CN108705052B - Continuous casting production method of cogged steel billets in bloom - Google Patents
Continuous casting production method of cogged steel billets in bloom Download PDFInfo
- Publication number
- CN108705052B CN108705052B CN201810700707.1A CN201810700707A CN108705052B CN 108705052 B CN108705052 B CN 108705052B CN 201810700707 A CN201810700707 A CN 201810700707A CN 108705052 B CN108705052 B CN 108705052B
- Authority
- CN
- China
- Prior art keywords
- crystallizer
- steel
- bloom
- casting
- continuous casting
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/0406—Moulds with special profile
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/055—Cooling the moulds
-
- 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
-
- 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
-
- 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
-
- 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
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Continuous Casting (AREA)
Abstract
The invention relates to a continuous casting production method of a cogged bloom gear steel casting blank, which is suitable for cogged bloom gear steel casting blanks with the cross sections of 360mm multiplied by 450mm and belongs to the technical field of cogged bloom gear steel production. On the basis of electromagnetic stirring of the crystallizer, an electromagnetic stirring device is additionally arranged between the secondary cooling zone and the solidification tail end, the installation positions and the working parameters of the secondary cooling zone and the solidification tail end are reasonably designed, and the superheat degree, the pouring speed, the cooling parameters and the like of the pouring molten steel are controlled in a combined manner, so that the compactness and the homogeneity of the cogged bloom steel continuous casting billet are improved, in addition, the corner cooling of the casting billet is optimized through the design of the fillet parameters of the tubular crystallizer, and the defect control of the corner of the casting billet is improved. Through the improvement of the cooling water path, the heat transfer uniformity is ensured, and the thickness of the casting blank shell at the outlet of the crystallizer is uniform. The invention can ensure the high-level control of the comprehensive quality of the bloom gear steel continuous casting billet.
Description
Technical Field
The invention relates to a continuous casting production method of a cogged bloom gear steel casting blank, which is suitable for cogged bloom gear steel casting blanks with the cross sections of 360mm multiplied by 450mm and belongs to the technical field of cogged bloom gear steel production.
Background
The gear is an important power transmission mechanical component, the stress conditions of the gears in different working conditions and different parts are different, the failure modes also have different degrees, and the failure modes are influenced by a plurality of factors such as gear materials, processing techniques, lubricating conditions, friction force, gear geometric parameters, load modes and the like. The main failure modes are as follows: tooth root fracture, tooth surface profile deformation by tooth surface depression, fatigue exfoliation, wear classified into adhesive wear and abrasive wear, and the like. According to the main failure modes, the performance requirements of the gear steel are high crushing resistance and good impact resistance and bending resistance with pitting peeling resistance. Proper hardenability, hardening layer depth and core hardness, good processing performance, cutting processability, deformation and dimensional stability. The automobile gear has the functions of power transmission and speed change and is a great important representative of the gear. The steel for manufacturing the gear not only needs to have good obdurability and wear resistance, can well bear impact, bending and contact stress, but also needs to have small deformation. In the manufacturing process of the gear, besides reasonable design and machining, heat treatment such as carburizing and quenching or quenching and tempering is also required to ensure that the surface of the gear is hardened and wear-resistant and the matrix resists impact. The quality of the gear machining blank determines to a large extent the efficiency and quality control of gear production.
With the continuous development of continuous casting production technology, the technical level of casting blank quality control is continuously improved. At present, the production of the automobile gear blank in China mainly takes billet continuous casting production as a main part, and along with the continuous improvement of the quality requirement of the gear, the requirements on the compactness and the homogeneity of the gear blank are higher. Compared with a small square billet, the rolling compression ratio of the large square billet gear steel casting billet is larger, and the high-quality large square billet is more favorable for improving the compactness and the homogeneity of a gear product. However, the high-quality production of the bloom continuous casting has certain technical difficulty, firstly, the solidification time of the center of a casting blank is long, the length of a liquid core is increased, feeding at the final solidification stage is difficult, the severity of the center segregation of the casting blank is improved, and the influence of the quality of the corner part of the casting blank on the subsequent solidification evolution is increased, so that interference control needs to be provided for the continuous casting crystallizer, the secondary cooling strength and the solidification evolution of the casting blank. Some scholars at home and abroad carry out corresponding researches on the quality control equipment and technology of the bloom casting blank, mainly aiming at bloom heavy rail steel and small square billet gear steel, and basically do not see the researches on the quality control of the bloom gear steel casting blank with the section of 360mm multiplied by 450 mm.
