CN117463965A - Segregation control process for high-carbon steel continuous casting blank - Google Patents
Segregation control process for high-carbon steel continuous casting blank Download PDFInfo
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- 238000009749 continuous casting Methods 0.000 title claims abstract description 106
- 229910000677 High-carbon steel Inorganic materials 0.000 title claims abstract description 103
- 238000005204 segregation Methods 0.000 title claims abstract description 78
- 238000000034 method Methods 0.000 title claims abstract description 53
- 230000008569 process Effects 0.000 title claims abstract description 48
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 202
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
- B22D11/225—Controlling or regulating processes or operations for cooling cast stock or mould for secondary cooling
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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
- B22D11/115—Treating the molten metal by using agitating or vibrating means by using magnetic fields
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/122—Accessories for subsequent treating or working cast stock in situ using magnetic fields
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/18—Controlling or regulating processes or operations for pouring
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/20—Controlling or regulating processes or operations for removing cast stock
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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Abstract
The application relates to the technical field of high-carbon steel continuous casting processes, and particularly discloses a high-carbon steel continuous casting blank segregation control process. The high-carbon steel continuous casting blank segregation control process comprises the following steps: primary cooling is carried out on molten steel, a crystallizer is arranged for electromagnetic stirring and continuous stirring to drive the molten steel to rotate, and a primary cooling blank with a steel shell formed on the surface is prepared; drawing the formed primary cooling blank at a constant speed, and performing secondary cooling on the obtained primary cooling blank to form a secondary cooling blank; the secondary cooling molten steel is subjected to secondary cooling electromagnetic stirring to form a high-carbon steel continuous casting blank, and the secondary cooling electromagnetic stirring device has the advantages of reducing carbon center segregation and shrinkage cavity of the high-carbon steel continuous casting blank and reducing the possibility of fracture.
Description
Technical Field
The application relates to the technical field of high-carbon steel continuous casting processes, in particular to a high-carbon steel continuous casting blank segregation control process.
Background
The high-carbon steel continuous casting billet generally refers to a product obtained by casting molten steel with carbon content of 0.6-1.7% through a continuous casting machine, wherein the molten steel is smelted through a steelmaking furnace. The common high-carbon steel continuous casting billet preparation process is that a ladle filled with refined molten steel is transported to a rotary table, the rotary table rotates to a pouring position, the molten steel is injected into a tundish, the tundish distributes the molten steel into each crystallizer, the crystallizer enables castings to be molded and rapidly solidified and crystallized, the castings in the crystallizer are pulled out through a withdrawal and straightening machine, and the high-carbon steel continuous casting billet is formed after cooling.
The high-carbon steel continuous casting blank is easy to generate defects such as carbon center segregation, looseness, shrinkage cavity and the like in the continuous casting process, so that a network cementite precipitated along a grain boundary is easy to form, the network cementite breaks grains in the wire drawing and stranded wire process, the binding force among the grains is weakened, and the high-carbon steel continuous casting blank is broken in the wire drawing process, so that the quality of the high-carbon steel continuous casting blank is influenced.
Disclosure of Invention
In order to reduce the carbon center segregation and shrinkage cavity of the high-carbon steel continuous casting blank and reduce the possibility of fracture, the application provides a high-carbon steel continuous casting blank segregation control process.
The high-carbon steel continuous casting blank segregation control process adopts the following technical scheme:
the high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel, a crystallizer is arranged for electromagnetic stirring and continuous stirring to drive the molten steel to rotate, and a primary cooling blank with a steel shell formed on the surface is prepared;
drawing the formed primary cooling blank at a constant speed, and performing secondary cooling on the obtained primary cooling blank to form a secondary cooling blank; and carrying out secondary cooling electromagnetic stirring on the secondary cooled molten steel to form a high-carbon steel continuous casting blank.
Through adopting above-mentioned technical scheme, cool down the molten steel through once cooling, simultaneously the crystallizer electromagnetic stirring drives the molten steel rotation, thereby make the composition in the molten steel rotate along with the molten steel and evenly distributed in the molten steel, be convenient for the inclusion come-up, reduce the production of subcutaneous inclusion, gas pocket and pinhole, simultaneously reduce the possibility of the enrichment segregation of high carbon steel continuous casting center that elements such as C, mn, cr are made, and the molten steel surface forms the steel shell at this moment, the pulling force drives the primary cooling base and removes, the secondary cooling is carried out to the primary cooling base at this moment, make the molten steel in the steel shell further cool down, until forming the secondary cooling base, the solidification terminal electromagnetic stirring drives the liquid core in the steel shell at this moment and rotates, thereby make the composition evenly distributed in the liquid core, reduce center shrinkage cavity and center segregation's circumstances production, and then reduce the possibility of fracture.
Preferably, the superheat degree of the molten steel is (20+/-5) DEG C.
