 2... Supported by the upstream roll stand is disposed at the meniscus distance M _i [m], and the downstream side It is assumed that the most downstream (roll pair 2 _{i + j} ) among a plurality of roll pairs 2 · 2... Supported by the roll stand is disposed at the meniscus distance M _{i + j} [m]. .

<STEP1: (1) to (3)>
(1) The roll gap G _i of the roll pair 2 _i arranged at the meniscus distance M _i [m] is measured.
Example: G _i [mm] = 376
(2) The distance (M _{i + j} −M _i ) [m] between the roll pair 2 _{i + j} arranged at the meniscus distance M _{i + j} [m] and the roll pair 2 _i is taking measurement.
Example: M _{i + j} −M _i [m] = 1.6
(3) The roll gap G _{i + j} of the roll pair 2 _{i + j} is obtained as shown in the following equation. Then, by moving at least one of the roll stands provided in a pair so as to sandwich the slab by an appropriate means, the obtained roll gap G _{i + j is set} to the roll pair 2 _{i + j} . It applies to.
G _{i + j} = G _i −GRD × (M _{i + j} −M _i )
Example: GRD [mm] = 1.1, G _{i + j} [mm] = 376−1.1 × 1.6 = 374.24

<STEP 2: (4) to (5)>
(4) The most upstream of the pair of rolls 2 _{i + j} arranged at the meniscus distance M _{i + j} [m] and the plurality of pairs of rolls 2, 2... Supported by the downstream roll stand. The distance (M _{i + j} −M _{i + 1} ) [m] between the roll pair 2 _{i + 1} is obtained.
Example: (M _{i + j} −M _{i + 1} ) [m] = 0.96
(5) As shown in the following equation, a roll gap G _{i + 1} to be applied to the roll pair 2 _{i + 1 is} obtained. Then, at least one of the roll stands provided in a pair so as to sandwich the slab is similarly moved and operated by an appropriate means, whereby the obtained roll gap G _{i + 1 is set} to the roll pair 2 _{i +} Applies to ₁ .
G _{i + 1} = G _{i + j} + GRD × (M _{i + j} −M _{i + 1} )
Example: G _{i + 1} [m] = 374.24 + 1.1 × 0.96 = 375.296

  Hereinafter, the test for confirming the technical effect of the center segregation improvement method of the bearing steel according to the present embodiment will be described. Each numerical range described above is reasonably supported by the following confirmation test.

  First, a method for evaluating a technical effect in each test will be described in detail with reference to the drawings. FIG. 9 is a diagram for explaining the procedure of the center segregation evaluation method.

<Summary of technical effect evaluation>
The object of this evaluation is the degree of center segregation of the slab. In particular, we focus on C segregation and Cr segregation. In the following (1) to (4), the evaluation method for C segregation will be described in detail, and in the following (5), the evaluation method for Cr segregation will be briefly described.

(1) Extraction of small slab That is, first, a portion of the slab is extracted from the cast slab by 250 mm in the casting direction. Secondly, a small slab is obtained by cutting a portion of the slab in parallel with the narrow surface so as to be halved in the slab width direction (see FIG. 9 upper).

(2) Collecting a chip sample Thirdly, a small slab obtained by the above-described cutting is drilled to collect a chip sample. Specifically, it is as follows (see the lower part of FIG. 9).
That is, the small slab obtained by the above cutting is along the casting direction on the center line in the thickness direction of the slab by using a φ5 mm drill blade from the “L section” in FIG. At a predetermined interval p (p = 10 mm), drilling is performed perpendicularly to the cross section at a predetermined depth dp (dp = 20 mm), and a total of 25 chips are collected.

(3) Component analysis Fourthly, each of the 25 chips samples obtained by the above drilling is subjected to component analysis by a predetermined component analysis method (for example, combustion infrared absorption method).
Fifth, the molten steel sample collected in advance from the above-mentioned tundish when casting the slab to be subjected to component analysis is subjected to component analysis by a predetermined component analysis method as in the case of the fourth.
In both the fourth and fifth component analyses, the C content C [wt%] of the sample is measured.