For example:
CN107262689A discloses a bloom second cold-pressing lower-foot-roll structure and a pressing process, in particular to a bloom second cold-pressing lower-foot-roll structure and a pressing process relating to the technical field of ferrous metallurgy. The bloom second cold pressing lower foot roller structure comprises a pressing area upper foot roller and a pressing area lower foot roller, wherein the pressing area lower foot roller is positioned below the pressing area upper foot roller, a boss is arranged in the middle of the pressing area lower foot roller, and the boss of the pressing area lower foot roller is longer than the boss of the pressing area upper foot roller. The second cold pressing area reduction process of the bloom blanks is characterized in that a plurality of groups of upper foot rollers and lower foot rollers in reduction areas are arranged, and the reduction amount of the upper foot rollers in the reduction areas is gradually increased in the blank drawing direction. The method can effectively solve the problems of center segregation and center porosity of the bloom continuous casting billet. However, some key details of quality control of a 360mm x 450mm cross-section cogged steel ingot are not mentioned.
CN106735013A discloses a continuous casting process for improving the quality of bloom blanks, which is simple and easy to implement, improves the contact between the molten steel for casting and the crystallizer copper plate, increases lubrication, eliminates the phenomenon of scraping steel by corner seams, effectively avoids the surface defects of the bloom blanks, ensures the quality of the bloom blanks, and improves the service life of the crystallizer copper plate. The method is characterized by comprising the following steps: (1) coating a crystallizer lubricant on the copper wall of the crystallizer 40 +/-5 min before the casting machine starts casting, and fully coating, especially the corner of the crystallizer; the mode of smearing the crystallizer lubricant is as follows: uniformly coating by using a roller, coating for the first time, naturally drying for 5 +/-1 min, coating for the second time, and performing other conventional preparation work before casting after naturally drying; (2) in the casting process, graphite is filled at the corner seam of the crystallizer copper plate during casting, the opening degree of the stopper rod is controlled to be 30-45% during casting, the steel flow is 40-60% of normal casting, after the operation is finished, other casting starting work is normally controlled until starting, and the pulling speed is stabilized at 0.45m/min or 0.48 m/min. However, some key details of quality control of a 360mm x 450mm cross-section cogged steel ingot are not mentioned.
CN107225148A discloses a rolling method for 22CrMoH gear steel, which can effectively reduce the length/width ratio of MnS inclusions by adjusting the blank opening temperature, the finish rolling temperature, the pass deformation and the controlled cooling process, wherein the rolling structure of the gear steel obtained by the method is a flattened austenite structure, the size of a precipitated phase is 20-25 nm, and the weight fraction of the precipitated phase is 0.31-0.38%; after heat treatment, the austenite grain size is 5-7 μm, and the longitudinal impact toughness ratio approaches to 1. The rolling method is characterized by comprising the following steps: (1) heating the continuous casting billet by a heating furnace, and descaling by high-pressure water to remove iron scales; (2) cogging the dephosphorized continuous casting billet to obtain a primary rolling billet; (3) rolling the primary rolling blank in a continuous rolling mill set; (4) after the product is discharged out of the continuous rolling mill set, water mist cooling is carried out; (5) after being cooled, the water mist enters a slow cooling bed for slow cooling; (6) entering a slow cooling pit for slow cooling; (7) and air cooling to obtain the hot-rolled 22CrMoH gear round steel. However, some key details of quality control of a 360mm x 450mm cross-section cogged steel ingot are not mentioned.
