WO2019184730A1 - 一种抑制柱状晶生长的连铸凝固过程控制方法 - Google Patents

一种抑制柱状晶生长的连铸凝固过程控制方法 Download PDF

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Publication number
WO2019184730A1
WO2019184730A1 PCT/CN2019/078325 CN2019078325W WO2019184730A1 WO 2019184730 A1 WO2019184730 A1 WO 2019184730A1 CN 2019078325 W CN2019078325 W CN 2019078325W WO 2019184730 A1 WO2019184730 A1 WO 2019184730A1
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continuous casting
exciting force
slab
force
columnar crystals
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PCT/CN2019/078325
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English (en)
French (fr)
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乌力平
沈昶
龚志翔
周寿好
陆强
臧红臣
张东浩
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马鞍山钢铁股份有限公司
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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
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • B22D11/114—Treating the molten metal by using agitating or vibrating means
    • 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
    • B22D11/20—Controlling or regulating processes or operations for removing cast stock
    • B22D11/207—Controlling or regulating processes or operations for removing cast stock responsive to thickness of solidified shell
    • 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
    • B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
    • 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

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  • the invention relates to the technical field of metallurgical continuous casting, and more particularly to a control method for continuous casting solidification process for inhibiting the growth of columnar crystals.
  • Electromagnetic stirring technology uses the principle of electromagnetic induction to generate an induced current inside the continuous casting billet. This current interacts with the magnetic field to generate electromagnetic force, which causes the molten metal to produce a unidirectional rotating flow and breaks the dendrites, which causes the broken crystal to generate more.
  • the crystal nucleus of the axial crystal thereby inhibiting the growth of the continuous casting slab dendrites during solidification, and at the same time expanding the equiaxed crystal ratio, and as a result, improving the quality of the slab.
  • the name of the invention is: a vibrating hammer device for continuous casting billet and its use method (application number: 201310412579.8, application date: 2013.09.11), in particular, a vibrating hammer device for continuous casting billet and its use method.
  • the vibrating hammer device for the continuous casting blank comprises a hammer head, a moving rod, a fixed holding mechanism and a power driving system, wherein the fixed holding mechanism is fixed in the middle and late regions where the casting blank solidifies, and the hammer head in the opposite direction passes the moving rod It is mounted on the fixed holding mechanism and spaced apart from the surface of the slab, and the moving rod is connected to the power drive system.
  • the vibration is transmitted to the core of the casting blank at the end of the thicker solidification of the shell, which is beneficial to crushing and refining the center equiaxed crystal, and effectively improving the center of the casting blank. Shrinkage and looseness; at the same time avoiding the occurrence of rolling cracks caused by solidification end casting.
  • the object of the invention is to improve the quality of the slab during the continuous casting process, and to provide a continuous casting solidification process control method for inhibiting the growth of columnar crystals, applying intermittent exciting force on the surface of the slab solidified shell, and exciting force
  • the metal liquid phase in the cross section of the slab at the point of application is 25% to 85%; the exciting force of the shell on the surface of the slab can regularly interrupt the dendrite head growing in the solidification front during cooling. Further, the growth of equiaxed crystals can be promoted, and the generation of negative segregation of the cast slab can be avoided or reduced.
  • the invention discloses a continuous casting solidification process control method for inhibiting columnar crystal growth, applying intermittent exciting force on the surface of the solidified shell of the continuous casting blank, and the molten metal in the cross section of the casting blank at the point of exciting force application
  • the phase ratio is 25% to 85%.
  • the excitation force is applied for a time interval of 1 to 30 seconds.
  • the impact energy applied by the exciting force ranges from 10 to 800 J.
  • b is the metal solid phase in the transverse section of the continuous casting slab at the action position Rate/%;
  • the value of the coefficient ⁇ of the continuous casting process of steel is 1.4 to 2.0, and the value of the coefficient ⁇ during the continuous casting of copper is 1.0 to 1.6;
  • S is the sectional area of the slab/mm 2 .
  • an exciting force is applied to both sides of the continuous casting slab.
  • the same exciting force is simultaneously applied at corresponding positions on both sides of the continuous casting blank.
  • At least one set of application points of the exciting force is provided on the surface of the solidified shell of the continuous casting billet along the longitudinal direction of the continuous casting billet.
  • a method for controlling a continuous casting solidification process for suppressing the growth of columnar crystals according to the present invention wherein an intermittent exciting force is applied to the surface of the solidified billet shell of the billet, and the metal in the cross section of the billet at the point of exciting force is applied
  • the liquid phase ratio is 25% to 85%; when the excitation force hits the shell of the slab surface, the dendrite head which grows at the solidification front during cooling can be regularly interrupted, and the broken dendrite head falls on the steel.
  • equiaxed crystals in water is a process in which columnar crystals are transformed into equiaxed crystals, without additionally increasing the relative relative displacement between the molten steel and the solidification front dendrites caused by the external field force, and inhibiting the liquid of the solute elements in the steel to the steel. Phase transfer, thereby preventing or reducing the occurrence of negative segregation of the slab while suppressing the growth of the columnar crystals and promoting the equiaxed crystal growth;
  • the time interval so as to avoid the continuous relative displacement between the molten steel and the solidification front dendrites caused by the excessive excitation frequency, so that the solute elements are continuously transferred into the liquid metal; the time interval for applying the exciting force can also be prevented from being too long.