By adopting the technical scheme, the superheat degree of molten steel is controlled to be between 15 and 25 ℃, a steel shell is formed on the surface of the molten steel during primary cooling, and the molten steel in the steel shell is not solidified at the moment, so that the superheat degree is reduced as much as possible under the condition that the molten steel is not solidified completely too early, the growth of columnar crystals in the prepared high-carbon steel continuous casting blank is reduced, and the possibility of center segregation of the prepared high-carbon steel continuous casting blank is further reduced; when the overheat is less than 15 ℃, the fluidity of the molten steel is reduced and the molten steel starts to change to a solid phase, so that adverse effect is caused on pouring, inclusions in the molten steel are difficult to float up completely, and the quality of the prepared high-carbon steel continuous casting blank is influenced; when the overheat is higher than 25 ℃, columnar crystals grow in the process of converting molten steel into solid phase and are easy to cause center segregation, and the overheat is too high to enable a steel shell formed when the molten steel moves to a primary cooling position to be thinner, so that the situation that the molten steel is difficult to bear the internal stress of the molten steel to crack is easy to generate, and the quality of the prepared high-carbon steel continuous casting blank is influenced.
Preferably, the pull rate is 1.75X10 -2 m/s。
By adopting the technical scheme, the ratio of 1.75X10 -2 The steel shell formed by the drawing speed driving of m/s drives the non-solidified molten steel in the steel shell to move to the secondary cooling area and pass through the secondary cooling area, at the moment, the steel shell drives the non-solidified molten steel in the steel shell to pass through the secondary cooling area at a uniform speed, the molten steel in the steel shell is gradually solidified near the center of the steel shell, the possibility of liquid cavity elongation is reduced, the reduction of solidification bridging is facilitated, V-shaped segregation and center segregation are improved, the constant drawing speed enables the positions of solidification ends of the produced high-carbon steel continuous casting blank to be approximately the same, the possibility that the positions of the solidification ends are difficult to determine due to frequent change of the drawing speed is reduced, so that the solidification ends are convenient to electromagnetically stir and drive a liquid core in the steel shell to rotate, components in the liquid core are uniformly distributed, and the possibility of center segregation is further reduced; when the pulling speed is greater than 1.75X10 -2 In m/s, the liquid phase pit of the prepared high-carbon steel continuous casting blank is prolonged, a solidification bridge and a central shrinkage cavity are easy to form, and further the possibility of fracture of the prepared high-carbon steel continuous casting blank is easy to cause, so that the quality is influenced.
Preferably, the secondary cooling electromagnetic stirring adopts a solidification end electromagnetic stirring mode, and the central magnetic field intensity of the stirring coil is (765+/-15) multiplied by 10 -4 T。
Through adopting above-mentioned technical scheme, the steel shell that forms drives the inside unset molten steel of steel shell and is close to and pass the secondary cooling district under the drive of pulling force, and the secondary cooling makes the liquid core in the steel shell solidify gradually this moment, and solidifies terminal electromagnetic stirring and make unset molten steel in the steel shell rotate to further make the component evenly distributed in the molten steel, reduce the possibility of component segregation in the molten steel solidification process, thereby reduce the high carbon steel continuous casting blank center shrinkage cavity and the possibility of center segregation that make, further reduce the possibility of high carbon steel continuous casting blank fracture.
Preferably, the electromagnetic stirring at the solidification end adopts an alternate stirring mode, and the stirring mode is specifically that the molten steel is driven to rotate for 10 seconds along a certain hour, then the molten steel stops for 3 seconds, and the molten steel is driven to reversely rotate for 10 seconds again.
By adopting the technical scheme, the unset molten steel in the steel shell is driven to rotate, so that components in the molten steel are difficult to selectively segregate in the crystallization process, the possibility of enrichment of the components in the molten steel at the crystallization tail end is further reduced, the molten steel is driven to rotate forwards and then stop, the inertia of the molten steel in the forward rotation gradually disappears, and the molten steel is driven to rotate backwards at the moment, so that the impact of the molten steel on the inner side wall of the steel shell is reduced while the molten steel is driven to rotate and the components in the molten steel are uniform, and the possibility of fracture of a high-carbon steel continuous casting billet is further reduced; when the molten steel in the steel shell is driven to always rotate in the same direction, the unset molten steel washes the inner side wall of the steel shell under the action of centrifugal force, so that the possibility of cracking the steel shell is easily caused, and the quality of the prepared high-carbon steel continuous casting blank is influenced; when the mode of immediately reversing after forward rotation is adopted, after the molten steel is driven to forward rotate and when the molten steel is driven to reversely rotate, the molten steel is driven to forward rotate under the action of inertia, and meanwhile, the molten steel is subjected to the force of reverse rotation, so that the molten steel is easy to impact the side wall of the steel shell under the combined action of the inertia and the reverse force, the possibility of cracking of the steel shell is easy to be caused, and the quality of the prepared high-carbon steel continuous casting billet is influenced.
Preferably, the solidification end electromagnetic stirring position is 9.75m from the crystallizer meniscus.