(4) Evaluation Sixthly, the C content C [wt%] of the chip sample having the highest C content C [wt%] among the plurality of chip samples collected from one small slab. ] Is recorded as Cmax [wt%].
Seventh, the ratio Cmax / Co obtained by dividing Cmax [wt%] recorded in the sixth by Co [wt%] as the C content C [wt%] obtained in the fifth is calculated. And record.
Eighth, the test in which the ratio Cmax / Co was 1.4 or less was evaluated as “◯ (small center segregation)”, and the same test exceeding 1.4 was evaluated as “× (center segregation remarkable)”.

(5) Cr segregation The C segregation evaluation methods described in the above (1) to (4) can be similarly applied to the above-described Cr segregation evaluation. However, the evaluation method for C segregation and the evaluation method for Cr segregation differ in the evaluation threshold.
That is, the ratio Cmax / Co as a parameter for evaluating C segregation was set to “1.4 or less is good”. On the other hand, the ratio Crmax / Cro as a parameter for evaluating Cr segregation is assumed to be “less than 1.5”.

  The method for evaluating the technical effect in each test has been described above. Next, the basis of the evaluation thresholds (C segregation: 1.4, Cr segregation: 1.5) described in (4) and (5) above will be described in detail in [A] to [D] below.

[A] The degree of central segregation is extremely important for the bearing steel, which is the target steel type of the present invention, as compared with other steel types such as SS400. This is because, depending on the degree of central segregation, the shape of the bearing roller is poor when it is formed.

[B] Generally, a slab as a bearing steel is formed into a bearing roller as a final product through the following steps (a) and (b).
(a) The bloom slab continuously cast by the above continuous casting machine 100 is heated to about 1200 to 1250 ° C. in a suitable soaking furnace and heating furnace, and then placed in a suitable split rolling facility. Then, it is rolled into a so-called billet having a cross section of 155 mm × 155 mm.
(b) The billet having a predetermined cross section obtained in the above (a) is cut into a predetermined dimension through a predetermined heating / rolling / heat treatment process, and formed into a bearing roller as a final product.

[C] <Cut surface evaluation test>
The “rolling” in the above (b) is performed step by step in several times. The steel material in one stage (φ19 mm) of the plurality of stages was evaluated as follows.
(a) That is, a steel material rolled to φ19 mm was shear-cut in a cold direction to a predetermined length in the longitudinal direction. A photograph of the cut surface obtained by the shear cutting is illustrated in FIG.
(b) The surface roughness Rz [μm] of the cut surface obtained in the above (a) (evaluated by the difference in height of the surface (cross section)) can be thought of as a diameter (indicated by the symbol di in FIG. 10). (This line passes through the center of the circular cross section.) Was measured using an appropriate surface roughness measuring device.
(c) A steel material having a surface roughness Rz [μm] obtained in (b) of less than 50 was accepted, and a steel material that was also 50 or more was rejected.

[D]
(a) The evaluation test related to the center segregation described above and the cut surface evaluation test (see item [C] above) were repeated about 100 times to investigate the relationship between them. 11 and 12 respectively show the ratio Cmax / Co or the ratio Crmax / Cro, which represents the degree of center segregation, as the horizontal axis, and the number of evaluations that failed as a result of the above-mentioned cut surface evaluation tests. The number of occurrences of cut surface defects (converted appropriately per ton of molten steel) is taken as the vertical axis.
(b) According to FIG. 11 and FIG. 12, when the ratio Cmax / Co is 1.4 or less and the ratio Crmax / Cro is 1.5 or less, the evaluation on the cut surface of a steel material having a diameter of 19 mm can be made extremely good. I understand.
(c) Based on the above consideration, the threshold values for the evaluation of C segregation and Cr segregation were set to 1.4 and 1.5, respectively, as described above.