  • the length of dendrite growth is too long, the number of broken dendrites is small, and the inhibition effect on columnar crystals is insufficient;
  • FIG. 1 is a schematic view of a control device for continuous casting solidification process for suppressing columnar crystal growth according to the present invention
  • FIG. 2 is a schematic view showing the microstructure of the slab of the embodiment 1;
  • FIG. 3 is a schematic view showing the morphology of the microstructure of the slab of Comparative Example 1.
  • the invention is a method for instantaneously hitting a billet shell of a slab surface by using an exciting force generating system for a certain position of the billet at a certain position and with a certain strength during the continuous casting production process of the steel, so that the exciting force passes through the billet.
  • the shell is transferred to the solidification front of the slab, periodically breaking the dendrite head growing at the solidification front, and suppressing the growth of the columnar crystal while providing the nucleus core for the subsequent formation of the central equiaxed crystal, without additionally increasing the external field force.
  • the continuous relative displacement between the molten steel and the dendrites at the solidification front inhibits the transfer of solute elements in the steel to the liquid phase of the steel, which can avoid or reduce the negative segregation of the cast slab.
  • the continuous casting blank 100 of the present invention comprises a concave side 101 of the casting blank, a convex arc side 102 and a circumferential side of the casting blank, the outer part of the continuous casting blank 100 is a solidified shell 120, and the inside of the solidified shell 120 is unsolidified molten steel 110;
  • a continuous casting solidification process control method for suppressing columnar crystal growth, applying intermittent exciting force on the surface of the solidified shell 120 of the continuous casting blank 100, and the molten metal in the cross section of the casting blank at the point of exciting force application The phase ratio is 25% to 85%, and the exciting force applying device 200 is provided at a position where the metal liquid phase ratio of the continuous casting blank 100 is 75% ⁇ b 2 > 25%, and the exciting force applying device 200 is used for the solidified billet An intermittent exciting force is applied to the surface of the shell 120 (as shown in FIG.
  • the direction of the exciting force is perpendicular to the surface of the shell of the continuous casting blank 100, and the exciting force is a single-direction intermittently applied striking force. , or a two-way intermittently applied striking force.
  • the solidified solid shell has a strength less than 85%, and does not have the external force to withstand the effective breaking of the dendritic head; when the metal liquid fraction is less than 25%, it is already at the end of solidification, continue The application of the exciting force has not been able to increase the equiaxed crystal ratio of the slab.
  • an exciting force to the slab concave side 101 of the slab 100 or the slab convex arc side 102 that is, the application position of the exciting force can be set to the concave side 101 of the slab or the convex side 102 of the slab;
  • the setting position of the exciting force may be located at each position on the circumferential side of the continuous casting blank 100; or an exciting force may be applied at a corresponding position of the concave side 101 of the continuous casting blank 100 and the convex side 102 of the casting blank.
  • the same exciting force is simultaneously applied to the corresponding positions of the concave side 101 of the continuous casting blank 100 and the convex side 102 of the casting blank.
  • At least a set of exciting force application points are provided on the surface of the solidified shell 120 of the continuous casting blank 100 along the longitudinal direction of the continuous casting billet 100, that is, at a metal liquid phase position of the continuous casting strand 100.
  • the one-side exciting force or the corresponding position on both sides simultaneously applies the exciting force to one set of exciting forces; and the plurality of exciting forces applied at different metal liquid phase positions of the continuous casting blank 100 are multiple sets of exciting forces.
  • a plurality of exciting force applying points may be disposed on the surface of the solidified shell 120 of the continuous casting blank 100 along the longitudinal direction of the continuous casting blank 100, and the molten metal in the cross section of the casting blank at each applied point The phase rates are not the same.
  • the excitation force is completely different from the vibration mode.
  • the intermittent excitation force is a single stroke to hit or knock on the surface of the solid shell at the end of the solidification.
  • the billet itself does not have relative displacement; It is a reciprocating sway or movement of the slab, the slab itself may have a relative displacement, and the vibration exerts a reciprocating force on the surface of the slab shell, so the intermittent exciting force is substantially different from the vibration;
  • the action mechanism is completely different. It is precisely because the excitation force and the vibration action mode are completely different.
  • the excitation force hits the billet shell on the surface of the slab, it can interrupt the dendrite head growing in the solidification front during cooling.
  • the columnar crystals are transformed into equiaxed crystals, and the continuous relative displacement between the molten steel and the solidification front dendrites caused by the external field force is not additionally increased, and the transfer of the solute elements in the steel to the liquid phase of the steel is inhibited; and the vibration is utilized by inertia.
  • the force plays a role in feeding and improving the looseness of the solidification structure of the metal.
  • the vibration will additionally increase the external field force and cause the continuous relative displacement between the molten steel and the dendrites at the solidification front, and promote the transfer of the solute elements in the steel to the liquid phase of the steel, resulting in Negative segregation of slabs.
  • the excitation force is applied for a time interval of 1-30 seconds. This is because the effect of the external force is close to a continuous action when the time is less than 1 second, resulting in a continuous relative displacement between the molten steel and the dendrites at the solidification front, causing the solute elements to continuously flow into the liquid state. In the metal transfer, negative segregation is easy to occur, and the breaking effect is also reduced due to the growth of the dendrites.
  • the time interval of the excitation force is too large, so that the length of dendrite growth is too long, the number of broken dendrites is small, and the inhibition effect on the columnar crystal is insufficient. It is worth noting that the time interval is related to the thickness of the shell of the action point.
  • T ⁇ ⁇ ⁇ ⁇ S, where T is time The interval / s, the coefficient ⁇ ranges from 0.4 to 0.8 s / mm 2 , and its specific value is related to the impact energy of the external force, the distribution of the action point, and the quantity.