CN106967931A discloses 20Cr2Ni4 gear steel and a production process thereof, wherein the 20Cr2Ni4 gear steel is made of 20Cr2Ni4, and the mass percentage of Mo in the 20Cr2Ni4 is as follows: 0.15 to 0.30 percent. The production process comprises the steps of proportioning, smelting in an electric arc furnace and smelting in a refining furnace, wherein molten steel is molten in the smelting process of the electric arc furnace, the temperature reaches 1570-1590 ℃, and sampling is carried out for detection and analysis, so that the mass percentage content of Mo reaches 0.15-0.30%; in the smelting process of the refining furnace, the temperature reaches 1570-1590 ℃, and the samples are sampled for detection and analysis, so that the mass percentage of Mo reaches 0.15-0.30%. The invention reduces the inclusion in the steel, reduces the H, O, N gas content in the steel, reduces the harmful elements P, S, As and Sn in the steel, adds a proper amount of Mo, can improve the comprehensive properties of the steel, such As hardenability, heat strength, refined crystal grain, improved steel strength and the like when being used for parts such As large gears, shafts and the like. The alloy is characterized in that the mass percentage of Mo in 20Cr2Ni4 is as follows: 0.15 to 0.30 percent. However, some key details of quality control of a 360mm x 450mm cross-section cogged steel ingot are not mentioned.
CN106566998A discloses a manufacturing method of CrMo gear round steel, which is characterized in that the components by weight percentage are as follows: c: 0.22 to 0.27 percent, Si: 0.03 to 0.12 percent, Mn: 1.20-1.45%, S is less than or equal to 0.020%, P is less than or equal to 0.020%, and Cr: 0.30% -0.60%, Mo: less than or equal to 0.20 percent, Al: 0.015-0.040%, Ni is less than or equal to 0.10%, O is less than or equal to 15 multiplied by 10-6%, and the balance is Fe and inevitable impurities. The A-type and D-type inclusions and the B-type and C-type inclusions of the prepared round steel are less than or equal to 1.5 grade and less than or equal to 1.0 grade, and the hardenability value of the round steel is 42-50 HRC for J5mm, 38-46 HRC for J9mm and 32-40 HRC for J15 mm. The method changes the traditional technical idea of improving the hardenability of steel by adding a large amount of alloy elements such as Cr, Ni and Mo, greatly reduces the Mo content and the Cr content by properly improving the C, Mn content, replaces Ni alloy, greatly reduces the production cost of products and improves the competitiveness of the products on the premise of ensuring that the hardenability of the gear steel is not reduced. However, some key details of quality control of a 360mm x 450mm cross-section cogged steel ingot are not mentioned.
Disclosure of Invention
The technical problem to be solved by the invention is as follows: the continuous casting production method of the cogged bloom gear steel casting blank is suitable for cogged blooms with the sections of 360mm multiplied by 450mm, can improve the compactness and the homogeneity of the cogged bloom gear steel casting blank and ensure the comprehensive high-quality and horizontal control of the cogged bloom gear steel casting blank.
In order to solve the technical problems, the invention adopts the technical scheme that:
(1) the tube crystallizer is adopted, and the size of a corner fillet of the tube crystallizer is R20mm, so that the cooling of the corner of a casting blank can be optimized, and the defect control of the corner of the casting blank is improved; the cooling water path has two inlets and two loops, and is provided with two water inlets and two water outlets, and a DN250 regulating valve is arranged at the position of the water inlet, so that the cooling intensity of the crystallizer can be accurately controlled; the technological parameters of the cooling water of the crystallizer are controlled to be 3150L/min-3350L/min, the water pressure is 0.80 MPa-0.90 MPa to ensure the thickness and uniformity of the blank shell of the casting blank at the outlet of the crystallizer, and the thickness size of the blank shell is preferably controlled to be 16 mm-20 mm.