By adopting the technical scheme, the pulling speed is determined to be 1.75X10 -2 On the basis of m/s, the electromagnetic stirring of the solidification end is arranged at a position 9.75m away from the meniscus of the crystallizer, so that the width of a pasty area in the steel billet is convenient for the electromagnetic stirring of the solidification end to stir a liquid core; when the distance between the electromagnetic stirring at the solidification end and the meniscus of the crystallizer is more than 9.75m, the width of the pasty area corresponding to the position of the electromagnetic stirring at the solidification end is smaller, the electromagnetic stirring at the solidification end is difficult to stir the liquid core, and further the possibility of component segregation in the liquid core is difficult to be inhibited, so that the quality of the prepared high-carbon steel continuous casting blank is influenced.
Preferably, the secondary cooling mode is aerosol cooling, the cooling medium is compressed air and water, and the specific water content of the primary cooling is 0.6L/kg of steel.
Through adopting above-mentioned technical scheme, spray compressed air and water smoke simultaneously on the steel shell surface that forms, it is effectual to heat transfer, is convenient for evenly cool down to once cooling base, reduces the uneven possibility of steel shell surface cooling, and water-saving simultaneously reduces the local quenching in steel shell surface and produces the condition of fracture and subcutaneous crackle when adopting the mode that water sprayed, reduces the impact of rivers to the steel shell surface simultaneously, reduces the high carbon steel continuous casting base fracture of making to the possibility.
In summary, the present application has the following beneficial effects:
1. the molten steel is cooled through primary cooling, and simultaneously the crystallizer is electromagnetically stirred to drive the molten steel to rotate, so that components in the molten steel rotate along with the molten steel and are uniformly distributed in the molten steel, the occurrence of shrinkage cavities on the surface of a prepared high-carbon steel continuous casting billet is reduced, meanwhile, the possibility of enrichment segregation of elements such as C, mn, cr and the like in the prepared high-carbon steel continuous casting center is reduced, a steel shell is formed on the surface of the molten steel, the primary cooling billet is driven to move through pulling force, the primary cooling billet is subjected to secondary cooling until the molten steel in the steel shell is further cooled, the secondary cooling billet is formed, and the solidification tail end is electromagnetically stirred to drive a liquid core in the steel shell to rotate, so that the components in the liquid core are uniformly distributed, the occurrence of center shrinkage cavities and center segregation is reduced, and the possibility of fracture is further reduced.
2. The superheat degree of the molten steel is controlled to be between 15 and 30 ℃, so that a steel shell is formed on the surface of the molten steel during primary cooling, and the molten steel in the steel shell is not solidified at the moment, so that the superheat degree is reduced as much as possible under the condition that the molten steel is not solidified completely too early, the growth of columnar crystals in the prepared high-carbon steel continuous casting blank is reduced, and the possibility of center segregation of the prepared high-carbon steel continuous casting blank is further reduced.
3. At a pull rate of 1.75X10 -2 On the basis of m/s, the electromagnetic stirring of the solidification end is arranged at a position 9.75m away from the meniscus of the crystallizer, so that the width of a pasty area in the steel billet is convenient for the electromagnetic stirring of the solidification end to stir a liquid core; when the distance between the electromagnetic stirring at the solidification end and the meniscus of the crystallizer is more than 9.75m, the width of the pasty area corresponding to the position of the electromagnetic stirring at the solidification end is smaller, and the electromagnetic stirring at the solidification end is difficult to stir the liquid core, so that the liquid core is difficult to stirSo as to inhibit the possibility of component segregation in the liquid core and influence the quality of the prepared high-carbon steel continuous casting billet.
Drawings
FIG. 1 is a line graph of average-difference value of carbon segregation of a sample of a high carbon steel continuous casting billet in example 1.11 of the present application.
FIG. 2 is a line graph of mean-to-maximum value of manganese segregation for a sample of high carbon steel continuous casting in example 1.11 of the present application.
FIG. 3 is a line graph of average-difference chromium segregation values for samples of high carbon steel continuous casting in example 1.11 of the present application.
Detailed Description
The present application is described in further detail below with reference to the drawings and examples.
Examples
Example 1
Example 1.1
Example 1.11
The high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel with the superheat degree of 20 ℃, and the molten steel is driven to rotate by electromagnetic stirring and continuous stirring of a crystallizer with the current of 450A and the frequency of 3Hz, so as to prepare a primary cooling blank with a steel shell formed on the surface;
for the primary cooling blank formed, the temperature was 1.75X10 -2 Drawing at a constant drawing speed of m/s, and performing secondary cooling on the prepared primary cooling blank in an aerosol cooling mode, wherein the specific water quantity is 0.6L/kg of steel, so as to form a secondary cooling blank;
the electromagnetic stirring position of the solidification end is adopted to be 9.75m from the meniscus of the crystallizer, and the magnetic field strength is 765 multiplied by 10 -4 And (3) performing secondary cooling electromagnetic stirring on the secondarily cooled molten steel in an electromagnetic stirring mode at the solidification tail end of the T, wherein the stirring mode is to drive the molten steel to rotate clockwise for 10s, stop for 3s, drive the molten steel to rotate anticlockwise for 10s again, stop for 3s, and drive the molten steel to rotate continuously in this mode to form the high-carbon steel continuous casting blank.