  • ⁇ is the solid phase ratio of the metal in the transverse section of the slab at the action position, steel
  • the value of the coefficient ⁇ of the continuous casting process is 1.4 to 2.0, and the value of the coefficient ⁇ during the continuous casting process is 1.0 to 1.6.
  • the specific values are related to the elastic modulus, strength and continuous casting speed and section shape of different metal materials. It is the cross-sectional area of the slab / mm 2 .
  • the impact energy applied by the exciting force ranges from 10 to 800 J.
  • W is the impact energy of the external force / J
  • coefficient a The range is 0.2-2.6J/mm 3 , and its specific value is related to the distribution and quantity of the exciting force action point.
  • b is the metal liquid phase ratio in the transverse section of the casting blank at the working position.
  • the value of C in the continuous casting process of steel is 1.8.
  • the value of C in the continuous casting process is 1.0-1.6, and its specific value is related to the elastic modulus and strength of different metal materials and the cross-sectional shape of the continuous casting machine.
  • S is the cross-sectional area of the slab/mm 2 .
  • the dendrite head growing in the solidification front during cooling can be regularly interrupted, and the broken dendrite head falls in the molten steel and forms equiaxed crystals, and will not
  • the additional relative displacement between the molten steel and the solidification front dendrites caused by the external field force is additionally increased, which inhibits the transfer of solute elements in the steel to the liquid phase of the steel, thereby preventing columnar crystal growth and promoting equiaxed crystal growth while avoiding Or reduce the generation of negative segregation of the slab.
  • a 5-stream round billet continuous casting machine is used in a continuous casting process of a high carbon steel round billet, wherein the billet section has a diameter of 380 mm, and an exciting force is applied at a point of application of the inner side of the continuous casting billet 100.
  • This exciting force is an intermittent hitting force applied to the inner side surface of the continuous casting blank 100 by the compressed gas driving device, that is, an intermittent impact force is applied to the concave side 101 of the casting blank.
  • an exciting force is applied at a point of application, wherein the metal liquid phase ratio in the cross section of the slab at the point of application is 75%, and the equiaxed crystal ratio and negative segregation of the slab are analyzed after the casting, the specific parameters of the embodiment and The results are shown in Table 1.
  • the schematic diagram of the morphology of the low-magnification structure in which the metal liquid phase rate of the excitation force application point is 75% is shown in Fig. 2.
  • Comparative Example 1 The basic content of this comparative example is the same as that of Embodiment 1, except that no exciting force is applied to the surface of the continuous casting blank 100 during the continuous casting. After the casting, the equiaxed crystal ratio and the negative segregation of the slab were analyzed. The specific parameters and results of Comparative Example 1 are shown in Table 1. A schematic diagram of the morphology of the low-magnification structure of Comparative Example 1 is shown in FIG.
  • FIG. 2 is a schematic view showing the morphology of the microstructure of the slab of Example 1
  • FIG. 3 is a schematic view showing the microstructure of the slab of Comparative Example 1; Crystal region 310 and equiaxed crystal region 320. It can also be seen from the comparison of Fig. 2 and Fig. 3 that the slab of Example 1 significantly increases the equiaxed crystal ratio without causing negative segregation, and the effect is remarkable.
  • the equiaxed crystal ratio of the examples was 58.5%, which was much larger than the equiaxed crystal ratio of 38.2% of the comparative example.
  • the energy of the exciting force when the exciting force hits the blank shell on the surface of the slab, the energy of the exciting force can be instantaneously transmitted to the surface of the slab, and transmitted along the shell to the solidification front of the slab, and the exciting force can be regularly Interrupting the dendrite head growing in the solidification front during cooling, thereby effectively inhibiting the growth of columnar crystals; at the same time, the interrupted dendritic head falls in the molten steel and forms equiaxed crystals, which is the subsequent formation of the central equiaxed crystal.
  • a crystal nucleus is provided to convert the columnar crystal into an equiaxed crystal.
  • the exciting force is a regular and instantaneous action, there is no continuous relative displacement between the molten steel and the dendrites at the solidification front, which will not cause the solute element to transfer into the liquid metal, causing negative segregation of the slab, and the excitation force on the columnar stalk
  • the breaking ability of the crystal head is much higher than that of the electromagnetic force. In turn, the growth of equiaxed crystals is promoted, and the negative segregation of the cast strand can be avoided or reduced.
  • a 5-stream round billet continuous casting machine is used in a continuous casting process of a high carbon steel round billet, wherein the billet section has a diameter of 700 mm, and the casting blank of the continuous casting billet 100 has different concave sides 101.
  • the force point applies an exciting force which applies an intermittent striking force to the inner side surface of the continuous casting blank 100 using the compressed gas driving device.
  • the exciting force is applied at two different application points, wherein the metal liquid phase ratio in the cross section of the slab at the application point is 45% and 40%, respectively, and the equiaxed crystal ratio and negative segregation of the slab are analyzed after the casting is completed.
  • the specific parameters and results of Example 2 are shown in Table 2.
  • Example 2 From the analysis of Comparative Example 2 and Example 2, it was found that the equiaxed crystal ratio of Example 2 was 62.1%, which was much larger than the equiaxed crystal ratio of the comparative example of 45.6%.
  • the exciting force is applied to the continuous casting blank 100, but also the exciting force is applied simultaneously at a different point of application, thereby realizing the multi-stage excitation force hitting; the exciting force hits the blank shell on the surface of the casting blank Instantly transfer the energy of the exciting force to the surface of the slab and transfer it along the shell to the solidification front of the slab.