  In the above, the evaluation method of the technical effect in each test and its basis were explained. Next, the test conditions of each test and the test results are shown in Table 1 below.

The test conditions for each test that are not described in Table 1 are as follows.
<Roll Pitch>: The roll pitch as the parallel spacing of the plurality of roll pairs 2... Arranged side by side along the casting path was 320 mm.
<Roll diameter>: The outer diameters of the rolls 2a, 2a constituting the roll pairs 2, 2,.
<Roll gradient in casting path not otherwise specified>: The roll gradient GRD [mm / m] in the path parts other than the first path part Int1 to the fourth path part is set to 0 to 0.25 unless otherwise specified.

As described above, in the above embodiment, the C content C [wt%] is 0.93 to 1.10, the Si content Si [wt%] is 0.15 to 0.35, and the Mn content Mn [wt%] is 0 to 0.50. The center segregation of the bearing steel with the Cr content Cr [wt%] of 1.30 to 1.60 is improved by the following method.
The mold thickness D [mm] at the upper end of the mold is set to 350 to 410.
・ Casting speed Vc [m / min] is set to 0.50 to 0.65.
-Set the specific water amount Wt [L / kg _Steel ] to 0.25 to 1.00.
-The molten steel superheat degree ΔT [° C.] is set to 10 to 45.
-Roll gradient GRD [mm / m] in the 1st path | route part Int1 as a casting path | route whose meniscus distance M [m] is 10.0-22.3 shall be 0.0-5.0.
The roll gradient GRD [mm / m] in the second path portion Int2 as the casting path having the meniscus distance M [m] of 22.3 to 25.9 is set to 0.0 to 1.0.
-Roll gradient GRD [mm / m] in the 3rd path | route part Int3 as a casting path | route whose said meniscus distance M [m] is 25.9-27.5 shall be 1.0-2.0.
The roll gradient GRD [mm / m] in the fourth path portion Int4 as the casting path having the meniscus distance M [m] of 27.5 to 32.3 is set to 0.5 to 2.0.

  According to this, the center segregation of the bearing steel can be improved (see Table 1 above).

From another point of view, the method for improving the center segregation of bearing steel according to the above embodiment can exhibit the following excellent effects as compared with the prior art.
In other words, the improvement of the above-mentioned center segregation does not use the central solid phase ratio that cannot be accurately determined due to calculation errors and operational variations, and is based on specific operating conditions (specific Is carried out based on the mold thickness D, the casting speed Vc, the specific water amount Wt, the meniscus distance M, and the roll reduction gradient GRD).
Therefore, it is not necessary to introduce expensive equipment for calculating the central solid fraction, advanced calculation techniques, and securing skilled personnel, and it can be carried out very easily in any existing continuous casting machine. . In addition, the reproducibility of the technical effect (stable appearance of the effect) is extremely high.

Here, please refer to FIGS. 14 to 17 so that the technical effect of the present invention related to the improvement of the center segregation can be understood more clearly. FIG. 14 and FIG. 16 are diagrams showing past results of C segregation or Si segregation in the applicant's ironworks. On the other hand, FIG.15 and FIG.17 is a figure which respectively shows the results of C segregation or Cr segregation in one Embodiment of this invention.
14 to 17 represents the degree of C segregation (Cmax / Co) (or the degree of Cr segregation (Crmax / Cro)), and the vertical axis represents the frequency. Here, the “frequency” specifically means that one sample is taken for one ladle (a molten steel capacity = 250 tons), and this is repeated a predetermined number of times, and the components of the collected multiple samples are collected. The analysis results are integrated for each degree of segregation.

  14 to 17, it can be easily understood that the technique according to the embodiment of the present invention exhibits a very useful effect in improving the center segregation as compared with the conventional technique.