Example 1.12
Unlike example 1.11, the superheat degree of the molten steel was 30 ℃.
Example 1.13
Unlike example 1.11, the superheat degree of the molten steel was 10 ℃.
Example 1.14
Unlike example 1.11, the solidification end electromagnetic stirring position is 11.1m from the crystallizer meniscus.
Example 1.15
Unlike example 1.14, the pull rate was 1.35×10 -2 m/s。
Example 1.2
The high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel with the superheat degree of 20 ℃, and the molten steel is driven to rotate by electromagnetic stirring and continuous stirring of a crystallizer with the current of 450A and the frequency of 3Hz, so as to prepare a primary cooling blank with a steel shell formed on the surface;
for the primary cooling blank formed, the temperature was 1.75X10 -2 Drawing at a constant drawing speed of m/s, and performing secondary cooling on the prepared primary cooling blank in an aerosol cooling mode, wherein the specific water quantity is 0.6L/kg of steel, so as to form a secondary cooling blank;
the electromagnetic stirring position of the solidification end is adopted to be 9.75m from the meniscus of the crystallizer, and the magnetic field strength is 765 multiplied by 10 -4 And (3) carrying out secondary cooling electromagnetic stirring on the secondarily cooled molten steel in an electromagnetic stirring mode at the solidification tail end of the T, wherein the stirring mode is to drive the molten steel to rotate clockwise for 10s and then drive the molten steel to rotate anticlockwise for 10s, so that the molten steel is driven to rotate continuously in the mode, and a high-carbon steel continuous casting blank is formed.
Example 1.3
The high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel with the superheat degree of 20 ℃, and the molten steel is driven to rotate by electromagnetic stirring and continuous stirring of a crystallizer with the current of 450A and the frequency of 3Hz, so as to prepare a primary cooling blank with a steel shell formed on the surface;
for the primary cooling blank formed, the temperature was 1.75X10 -2 Drawing at a constant drawing speed of m/s, and performing secondary cooling on the prepared primary cooling blank in an aerosol cooling mode, wherein the specific water quantity is 0.6L/kg of steel, so as to form a secondary cooling blank;
crystallizer adopting electromagnetic stirring position distance of solidification tail endMeniscus 9.75m with a magnetic field strength of 765×10 -4 And (3) carrying out secondary cooling electromagnetic stirring on the secondarily cooled molten steel in a solidification tail end electromagnetic stirring mode, wherein the stirring mode is to drive the molten steel to continuously rotate along a single mode, so as to form a high-carbon steel continuous casting blank.
Example 2
Example 2.1
The high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel with the superheat degree of 20 ℃, and the molten steel is driven to rotate by electromagnetic stirring and continuous stirring of a crystallizer with the current of 450A and the frequency of 3Hz, so as to prepare a primary cooling blank with a steel shell formed on the surface;
for the primary cooling blank formed, the temperature was 1.75X10 -2 Drawing at a constant drawing speed of m/s, and performing secondary cooling on the prepared primary cooling blank in a water cooling mode, wherein the specific water quantity is 0.6L/kg of steel, so as to form a secondary cooling blank;
the electromagnetic stirring position of the solidification end is adopted to be 9.75m from the meniscus of the crystallizer, and the magnetic field strength is 765 multiplied by 10 -4 And (3) performing secondary cooling electromagnetic stirring on the secondarily cooled molten steel in an electromagnetic stirring mode at the solidification tail end of the T, wherein the stirring mode is to drive the molten steel to rotate clockwise for 10s, stop for 3s, drive the molten steel to rotate anticlockwise for 10s again, stop for 3s, and drive the molten steel to rotate continuously in this mode to form the high-carbon steel continuous casting blank.
Example 2.2
The high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel with the superheat degree of 20 ℃, and the molten steel is driven to rotate by electromagnetic stirring and continuous stirring of a crystallizer with the current of 450A and the frequency of 3Hz, so as to prepare a primary cooling blank with a steel shell formed on the surface;
for the primary cooling blank formed, the temperature was 1.75X10 -2 Drawing at a constant drawing speed of m/s, and performing secondary cooling on the prepared primary cooling blank in a water cooling mode, wherein the specific water quantity is 0.6L/kg of steel, so as to form a secondary cooling blank;
the electromagnetic stirring position of the solidification end is adopted to be 9.75m from the meniscus of the crystallizer, and the magnetic field strength is 765 multiplied by 10 -4 T solidification end electromagnetic stirringThe secondary cooling molten steel is subjected to secondary cooling electromagnetic stirring in a way that the molten steel is driven to rotate clockwise for 10s and then is driven to rotate anticlockwise for 10s, so that the molten steel is driven to rotate continuously to form a high-carbon steel continuous casting blank.