  • the exciting force can not only periodically interrupt the dendrite head growing at the solidification front, but also the two points of action. The action time and effect are different, which can fully promote the broken dendritic head falling in the molten steel, and form a uniform nucleation core, which promotes the growth of equiaxed crystals.
  • the basic content of this embodiment is the same as that of the first embodiment, except that the test is carried out on a slab continuous casting machine of a steel mill.
  • the force point position is applied with the same impact work symmetrical impact applying the exciting force, that is, the same exciting force is simultaneously applied to the corresponding positions of the concave side 101 of the continuous casting blank 100 and the convex side 102 of the casting blank.
  • two sets of experiments were carried out, and under the same conditions of the section of the cast slab, the experiments were carried out at different positions of the exciting force.
  • the vibration force the exciting force applied on both sides, promotes the excitation force to quickly transfer the ability to the solidification front, and the simultaneous excitation force on both sides promotes the cracking and breaking of the dendrite head, which can fully promote the breaking.
  • the dendrites fall in the molten steel and form a uniform nucleation core, which promotes the growth of equiaxed grains.
  • the basic content of this embodiment is the same as that of the first embodiment, except that the test is carried out on a slab continuous casting machine of a steel mill.
  • the slab projection of the continuous casting slab 100 is convex.
  • the arc side 102 applies an exciting force, and the experimental exciting force acting position, the acting time interval, and the magnitude of the impact work are shown in Table 4.
  • the equiaxed crystal ratio and the negative segregation of the slab were analyzed. The specific parameters and results of the examples are shown in Table 4.
  • the convex arc side 102 of the slab 100 is subjected to an exciting force, which promotes the exciting force to rapidly transfer the ability to the solidification front, promotes the cracking and breaking of the dendrite head, and promotes the broken branches.
  • the crystal head uniformly falls in the molten steel and forms a uniform nucleation core, which promotes the growth of equiaxed crystals.