(2) The electromagnetic stirring of the crystallizer is low-position installation at the outlet of the crystallizer, the covering height of the electromagnetic stirring equipment of the crystallizer is 350mm, and the lower end of the electromagnetic stirring equipment of the crystallizer is flush with the lower opening of the crystallizer; measuring the gauss intensity of an electromagnetic stirring actual magnetic field of the crystallizer, and setting the stirring current with the gauss intensity of the actual stirring magnetic field being 280 +/-15 Gs, wherein the frequency of the stirring current is 2.4 Hz;
(3) an electromagnetic stirring device is arranged between the secondary cooling zone and the solidification tail end, and the installation position of the electromagnetic stirring device is a region with a solidification linearity ratio of 0.45-0.47, specifically a region 10.0-11.0 m away from the molten steel level of the crystallizer; actually measuring the Gaussian intensity of the stirring magnetic field, and setting the stirring current intensity according to the practical Gaussian intensity of the magnetic field of 200 +/-25 Gs, wherein the stirring current frequency is 7.0 Hz;
(4) the specific water amount of secondary cooling is 0.301L kg-1 Steel～0.323L·kg-1 SteelSetting is carried out;
in addition, the molten tundish steel needs to have a certain superheat degree so as to meet the casting requirement. For the 1 st heat of tundish casting, controlling the superheat degree of casting molten steel at 25-45 ℃; controlling the superheat degree of the casting molten steel at 15-35 ℃ for the 2 nd-N heats of the tundish casting;
the pulling speed is controlled between 0.45m/min and 0.55m/min, and the casting can be carried out at a constant speed of 0.50m/min according to the target pulling speed.
The invention has the beneficial effects that: on the basis of electromagnetic stirring of the crystallizer, electromagnetic stirring equipment is additionally arranged between a secondary cooling zone and a solidification tail end, the installation positions and the working parameters of the secondary cooling zone and the solidification tail end are reasonably designed, and the superheat degree, the pouring speed, the cooling parameters and the like of pouring molten steel are controlled in a combined mode, so that the compactness and the homogeneity of the cogged steel bloom continuous casting billet are improved, in addition, through the design of fillet parameters of the tubular crystallizer, the corner cooling of the casting billet is optimized, and the defect control of the corner of the casting billet is improved. Through the improvement of the cooling water path, the heat transfer uniformity is ensured, and the thickness of the casting blank shell at the outlet of the crystallizer is uniform. The invention can ensure the high-level control of the comprehensive quality of the bloom gear steel continuous casting billet.
Detailed Description
The present invention will be further described with reference to the following examples.
In the examples, the electromagnetic stirring equipment installed between the secondary cooling zone and the solidification end is referred to as "electromagnetic stirring between the secondary cooling zone and the solidification end" (S-F-EMS).
Example 1
In this example, a steel mill produced a continuous casting bloom of 20CrMnTiH series gear steel with a cross section of 360mm × 450mm by the method of the present invention. The specific implementation mode of the invention is as follows: a tubular crystallizer is adopted, and the corner fillet size is R20 mm; the water path of the tubular crystallizer is designed to be two-in and two-back, so that the heat transfer uniformity is ensured; the cooling water quantity of the crystallizer is 3150L/min-3350L/min, the water pressure is 0.80 MPa-0.90 MPa, and DN250 regulating valve is adopted to finely regulate the cooling water of the crystallizer; the electromagnetic stirring of the crystallizer is low-position installation at the outlet of the crystallizer, the covering height of the electromagnetic stirring equipment of the crystallizer is 350mm, and the lower end of the electromagnetic stirring equipment of the crystallizer is flush with the lower opening of the crystallizer; the practical magnetic field Gaussian intensity of the crystallizer is electromagnetically stirred to be 280 +/-15 Gs, the stirring current is set to be 490-510A, and the stirring current frequency is 2.4 Hz. Mounting mediumIn the electromagnetic stirring (S-F-EMS) position of the secondary cooling and solidification tail end, the solidification linearity ratio is 0.45-0.47, specifically, in the interval of 10.0-11.0 m from the crystallizer steel liquid level, the Gaussian intensity of the stirring magnetic field is 200 +/-25 Gs, the stirring current intensity is 210A-220A, and the stirring current frequency is 7.0 Hz; the secondary cooling specific water amount is 0.301L kg-1 Steel～0.323L·kg-1 Steel。
In addition, the superheat degree of the casting molten steel (tundish casting) is controlled to be 17-32 ℃, the first time of tundish casting is carried out, and the superheat degree is controlled to be 25-45 ℃; the pulling speed is controlled to be 0.45 m/min-0.55 m/min, and the proportion of the constant-speed pouring time of the target pulling speed of 0.50m/min is 91%.