Example 2.3
The high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel with the superheat degree of 20 ℃, and the molten steel is driven to rotate by electromagnetic stirring and continuous stirring of a crystallizer with the current of 450A and the frequency of 3Hz, so as to prepare a primary cooling blank with a steel shell formed on the surface;
for the primary cooling blank formed, the temperature was 1.75X10 -2 Drawing at a constant drawing speed of m/s, and performing secondary cooling on the prepared primary cooling blank in a water cooling mode, wherein the specific water quantity is 0.6L/kg of steel, so as to form a secondary cooling blank;
the electromagnetic stirring position of the solidification end is adopted to be 9.75m from the meniscus of the crystallizer, and the magnetic field strength is 765 multiplied by 10 -4 And (3) carrying out secondary cooling electromagnetic stirring on the secondarily cooled molten steel in a solidification tail end electromagnetic stirring mode, wherein the stirring mode is to drive the molten steel to continuously rotate along a single mode, so as to form a high-carbon steel continuous casting blank.
Comparative example
Comparative example 1
The high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel with the superheat degree of 20 ℃, and the molten steel is driven to rotate by electromagnetic stirring and continuous stirring of a crystallizer with the current of 450A and the frequency of 3Hz, so as to prepare a primary cooling blank with a steel shell formed on the surface;
for the primary cooling blank formed, the temperature was 1.75X10 -2 Drawing at a constant drawing speed of m/s, and performing secondary cooling on the prepared primary cooling blank by adopting an aerosol cooling mode, wherein the specific water quantity is 0.6L/kg of steel, so as to form the high-carbon steel continuous casting blank.
Comparative example 2
The high-carbon steel continuous casting blank segregation control process comprises the following steps:
primary cooling is carried out on molten steel with the superheat degree of 20 ℃ to obtain a primary cooling blank with the surface of which a steel shell is formed;
for the primary cooling blank formed, the temperature was 1.75X10 -2 Drawing at a constant drawing speed of m/s, and performing secondary cooling on the prepared primary cooling blank in an aerosol cooling mode, wherein the specific water quantity is 0.6L/kg of steel, so as to form a secondary cooling blank;
the electromagnetic stirring position of the solidification end is adopted to be 9.75m from the meniscus of the crystallizer, and the magnetic field strength is 765 multiplied by 10 -4 And (3) performing secondary cooling electromagnetic stirring on the secondarily cooled molten steel in an electromagnetic stirring mode at the solidification tail end of the T, wherein the stirring mode is to drive the molten steel to rotate clockwise for 10s, stop for 3s, drive the molten steel to rotate anticlockwise for 10s again, stop for 3s, and drive the molten steel to rotate continuously in this mode to form the high-carbon steel continuous casting blank.
The low-power detection method of the high-carbon steel continuous casting blank prepared in all the embodiments is as follows:
1. central crack, shrinkage cavity
The prepared high-carbon steel continuous casting blank is sampled and the obtained sample is pickled according to the detection standard of national standard GB/T226-2015 'steel macrostructure and defect acid etching test method', and the central crack and shrinkage cavity of the pickled sample are rated according to the line standard YB/T153-2015 'high-quality structural steel continuous casting blank macrostructure defect rating map', and the detection data are shown in Table 1. Detection conditions: 25 ℃.
2. Carbon segregation index
The carbon segregation index in the prepared high-carbon steel continuous casting blank is detected according to the detection standard of national standard GB/T33165-2016 method for quantitative analysis of center segregation of high-carbon steel wire rods, and the detection data are shown in Table 1. Detection conditions: 25 ℃.
TABLE 1 Performance test data Table for examples 1-2 and comparative examples 1-2
| Central crack/stage | Shrinkage cavity is less than or equal to 0.5 proportion | Carbon segregation index | |
| Example 1.11 | 0 | 100 | 1.00 |
| Example 1.12 | 0 | 98 | 1.00 |
| Example 1.13 | 1 | 50 | 1.30 |
| Example 1.14 | 0 | 95 | 1.08 |
| Example 1.15 | 0 | 90 | 1.23 |
| Example 1.2 | 0 | 96 | 1.01 |
| Example 1.3 | 0 | 96 | 1.01 |
| Example 2.1 | 0 | 95 | 1.03 |
| Example 2.2 | 0 | 95 | 1.05 |
| Example 2.3 | 0 | 95 | 1.05 |
| Comparative example 1 | 2 | 36 | 1.50 |
| Comparative example 2 | 2 | 36 | 1.50 |
The present application is described in detail below in conjunction with the test data provided in table 1.
As a result of combining comparative examples 1-2 and examples 1-2, it was found that the center crack and carbon segregation index of the high carbon steel continuous casting slab obtained by the control process in examples 1-2 of the present application were both lower than those of comparative examples 1-2, and the proportion of shrinkage cavity of 0.5 or less was increased as compared with comparative examples 1-2, indicating that the control process of the present application exhibited better performance in reducing the center crack, shrinkage cavity and carbon segregation index of the high carbon steel continuous casting slab.
Examples 1.11 to 1.13 were compared with respect to the degree of superheat of molten steel, and as a result, it was found that the high-carbon steel continuous casting slab produced in example 1.11 was superior in terms of the ratio of central crack, shrinkage cavity of 0.5 or less and carbon segregation index, which means that controlling the degree of superheat of molten steel in the range of 20.+ -. 5 ℃ was superior in terms of improving central crack, shrinkage cavity and carbon segregation of the produced high-carbon steel continuous casting slab.