  • the basic content of this embodiment is the same as that of the first embodiment, except that the test is carried out on a steel slab continuous casting machine, and is applied on the circumferential side of the continuous casting blank 100 during the continuous casting of the 2150 ⁇ 230 broken slab blank.
  • the circumferential side is the position of the non-casting concave concave side 101 or the convex arc side 102 of the casting blank, and the experimental exciting force acting position, the working time interval and the magnitude of the impact work provided are shown in Table 5.
  • the equiaxed crystal ratio and the negative segregation of the cast slab were analyzed. The specific parameters and results of the examples are shown in Table 5.
  • the exciting force is applied to the circumferential side of the continuous casting slab 100, which promotes the exciting force to rapidly transfer the ability to the solidification front.
  • the exciting force promotes the cracking and breaking of the dendrite head, and can fully promote the broken dendrites.
  • the head falls in the molten steel and forms a uniform nucleation core, which promotes the growth of equiaxed crystals.

Abstract

一种抑制柱状晶生长的连铸凝固过程控制方法，在连铸坯凝固坯壳的表面施加间歇性的激振力，激振力施力点处的铸坯横截面中金属液相率为25％～85％。激振力击打在铸坯表面坯壳时，可以打断冷却过程中凝固前沿生长的枝晶头，促使着柱状晶转化为等轴晶，不会额外增加外场力造成的钢液与凝固前沿枝晶间的持续相对位移，抑制了钢中溶质元素向钢液中转移，从而在抑制柱状晶生长、促进等轴晶生长的同时，可以避免或减少了铸坯负偏析的产生。

Description

一种抑制柱状晶生长的连铸凝固过程控制方法 技术领域
本发明涉及冶金连铸技术领域，更具体地说，涉及一种抑制柱状晶生长的连铸凝固过程控制方法。
背景技术
在钢铁连铸生产过程中，为改善铸坯的凝固结构，提高等轴晶率，减少铸坯中心区域的疏松和成分偏析，广泛采用以电磁搅拌为典型的施加外场力搅拌技术。电磁搅拌技术利用电磁感应原理，在连铸坯内部产生感应电流，此电流与磁场相互作用产生电磁力，使金属液产生单向的旋转流动而折断树枝晶，促使破碎的晶体生成更多的等轴晶的晶核，从而达到了抑制凝固过程中的连铸坯树枝晶的生长，同时扩大等轴晶率，结果改善铸坯质量。
但是采用该类方法由于持续对液态金属施加恒定或交变电磁力，在刷断柱状晶的枝晶头成为中心等轴晶晶核的同时，还使得液态金属与凝固前沿的枝晶持续发生相对运动，也就是液态金属对凝固前沿的不断冲刷，造成溶质元素不断向液态金属内转移，引起持续外场力作用区域铸坯内部严重的宏观负偏析，例如连续铸钢中的铸坯白亮带。一般地，如果出现负偏析带，往往相应不可避免地也会出现正偏析带。
经检索，发明创造的名称为：一种连铸坯用的震动锤装置及使用方法(申请号：201310412579.8，申请日：2013.09.11)，特别涉及一种连铸坯用的震动锤装置及使用方法。所述连铸坯用的震动锤装置，包括锤头、运动杆、固定把持机构以及动力驱动系统，其中，固定把持机构固定在铸坯凝固的中后期区域，位于相对方向的锤头通过运动杆安装在固定把持机构上并与铸坯的表面间隔一定距离，运动杆与动力驱动系统相连。由于采取了锤击的方式取代接触式振动，在坯壳较厚的凝固末期，震动被传入铸坯芯部的效果更好，有利于破碎和细化中心等轴晶，有效改善铸坯中心缩孔和疏松；同时避免了凝固末端铸轧所造成的轧制裂纹的产生。
发明内容
1.发明要解决的技术问题
本发明的目的在于提高连铸过程中的铸坯质量，提供一种抑制柱状晶生长的连铸凝固过程控制方法，在铸坯凝固坯壳的表面施加间歇性的激振力，且激振力施力点处的铸坯横截面中金属液相率为25％～85％；击打在铸坯表面坯壳的激振力，可以规律性地打断冷却过程中凝固前沿生长的枝晶头，进而可以促进等轴晶的生长，同时可以避免或减少了铸坯负偏析的产 生。
2.技术方案
为达到上述目的，本发明提供的技术方案为：
本发明的一种抑制柱状晶生长的连铸凝固过程控制方法，在连铸坯的凝固坯壳的表面施加间歇性的激振力，且激振力施力点处的铸坯横截面中金属液相率为25％～85％。本发明的激振力击打在铸坯表面坯壳时，可以打断冷却过程中凝固前沿生长的枝晶头，促使着柱状晶转化为等轴晶，同时不会额外增加外场力造成的钢液与凝固前沿枝晶间的持续相对位移，抑制了钢中溶质元素向钢的液相中转移，从而达到抑制柱状晶生长和促进等轴晶生长目的。
优选地，激振力施加的时间间隔为1-30秒。
优选地，激振力施加的冲击能范围为10～800J。