<Document 1>
The measuring method of the above-mentioned molten steel superheat degree ΔT [° C.] will be described in detail in the following first and second.
That is, first, the temperature of the molten steel held in the above-described tundish (replaced and flowing in / out) is measured using an appropriate temperature measuring device.
(Example) This temperature measuring device includes, for example, a thermocouple type having a temperature sensing portion at the tip thereof, and in this case, the temperature sensing portion is inserted into the molten steel held in the tundish. The temperature of the molten steel is measured by immersing 50 mm or more. Since it is well known that thermocouples have the characteristic of raising and lowering the output voltage according to the temperature of the object to be measured, measuring the temperature of molten steel can be achieved by using appropriate means to measure the voltage output by the thermocouple. In other words, it can be read.
Secondly, the temperature of the molten steel measured in the first is compared with a so-called solidification start temperature that is uniquely determined by the molten steel component of the molten steel. And the above-mentioned molten steel superheat degree (DELTA) T [degreeC] can be calculated | required as the remainder which remove | excluded the latter from the former (it subtracted).

<Document 2>
A method for measuring the above-described molten steel stirring strength M-EMS [gauss] will be described.
That is, the electromagnetic stirring intensity M-EMS [gauss] in the mold is the center in the width direction of the mold 1, separated from the upper end of the mold 1 by 250 mm toward the lower end, and from the inner surface on the wide surface side of the mold. It shall be a value (unit: [gauss]) measured by an appropriate gauss meter at a point 15 mm away.

Schematic diagram for explaining the definition of roll gradient Schematic of a continuous casting machine according to an embodiment of the present invention Explanatory drawing of the roll gradient which concerns on one Embodiment of this invention The figure which shows the example which satisfy | fills all the conditions regarding the roll gradient which concern on one Embodiment of this invention. The figure which shows the example which has not satisfy | filled all the conditions regarding the roll gradient which concern on one Embodiment of this invention. The figure which shows the example which has not satisfy | filled all the conditions regarding the roll gradient which concern on one Embodiment of this invention. The figure which shows the example which has not satisfy | filled all the conditions regarding the roll gradient which concern on one Embodiment of this invention. The figure which illustrates one setting method of roll slope Diagram for explaining the procedure of the evaluation method for center segregation The figure which shows the photograph of the cut surface obtained by shear cutting of the steel material rolled to φ19mm Diagram showing the relationship between center segregation and the number of occurrences of cut surface defects Diagram showing the relationship between center segregation and the number of occurrences of cut surface defects Illustration of difficulty in calculating the central solid fraction Diagram showing the results of C segregation in the prior art The figure which shows the performance of C segregation in one Embodiment of this invention Diagram showing the results of Cr segregation in the prior art The figure which shows the track record of Cr segregation in one Embodiment of this invention

Explanation of symbols

M meniscus distance
GRD roll gradient

Claims (1)

C content C [wt%] is 0.93 to 1.10, Si content Si [wt%] is 0.15 to 0.35, Mn content Mn [wt%] is 0 to 0.50, Cr content Cr [wt%] In the method for improving the center segregation of bearing steel with 1.30 to 1.60,
The mold thickness D [mm] at the upper end of the mold is set to 350 to 410,
The casting speed Vc [m / min] is 0.50 to 0.65,
The specific water amount Wt [L / kg _Steel ] is 0.25 to 1.00,
The molten steel superheat degree ΔT [° C.] is 10 to 45,
Roll gradient GRD [mm] in the first path portion Int1 as a casting path having a meniscus distance M [m] of 10.0 to 22.3 starting from the molten steel surface poured into the mold. / m] is 0.0-5.0,
The roll gradient GRD [mm / m] in the second path portion Int2 as the casting path having the meniscus distance M [m] of 22.3 to 25.9 is set to 0.0 to 1.0,
The roll gradient GRD [mm / m] in the third path portion Int3 as the casting path having the meniscus distance M [m] of 25.9 to 27.5 is set to 1.0 to 2.0,
The roll gradient GRD [mm / m] in the fourth path portion Int4 as the casting path having the meniscus distance M [m] of 27.5 to 32.3 is set to 0.5 to 2.0.
For improving center segregation of bearing steel