And the degree of superheat of the molten steel in example 1.13 is 10 ℃, the produced high-carbon steel continuous casting blank is worse than that in example 1.11 in terms of central crack, proportion of shrinkage cavity less than or equal to 0.5 and carbon segregation index, which is probably caused by the fact that when the degree of superheat of the molten steel is less than 15 ℃, the fluidity of the molten steel is poor, and the molten steel starts to change to a solid phase, so that the casting of the molten steel and the floating of nonmetallic inclusion in the molten steel are influenced.
By combining the embodiment 1.11 and the comparative example 1-2, the electromagnetic stirring mode of the crystallizer is adopted in the comparative example 1, and the prepared high-carbon steel continuous casting blank is worse than the embodiment 1.11 in the aspects of central crack, the proportion of shrinkage cavity less than or equal to 0.5 and the carbon segregation index; in comparative example 2, the ratio of the central crack, shrinkage cavity less than or equal to 0.5 and carbon segregation index of the prepared high-carbon steel continuous casting blank are inferior to those of example 1.11, probably due to the combined electric stirring mode of the electromagnetic stirring of the crystallizer and the electromagnetic stirring of the solidification end adopted in example 1.11, when the molten steel moves into the crystallizer, the electromagnetic stirring of the crystallizer drives the molten steel to rotate, so that the components in the molten steel are uniformly dispersed, the possibility of segregation in the crystallizer is reduced, and when the formed steel shell moves to a secondary cooling zone under tension and the like, the liquid core in the steel shell is gradually solidified, and at the moment, the electromagnetic stirring of the solidification end enables the liquid core in the steel shell to rotate, so that the components in the liquid core are further uniformly dispersed, and the components in the liquid core are not easy to cause segregation in the solidification process of the liquid core.
In example 1.14 of the present application, the influence of the distance of the electromagnetic stirring at the solidification end from the meniscus of the crystallizer on the produced high-carbon steel continuous casting slab was examined by taking example 1.11 as a control. As a result, it was found that the distance from the solidification end to the meniscus of the crystallizer in example 1.14 was 11.1m, and the produced high-carbon steel continuous casting billet was inferior to example 1.11 in terms of the ratio of the central crack, shrinkage cavity of 0.5 or less and the carbon segregation index, probably due to the fact that the area of the unset liquid core was small and the area of the liquid core due to the electromagnetic stirring was reduced when the formed steel shell driven the liquid core to move to the solidification end electromagnetic stirring place due to the increase of the distance from the solidification end to the meniscus of the crystallizer.
In the present application, example 1.15 examined the influence of the drawing speed on the produced high-carbon steel continuous casting slab by taking example 1.11 as a control. As a result, it was found that the drawing rate of example 1.15 was lower than that of example 1.11, and the produced high-carbon steel continuous casting slab was inferior to example 1.11 in terms of the ratio of center crack, shrinkage cavity.ltoreq.0.5 and carbon segregation index, probably due to the gradual solidification and segregation of the liquid core in the steel shell and the reduction of the liquid core area by electromagnetic stirring action at the solidification end when the steel shell reached the solidification end.
Examples 1.2 to 1.3 examined the influence of electromagnetic stirring modes at different solidification ends on the produced high-carbon steel continuous casting blank by taking example 1.11 as a control. As a result, it was found that the high-carbon steel continuous casting slab produced in example 1.2 was inferior to example 1.11 in terms of the central crack, the ratio of shrinkage cavity to 0.5 and the carbon segregation index, probably due to the fact that the solidification end applied a reverse force to the liquid core while maintaining the inertia of the forward rotation and the solidification end applied a reverse force to the liquid core, so that the liquid core was moved outside the steel shell and impacted the side wall of the steel shell.
In the embodiment 1.3, the mode of stirring in a single direction is adopted, and the prepared high-carbon steel continuous casting blank is worse than the embodiment 1.11 in the aspects of central crack, the proportion of shrinkage cavity less than or equal to 0.5 and the carbon segregation index, which is probably caused by the fact that the liquid core always rotates in a single direction and forms centrifugal force, so that the impact is generated on the side wall of the steel shell.
In embodiment 1.11, the method of stopping 3s after forward rotation and then reversing is adopted, so that the inertia of the liquid core is gradually reduced in the process of driving the liquid core to change direction by the solidification tail end, thereby facilitating the driving of the liquid core to change direction and reducing the impact of the liquid core on the side wall of the steel shell.
Examples 2.1 to 2.3 examined the effect of different secondary cooling modes on the high carbon steel continuous casting slab produced by taking example 1.11 as a control. As a result, it was found that the high-carbon steel continuous casting billets prepared in examples 2.1 to 2.3 were each inferior to example 1.11 in terms of the central crack, the ratio of shrinkage cavity to 0.5 or less and the carbon segregation index, probably due to the fact that when the cold water was directly cooled down the billets, the cold water was difficult to uniformly contact with the surface of the steel shell, so that the surface of the steel shell was unevenly cooled down, and the impact was caused to the surface of the steel shell when the cold water contacted with the steel shell.