优选地，激振力施加的时间间隔为T，T＝ε×b τ×S，ε取值范围为0.4～0.8s/mm 2；b为作用位置处连铸坯横向截面中的金属固相率/％；钢铁连铸过程系数τ的值为1.4～2.0，铜连铸过程中系数τ的值为1.0～1.6；S为铸坯断面面积/mm 2。
优选地，激振力施加的冲击能范围为W，W＝a×(1-b) C×S 1.5，a取值范围为0.2～2.6J/mm 3，b为凝固中段激振力施力点位置的铸坯横向截面的金属液相率/％；钢铁连铸过程C的值为1.8～2.4，铜连铸过程中C的值为1.0～1.6；S为铸坯断面面积/mm 2。
优选地，在连铸坯对应的两侧面施加激振力。
优选地，在连铸坯两侧的对应位置同时施加相同的激振力。
优选地，沿着连铸坯液相线长度方向，在连铸坯的凝固坯壳的表面至少设置1组激振力的施力点。
3.有益效果
采用本发明提供的技术方案，与已有的公知技术相比，具有如下显著效果：
(1)本发明的一种抑制柱状晶生长的连铸凝固过程控制方法，在铸坯凝固坯壳的表面施加间歇性的激振力，且激振力施力点处的铸坯横截面中金属液相率为25％～85％；激振力击打在铸坯表面坯壳时，可以规律性地打断冷却过程中凝固前沿生长的枝晶头，被打断的枝晶头落在钢水中并形成等轴晶，是柱状晶转化为等轴晶的过程，同时不会额外增加外场力造成的钢液与凝固前沿枝晶间的持续相对位移，抑制了钢中溶质元素向钢的液相中转移，从而在抑制柱状晶生长、促进等轴晶生长的同时，可以避免或减少了铸坯负偏析的产生；
(2)本发明的一种抑制柱状晶生长的连铸凝固过程控制方法，激振力施力点处的铸坯横截面中金属液相率为25％～85％，使得凝固坯壳在能承受打击激振力的同时，可以将凝固前沿生长的枝晶头被打断，并促进等轴晶的生长；
(3)本发明的一种抑制柱状晶生长的连铸凝固过程控制方法，激振力施加的时间间隔为T，T＝ε×σ τ×S，ε的范围是0.4～0.8s/mm 2，σ为作用位置处铸坯横向截面中的金属固相率，钢铁连铸过程系数τ，S为铸坯断面面积/mm 2；可以根据连铸生产过程中的实际需要，调节激振力施加的时间间隔，从而避免激振力频率过高造成的钢液与凝固前沿枝晶间的持续相对位移，使得溶质元素不断向液态金属内转移；也可以避免激振力施加的时间间隔过长，使得枝晶生长的长度过长，破断枝晶头少，对柱状晶抑制效果不够；
(4)本发明的一种抑制柱状晶生长的连铸凝固过程控制方法，激振力施加的冲击能范围为W，W＝a×(1-b) C×S 1.5，系数a的范围是0.2～2.6J/mm 3，b为作用位置处铸坯横向截面中的金属液相率，S为铸坯断面面积/mm 2；从而可以根据厚度施加适宜的冲击能，既能避免坯壳变形施加低能量激振力，并且可以有效破断枝晶头，进而将凝固前沿生长的枝晶头被打断，并促进等轴晶的生长，同时可以避免或减少了铸坯负偏析的产生。
附图说明
图1为本发明的一种抑制柱状晶生长的连铸凝固过程控制装置示意图；
图2为实施例1的铸坯微观组织的形貌示意图；
图3为对比例1的铸坯微观组织的形貌示意图。
示意图中的标号说明：
100、连铸坯；110、未凝固钢水；120、凝固坯壳；101、铸坯凹弧侧；102、铸坯凸弧侧；
200、激振力施加装置；
310、柱状晶区；320、等轴晶区。
具体实施方式
为进一步了解本实用新型的内容，结合附图和实施例对本实用新型作详细描述。
本说明书附图所绘示的结构、比例、大小等，均仅用以配合说明书所揭示的内容，以供熟悉此技术的人士了解与阅读，并非用以限定本发明可实施的限定条件，故不具技术上的实质意义，任何结构的修饰、比例关系的改变或大小的调整，在不影响本发明所能产生的功效及所能达成的目的下，均应仍落在本发明所揭示的技术内容得能涵盖的范围内。同时，本说明书中所引用的如“上”、“下”、“左”、“右”、“中间”等用语，亦仅为便于叙述的明了，而非用以限定可实施的范围，其相对关系的改变或调整，在无实质变更技术内容下，当亦视为本发明可实施的范畴。
本发明是在钢铁连铸生产过程中，采用激振力发生系统对铸坯一定位置、每隔一定时间、用一定强度的外力瞬时击打铸坯表面坯壳的方法，使激振力通过坯壳传递到铸坯凝固前沿，周期性地破断凝固前沿生长的枝晶头，在抑制柱状晶生长的同时，为中心等轴晶的后续形成 提供晶核核心，同时不会额外增加外场力造成的钢液与凝固前沿枝晶间的持续相对位移，抑制了钢中溶质元素向钢的液相中转移，可以避免或减少了铸坯负偏析的产生。
本发明的连铸坯100包括铸坯凹弧侧101、铸坯凸弧侧102和周侧，连铸坯100的外部为凝固坯壳120，凝固坯壳120内部为未凝固钢水110；本发明的一种抑制柱状晶生长的连铸凝固过程控制方法，在连铸坯100的凝固坯壳120的表面施加间歇性的激振力，且激振力施力点处的铸坯横截面中金属液相率为25％～85％，在连铸坯100金属液相率为75％≥b 2>25％的位置处设置有激振力施加装置200，激振力施加装置200用于向凝固坯壳120表面施加间歇性的激振力(如图1所示)，激振力的施力方向垂直于连铸坯100的坯壳表面，该激振力力是单方向间歇性施加的打击力，或者双向间歇性同时施加的打击力。这是由于金属液相率高于85％时已凝固的坯壳强度不够，不具备承受有效破断枝晶头的外力击打的条件；金属液相率低于25％时已经处于凝固末端，继续施加激振力已经无法提高铸坯等轴晶比例。在连铸坯100的铸坯凹弧侧101或者铸坯凸弧侧102施加激振力，即可以将激振力的施加位置设置于铸坯凹弧侧101或者铸坯凸弧侧102；当然激振力的设置位置也可以位于连铸坯100的周侧各个位置处；或者在连铸坯100铸坯凹弧侧101和铸坯凸弧侧102的两侧面的对应位置施加激振力。在连铸坯100铸坯凹弧侧101和铸坯凸弧侧102的两侧面的对应位置同时施加相同的激振力。
沿着连铸坯100液相线长度方向，在连铸坯100的凝固坯壳120的表面至少设置1组激振力的施力点，即在连铸坯100的一个金属液相率位置施加的单侧激振力或者两侧面的对应位置同时施加激振力为1组激振力；在连铸坯100的不同金属液相率位置施加的多个激振力，则为多组激振力。即可沿着连铸坯100液相线长度方向，在连铸坯100的凝固坯壳120的表面设置多个激振力的施力点，且每个施力点处的铸坯横截面中金属液相率不相同。