The liquid level of molten steel in the crystallizer is stable in the continuous casting process, and the thickness of the covering slag is uniformly distributed. Carrying out low-power detection on the continuous casting bloom; the cold acid dendrite corrosion is adopted to detect the blank shell thickness distribution condition of the cross section of a casting blank, and the result shows that the blank shell thickness of the 20CrMnTiH series gear steel continuous casting bloom produced by the technology is uniformly distributed along the circumferential direction of the cross section and the whole thickness is controlled to be 16-20 mm; the corner part quality of the casting blank is good, metal in-situ scanning detection is carried out on the full section of the continuous casting blank, the homogeneity degree of the full section of the casting blank is 0.901-0.922, the core density is 0.913-0.941, the center segregation and the center porosity of the casting blank are respectively less than or equal to 0.5 grade corresponding to acid pickling corrosion low-power rating, and no center shrinkage cavity exists.
Example 2
In this example, a steel mill produced a continuous casting bloom of 20CrMo series gear steel with a cross section of 360mm × 450mm by the method of the present invention. The specific implementation mode of the invention is as follows: a tubular crystallizer is adopted, and the corner fillet size is R20 mm; the water path of the tubular crystallizer is designed to be two-in and two-back, so that the heat transfer uniformity is ensured; the cooling water quantity of the crystallizer is 3157L/mi-3340L/min, the water pressure is 0.82 MPa-0.87 MPa, and DN250 regulating valve is adopted to finely regulate the cooling water of the crystallizer; the electromagnetic stirring of the crystallizer is low-position installation at the outlet of the crystallizer, the covering height of the electromagnetic stirring equipment of the crystallizer is 350mm, and the lower end of the electromagnetic stirring equipment of the crystallizer is flush with the lower opening of the crystallizer; the practical magnetic field gauss intensity of the crystallizer is electromagnetically stirred to be 280 +/-5 Gs, the stirring current is set to be 491A-500A, and the stirring current frequency is 2.4 Hz. Setting the position between secondary cooling and solidification tail end electromagnetic stirring (S-F-EMS) as solidificationThe solid-linear ratio is 0.45-0.47, specifically in the interval of 10.0-11.0 m away from the liquid level of the crystallizer steel, the gauss intensity of the stirring magnetic field is 200 +/-25 Gs, the stirring current intensity is 214A-218A, and the stirring current frequency is 7.0 Hz; the secondary cooling specific water amount is 0.311L kg-1 Steel～0.320L·kg-1 Steel。
In addition, the superheat degree of the casting molten steel (tundish casting) is controlled at 16-35 ℃, the first heat of tundish is controlled at 27-43 ℃; the pulling speed is controlled to be 0.47 m/min-0.53 m/min, and the proportion of the constant-speed pouring time of the target pulling speed of 0.50m/min is 95 percent.
The liquid level of molten steel in the crystallizer is stable in the continuous casting process, and the thickness of the covering slag is uniformly distributed. Carrying out low-power detection on the continuous casting bloom; the cold acid dendrite corrosion is adopted to detect the blank shell thickness distribution condition of the cross section of a casting blank, and the result shows that the blank shell thickness of the 20CrMnTiH series gear steel continuous casting bloom produced by the technology is uniformly distributed along the circumferential direction of the cross section and the whole thickness is controlled to be 17-18.6 mm; the quality of the corner part of the casting blank is good, metal in-situ scanning detection is carried out on the full section of the continuous casting blank, the homogeneity degree of the full section of the casting blank is 0.904-0.931, the core density is 0.910-0.936, the center segregation and the center porosity of the corresponding acid pickling corrosion low-power grade are less than or equal to 0.5 grade, and no center shrinkage cavity exists.