In the embodiment 1.11, the aerosol cooling mode is adopted, and the impact on the surface of the steel shell is reduced while the surface of the steel shell is uniformly cooled, so that the adverse effects on the central crack, shrinkage cavity and carbon segregation of the prepared high-carbon steel continuous casting blank are reduced.
And the high-carbon steel continuous casting blank prepared in the example 2.1 is superior to the example 2.2 and the example 2.3 in the aspects of the central crack, the shrinkage cavity and the carbon segregation index, which are all superior to those of the example 2.2 and the example 2.3, and the method of stopping 3s and reversing after forward rotation is adopted in the same water cooling mode, so that the central crack, the shrinkage cavity and the carbon segregation of the high-carbon steel continuous casting blank prepared are better than those of the method of immediately reversing or stirring in a single direction after forward rotation.
3. Composition segregation
11 high-carbon steel continuous casting billets are prepared according to the control process described in the embodiment 1.11, the prepared 11 continuous casting billets are subjected to in-line detection and sampling for 9 points, and the segregation indexes of C, mn and Cr components of the sampling points are detected according to the detection standard of national standard GB/T33165-2016 of high-carbon steel wire rod center segregation quantitative analysis method, so that the average value and the extremely poor value are obtained.
Referring to fig. 1, the average value of carbon segregation of each high-carbon steel continuous casting slab manufactured by the control process of example 1.11 was about 1.00, and the difference value was 0.15 or less, so that it was found that the cross section of the manufactured continuous casting slab was not greatly different in carbon segregation index from edge to core, and carbon elements were uniformly distributed in the manufactured high-carbon steel continuous casting slab.
Referring to fig. 2, the average value of manganese segregation of each high-carbon steel continuous casting blank prepared by the control process of example 1.11 is about 1.00, and the difference value is below 0.075, so that the manganese segregation indexes of the cross section of the prepared continuous casting blank from the edge to the core are not greatly different, and manganese elements are uniformly distributed in the prepared high-carbon steel continuous casting blank.
Referring to fig. 3, the average value of chromium segregation of each high-carbon steel continuous casting slab manufactured by the control process of example 1.11 is about 1.00, and the difference value is between 0.10 and 0.15, so that the cross section of the manufactured continuous casting slab has a small difference between the chromium segregation indexes from the edge to the core, and the chromium elements are uniformly distributed in the manufactured high-carbon steel continuous casting slab.
As can be seen from fig. 1-3, the carbon element, manganese element and chromium element are all uniformly distributed in the high-carbon steel continuous casting billet prepared by the control process of example 1.11, which indicates that the control process of example 1.11 is better in improving the segregation of the steel billet components and further improving the central crack, shrinkage cavity and carbon segregation index of the high-carbon steel continuous casting billet.
Application example
Application examples 1-2
The high carbon steel continuous casting billets prepared in examples 1-2 were prepared into wire rods by the same process.
Comparative application examples 1-2
The high carbon steel continuous casting slab obtained in comparative example 1-2 was subjected to the same process as in application example 1-2 to obtain a wire rod.
The wire rods prepared in application examples 1-2 and comparative application examples 1-2 were subjected to the following performance tests. Performance measurements included mesh carbide rating of the wire rod core, tensile strength, reduction of area, and elongation after break of the wire rod. The test data are shown in Table 2.
1. Network carbide
The mesh carbide of the wire rod is rated according to the detection standard of the industry standard YB/T4412-2014 high carbon steel mesh cementite evaluation method. Detection conditions: 25 ℃.
2. Tensile strength of
According to national standard GB/T228.1-2021 section 1 of tensile test of metallic materials: the tensile strength of the wire rod obtained was measured according to the measurement standard of the room temperature test method. Detection conditions: 25 ℃.
3. Shrinkage of section and elongation after break
According to national standard GB/T228.1-2021 section 1 of tensile test of metallic materials: the reduction of area and the elongation after break of the wire rod obtained were examined according to the detection standard of the room temperature test method. Detection conditions: 25 ℃.
TABLE 2 Performance test data Table for application examples 1-2 and comparative application examples 1-2
The present application is described in detail below in conjunction with the test data provided in table 2.
In combination with the wire rods produced by application of examples 1-2 and the wire rods produced by comparative examples 1-2, it was found that the wire rods produced by application of examples 1-2 were superior to the wire rods produced by comparative examples 1-2 in terms of net-like carbide, tensile strength, reduction of area and elongation after break, which means that the control process of examples 1-2 according to the present application was superior in terms of improving net-like carbide, tensile strength, reduction of area and elongation after break of the produced wire rods, and was more conducive to reducing the possibility of breakage of the wire rods during drawing.
As a result of comparing the superheat degree of molten steel with application examples 1.11 to 1.13, it was found that the wire rods produced in application example 1.11 exhibited better in terms of net-like carbide, tensile strength, reduction of area and elongation after break, which means that controlling the superheat degree of molten steel in the range of 20.+ -. 5 ℃ exhibited better in terms of net-like carbide, tensile strength, reduction of area and elongation after break for the wire rods produced by improvement.