此处说明施加的激振力与与简单意义上的振动完全不同，具体说明如下：
(1)激振力与振动的作用方式完全不同，其中间歇性激振力是单程单次对凝固末端的坯壳表面的击打或者敲击，铸坯自身并不会有相对位移；而振动是对铸坯的往复晃动或运动，铸坯本身可能会产生相对位移，而且振动对铸坯坯壳表面施加的是往复的作用力，因此间歇性激振力与振动有本质的区别；
(2)作用机理完全不同，正是由于激振力与振动的作用方式完全不同，激振力击打在铸坯表面坯壳时，可以打断冷却过程中凝固前沿生长的枝晶头，促使着柱状晶转化为等轴晶，同时不会额外增加外场力造成的钢液与凝固前沿枝晶间的持续相对位移，抑制了钢中溶质元素向钢的液相中转移；而振动是利用惯性力起到补缩和改善金属凝固组织疏松的问题，振动会额外增加外场力并引起的钢液与凝固前沿枝晶间的持续相对位移，促进钢中溶质元素向钢 的液相中转移，造成铸坯负偏析的产生。
因此，激振力与振动的作用原理、达到的效果、作用机理完全不同。
激振力施加的时间间隔为1-30秒，这是由于时间低于1秒时，外力的效果接近连续作用，造成钢液与凝固前沿枝晶间的持续相对位移，造成溶质元素不断向液态金属内转移，容易产生负偏析，破断效果也因枝晶来不及生长而降低；激振力时间间隔太大使得枝晶生长的长度过长，破断枝晶头少，对柱状晶抑制效果不够。值得注意的是，时间间隔与作用点坯壳厚度有关，坯壳薄时枝晶生长快，激振间隔要短，具体可用以下关系式表示：T＝ε×σ τ×S，其中T为时间间隔/s，系数ε的范围是0.4～0.8s/mm 2，其具体数值与外力的冲击能、作用点分布、数量有关，σ为作用位置处铸坯横向截面中的金属固相率，钢铁连铸过程系数τ的值为1.4～2.0，铜连铸过程中系数τ的值为1.0～1.6，其具体数值与不同金属材料的弹性模量、强度以及连铸拉速和断面形状有关，S为铸坯断面面积/mm 2。
激振力施加的冲击能范围为10～800J。具体取值与坯壳厚度(金属液相率)等因素有关，具体可用以下关系式表示：W＝a×(1-b) C×S 1.5，其中W为外力的冲击能/J，系数a的范围是0.2～2.6J/mm 3，其具体数值与激振力作用点分布和数量有关，b为作用位置处铸坯横向截面中的金属液相率，钢铁连铸过程C的值为1.8～2.4，铜连铸过程中C的值为1.0～1.6，其具体数值与不同金属材料的弹性模量、强度以及连铸机断面形状有关，S为铸坯断面面积/mm 2。当厚度较小时，恰当能量的激振力可以在避免坯壳变形的同时有效破断枝晶头；当厚度大时，恰当能量的激振力可以穿透坯壳表面，从而有效地破断枝晶头，使得激振力对连铸坯100打击时，可以规律性地打断冷却过程中凝固前沿生长的枝晶头，被打断的枝晶头落在钢水中并形成等轴晶，同时不会额外增加外场力造成的钢液与凝固前沿枝晶间的持续相对位移，抑制了钢中溶质元素向钢的液相中转移，从而在抑制柱状晶生长、促进等轴晶生长的同时，可以避免或减少了铸坯负偏析的产生。
实施例1
本实施例采用某厂5流圆坯连铸机，在高碳钢圆坯的连铸过程中，其中铸坯断面为直径为380mm，在连铸坯100的内侧面的施力点施加激振力，该激振力即为使用压缩气体驱动装置向连铸坯100的内侧面施加间歇性的击打力，即铸坯凹弧侧101施加间歇性的击打力。
本实施例在施力点施加激振力，其中施力点处的铸坯横截面中金属液相率分别为75％，浇铸结束后分析铸坯等轴晶率和负偏析情况，实施例具体参数及结果如表1所示。其中激振力施力点金属液相率为75％的低倍组织的形貌示意图如图2所示。
表1
Figure PCTCN2019078325-appb-000001
Figure PCTCN2019078325-appb-000002
对比例1
本对比例的基本内容同实施例1，其不同之处在于，在连铸的过程中不向连铸坯100表面施加激振力。浇铸结束后分析铸坯等轴晶率和负偏析情况，对比例1具体参数及结果如表1所示。对比例1的低倍组织的形貌示意图如图3所示。
通过对对比例1和实施例1的分析可以发现，图2为实施例1的铸坯微观组织的形貌示意图；图3为对比例1的铸坯微观组织的形貌示意图；图中包括柱状晶区310和等轴晶区320。从图2和图3的对比也可以发现，实施例1的铸坯在不产生负偏析的情况下，明显提高等轴晶率，效果明显。实施例的等轴晶率为58.5％，远远大于对比例38.2％的等轴晶率。实施例1由于激振力击打在铸坯表面坯壳时，可以瞬间将激振力的能量传递给铸坯表面，并沿着坯壳传递到铸坯凝固前沿，激振力可以规律性地打断冷却过程中凝固前沿生长的枝晶头，进而有效地抑制柱状晶生长；与此同时，被打断的枝晶头落在钢水中并形成等轴晶，为中心等轴晶的后续形成提供晶核，使得柱状晶转化为等轴晶。
由于激振力是间断有规律的瞬间作用，钢液与凝固前沿枝晶间没有的持续相对位移，不会造成溶质元素向液态金属内转移而引起铸坯负偏析，而且激振力对柱状晶枝晶头的破断能力大大高于电磁力。进而促进了等轴晶的生长，同时可以避免或减少了铸坯负偏析的产生。
实施例2
本实施例采用某厂5流圆坯连铸机，在高碳钢圆坯的连铸过程中，其中铸坯断面为直径为700mm，在连铸坯100的铸坯凹弧侧101不同的施力点施加激振力，该激振力即为使用压缩气体驱动装置向连铸坯100的内侧面施加间歇性的击打力。
本实施例在两个不同的施力点施加激振力，其中施力点处的铸坯横截面中金属液相率分别为45％和40％，浇铸结束后分析铸坯等轴晶率和负偏析情况，实施例2具体参数及结果如表2所示。
表2
Figure PCTCN2019078325-appb-000003
Figure PCTCN2019078325-appb-000004
对比例2
本对比例的基本内容同实施例2，其不同之处在于，在连铸的过程中不向连铸坯100表面施加激振力。浇铸结束后分析铸坯等轴晶率和负偏析情况，对比例2具体参数及结果如表2所示。