In combination with application example 1.11 and comparative application examples 1-2, it was found that the mesh carbide, tensile strength, reduction of area and elongation after break of the wire rod prepared in comparative example 1 by electromagnetic stirring with a crystallizer were inferior to application example 1.11; the mesh carbide, tensile strength, reduction of area and elongation after break of the wire rod prepared in comparative example 2 by means of electromagnetic stirring at the solidification end are inferior to those of application example 1.11, which means that the control process of example 1.11 is advantageous for improving the mesh carbide, tensile strength, reduction of area and elongation after break of the wire rod prepared.
Using application example 1.11 as a control, the effect of the distance of the electromagnetic stirring at the solidification end from the meniscus of the crystallizer on the wire rod produced was examined in application example 1.14. As a result, it was found that the distance of the solidification end electromagnetic stirring from the meniscus of the mold in example 1.14 was 11.1m, and the net-like carbide, tensile strength, reduction of area and elongation after break of the produced wire rod were inferior to those of application example 1.11, probably due to the fact that the increase of the distance of the solidification end electromagnetic stirring from the meniscus of the mold, the solidification end electromagnetic stirring was difficult to exert a sufficient effect, the prevention of segregation of the components of the continuous casting slab was difficult, and the mechanical properties of the produced wire rod were not improved.
Application example 1.15 examined the effect of pull rate on the wire rod produced, with application example 1.11 as a control. As a result, it was found that the drawing rate of example 1.15 was lower than that of example 1.11, and the net-like carbide, tensile strength, reduction of area and elongation after fracture of the produced wire rod were all inferior to those of application example 1.11, probably due to the fact that the drawing rate was lowered, the liquid core in the steel shell was gradually solidified and the component was segregated when the steel shell reached the solidification end, the electromagnetic stirring at the solidification end was difficult to prevent the component segregation, and the mechanical properties of the wire rod were not improved.
Using application example 1.11 as a control, application examples 1.2 to 1.3 examined the influence of different coagulation-end electromagnetic stirring modes on the produced wire rods. As a result, it was found that the wire rods produced in example 1.11 were superior in terms of net-shape carbide, tensile strength, reduction of area and elongation after break by stopping for 3 seconds after normal rotation, which suggests that the two-cold stirring process of example 1.11 is advantageous for improving net-shape carbide, tensile strength, reduction of area and elongation after break of the wire rods produced.
Using application example 1.11 as a control, application examples 2.1 to 2.3 examined the effect of different secondary cooling modes on the wire rods produced. As a result, it was found that the wire rods produced in examples 2.1 to 2.3 were inferior to the application example 1.11 in terms of net-like carbide, tensile strength, reduction of area and elongation after break by water cooling, which means that the aerosol cooling in example 1.11 was advantageous for improving net-like carbide, tensile strength, reduction of area and elongation after break of the produced wire rods.
The present embodiment is merely illustrative of the present application and is not intended to be limiting, and those skilled in the art, after having read the present specification, may make modifications to the present embodiment without creative contribution as required, but is protected by patent laws within the scope of the claims of the present application.
Claims (7)
1. The high-carbon steel continuous casting blank segregation control process is characterized by comprising the following steps of:
primary cooling is carried out on molten steel, a crystallizer is arranged for electromagnetic stirring and continuous stirring to drive the molten steel to rotate, and a primary cooling blank with a steel shell formed on the surface is prepared;
drawing the formed primary cooling blank at a constant speed, and performing secondary cooling on the obtained primary cooling blank to form a secondary cooling blank;
and carrying out secondary cooling electromagnetic stirring on the secondary cooled molten steel to form a high-carbon steel continuous casting blank.
2. The high-carbon steel continuous casting slab segregation control process according to claim 1, characterized in that: the superheat degree of the molten steel is (20+/-5) DEG C.
3. The high-carbon steel continuous casting slab segregation control process according to claim 2, characterized in that: the pulling speed is 1.75X10 -2 m/s。
4. The high-carbon steel continuous casting slab segregation control process according to claim 1, characterized in that: the secondary cooling electromagnetic stirring adopts a solidification end electromagnetic stirring mode, and the central magnetic field intensity of the stirring coil is (765+/-15) multiplied by 10 -4 T。
5. The high-carbon steel continuous casting slab segregation control process according to claim 4, wherein the process comprises the following steps of: the electromagnetic stirring at the solidification end adopts an alternate stirring mode, and the stirring mode is specifically that after driving molten steel to rotate for 10s along a certain hour, the molten steel stops for 3s and is driven to reversely rotate for 10s again.
6. The high-carbon steel continuous casting slab segregation control process according to claim 5, wherein the process comprises the following steps of: the solidification end electromagnetic stirring position is 9.75m from the crystallizer meniscus.
7. The high-carbon steel continuous casting slab segregation control process according to claim 6, characterized in that: the secondary cooling mode is aerosol cooling, the cooling medium is compressed air and water, and the specific water quantity of the primary cooling is 0.6L/kg of steel.
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