通过对对比例2和实施例2的分析可以发现，实施例2的等轴晶率为62.1％，远远大于对比例45.6％的等轴晶率。本实施例不仅在连铸坯100上施加激振力，而且在个不同的施力点同时施加激振力，实现了多段式的激振力击打；激振力击打在铸坯表面坯壳时，瞬间将激振力的能量传递给铸坯表面，并沿着坯壳传递到铸坯凝固前沿，激振力不仅可以规律性地打断凝固前沿生长的枝晶头，而且两个作用点的作用时间和作用有一定的区别，可以充分促进打碎的枝晶头落在钢水中，并形成均匀的形核核心，促进了等轴晶的生长。
实施例3
本实施例的基本内容同实施例1，不同之处在于：在某钢厂板坯连铸机上进行试验，在2150×230断面板坯的连铸过程中，在铸坯两侧面表面的一个施力点位置同时、使用相同冲击功对称冲击施加激振力，即在连铸坯100铸坯凹弧侧101和铸坯凸弧侧102的两侧面的对应位置同时施加相同的激振力。本实施例进行了2组实验，并在相同的铸坯断面条件下，在不同的激振力作用位置分别实验，每组实验的激振力作用位置、作用时间间隔和提供冲击功大小如表3所示。浇铸结束后分析铸坯等轴晶率和负偏析情况，实施例具体参数及结果如表3所示。
对比例3
本对比例的基本内容同实施例3，其不同之处在于，在连铸的过程中不向连铸坯100表面施加激振力。浇铸结束后分析铸坯等轴晶率和负偏析情况，对比例3具体参数及结果如表3所示。
表3
Figure PCTCN2019078325-appb-000005
由实施结果可以看出，通过本发明方案的实施，使用本发明的铸坯在不产生负偏析的情况下，明显提高等轴晶率，效果明显。通过对对比例3和实施例3的分析可以发现，实施例3的等轴晶率均大于35.7％，远大于对比例23.1％的等轴晶率。本实施例不仅在连铸坯100上施加激振力，而且在在铸坯两侧面表面的一个施力点位置同时、使用相同冲击功对称冲击施加激振力，实现了同一位置两侧同时施加激振力，两侧同时施加的激振力，促进了激振力迅速将能力传递至凝固前沿，并且两侧同时施加的激振力促进了枝晶头的破裂和打碎，可以充分促进打碎的枝晶头落在钢水中，并形成均匀的形核核心，促进了等轴晶的生长。
实施例4
本实施例的基本内容同实施例1，不同之处在于：在某钢厂板坯连铸机上进行试验，在2150×230断面板坯的连铸过程中，在连铸坯100的铸坯凸弧侧102施加激振力，实验的激振力作用位置、作用时间间隔和提供冲击功大小如表4所示。浇铸结束后分析铸坯等轴晶率和负偏析情况，实施例具体参数及结果如表4所示。
表4
Figure PCTCN2019078325-appb-000006
本实施例连铸坯100的铸坯凸弧侧102施加激振力，促进了激振力迅速将能力传递至凝固前沿，促进了枝晶头的破裂和打碎，可以促进被打碎的枝晶头均匀的落在钢水中，并形成均匀的形核核心，促进了等轴晶的生长。
实施例5
本实施例的基本内容同实施例1，不同之处在于：在某钢厂板坯连铸机上进行试验，在2150×230断面板坯的连铸过程中，在连铸坯100的周侧施加激振力，周侧为非铸坯凹弧侧101或者铸坯凸弧侧102的位置，实验的激振力作用位置、作用时间间隔和提供冲击功大小如表5所示。浇铸结束后分析铸坯等轴晶率和负偏析情况，实施例具体参数及结果如表5所示。
表5
Figure PCTCN2019078325-appb-000007
本实施例连铸坯100的周侧施加激振力，促进了激振力迅速将能力传递至凝固前沿，激 振力促进了枝晶头的破裂和打碎，可以充分促进打碎的枝晶头落在钢水中，并形成均匀的形核核心，促进了等轴晶的生长。
在上文中结合具体的示例性实施例详细描述了本发明。但是，应当理解，可在不脱离由所附权利要求限定的本发明的范围的情况下进行各种修改和变型。详细的描述和附图应仅被认为是说明性的，而不是限制性的，如果存在任何这样的修改和变型，那么它们都将落入在此描述的本发明的范围内。此外，背景技术旨在为了说明本技术的研发现状和意义，并不旨在限制本发明或本申请和本发明的应用领域。

Claims (8)

  1. 一种抑制柱状晶生长的连铸凝固过程控制方法，其特征在于：在连铸坯(100)的凝固坯壳的表面施加间歇性的激振力，且激振力施力点处的铸坯横截面中金属液相率为25％～85％。
  2. 根据权利要求1所述的一种抑制柱状晶生长的连铸凝固过程控制方法，其特征在于：激振力施加的时间间隔为1-30秒。
  3. 根据权利要求1所述的一种抑制柱状晶生长的连铸凝固过程控制方法，其特征在于：激振力施加的冲击能范围为10～800J。
  4. 根据权利要求1所述的一种抑制柱状晶生长的连铸凝固过程控制方法，其特征在于：激振力施加的时间间隔为T，T＝ε×b τ×S，
    ε取值范围为0.4～0.8s/mm 2；
    b为作用位置处连铸坯(100)横向截面中的金属固相率/％；
    钢铁连铸过程系数τ的值为1.4～2.0，铜连铸过程中系数τ的值为1.0～1.6；
    S为铸坯断面面积/mm 2。
  5. 根据权利要求1所述的一种抑制柱状晶生长的连铸凝固过程控制方法，其特征在于：激振力施加的冲击能范围为W，W＝a×(1-b) C×S 1.5，
    a取值范围为0.2～2.6J/mm 3，
    b为凝固中段激振力施力点位置的铸坯横向截面的金属液相率/％；
    钢铁连铸过程C的值为1.8～2.4，铜连铸过程中C的值为1.0～1.6；
    S为铸坯断面面积/mm 2。
  6. 根据权利要求4所述的一种抑制柱状晶生长的连铸凝固过程控制方法，其特征在于：在连铸坯(100)对应的两侧面施加激振力。
  7. 根据权利要求6所述的一种抑制柱状晶生长的连铸凝固过程控制方法，其特征在于：在连铸坯(100)两侧的对应位置同时施加相同的激振力。
  8. 根据权利要求1-7任一项所述的一种抑制柱状晶生长的连铸凝固过程控制方法，其特征在于：沿着连铸坯(100)液相线长度方向，在连铸坯(100)的凝固坯壳的表面至少设置1组激振力的施力点。
PCT/CN2019/078325 2018-03-29 2019-03-15 一种抑制柱状晶生长的连铸凝固过程控制方法 WO2019184730A1 (zh)

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