Example 3
In this example, a steel mill produced a 22CrMo series gear steel continuous casting bloom with a cross section of 360mm × 450mm by the method of the present invention. The specific implementation mode of the invention is as follows: a tubular crystallizer is adopted, and the corner fillet size is R20 mm; the water path of the tubular crystallizer is designed to be two-in and two-back, so that the heat transfer uniformity is ensured; the cooling water quantity of the crystallizer is 3255L/min-3350L/min, the water pressure is 0.85 MPa-0.90 MPa, and DN250 regulating valve is adopted to finely regulate the cooling water of the crystallizer; the electromagnetic stirring of the crystallizer is low-position installation at the outlet of the crystallizer, the covering height of the electromagnetic stirring equipment of the crystallizer is 350mm, and the lower end of the electromagnetic stirring equipment of the crystallizer is flush with the lower opening of the crystallizer; the practical magnetic field Gaussian intensity of the crystallizer is electromagnetically stirred to be 280 +/-10 Gs, the stirring current is set to be 495A-510A, and the stirring current frequency is 2.4 Hz. Installing a region with solidification linearity ratio of 0.45-0.47 at the position of electromagnetic stirring (S-F-EMS) between secondary cooling and solidification ends, specifically, a distanceThe steel liquid level of the crystallizer ranges from 10.0m to 11.0m, the Gaussian intensity of a stirring magnetic field is 200 +/-25 Gs, the stirring current intensity is 215A to 220A, and the stirring current frequency is 7.0 Hz; the secondary cooling specific water amount is 0.312L kg-1 Steel～0.322L·kg-1 Steel。
In addition, the superheat degree of the casting molten steel (tundish casting) is controlled at 15-35 ℃, the first heat of tundish is controlled at 29-45 ℃; the pulling speed is controlled to be 0.46 m/min-0.55 m/min, and the proportion of the constant-speed pouring time of the target pulling speed of 0.50m/min is 90.3 percent.
The liquid level of molten steel in the crystallizer is stable in the continuous casting process, and the thickness of the covering slag is uniformly distributed. Carrying out low-power detection on the continuous casting bloom; the cold acid dendrite corrosion is adopted to detect the blank shell thickness distribution condition of the cross section of a casting blank, and the result shows that the blank shell thickness of the 20CrMnTiH series gear steel continuous casting bloom produced by the technology is uniformly distributed along the circumferential direction of the cross section and the whole thickness is controlled to be 17.8 mm-20 mm; the quality of the corner part of the casting blank is good, metal in-situ scanning detection is carried out on the full section of the continuous casting blank, the homogeneity degree of the full section of the casting blank is 0.900-0.931, the density of the core part is 0.921-0.933, the center segregation and the center porosity of the corresponding pickling corrosion low-power grade are less than or equal to 0.5 grade, and no center shrinkage cavity exists.
The above embodiment illustrates that, by adopting the technical scheme of the invention, the casting blank quality of the gear steel bloom with the cross section of 360mm × 450mm is well controlled, the corner of the casting blank has zero defect, the thickness of the blank shell is uniformly distributed along the circumferential direction, the homogeneity of the whole cross section of the casting blank is good, the core looseness and the shrinkage cavity are effectively controlled, the core density of the casting blank is controlled at a high level, the quality rating indexes of the center looseness and the center segregation are controlled well, and other quality performances are all qualified.
Claims (5)
1. The continuous casting production method of the gear steel casting blank of the bloom is characterized in that: a tubular crystallizer is adopted, the technological parameters of cooling water of the crystallizer are controlled to be water flow of 3150L/min to 3350L/min and water pressure of 0.80MPa to 0.90 MPa;
the electromagnetic stirring of the crystallizer is low-position installation at the outlet of the crystallizer, the covering height of the electromagnetic stirring equipment of the crystallizer is 350mm, and the lower end of the electromagnetic stirring equipment of the crystallizer is flush with the lower opening of the crystallizer; measuring the gauss intensity of an electromagnetic stirring actual magnetic field of the crystallizer, and setting the stirring current with the gauss intensity of the actual stirring magnetic field being 280 +/-15 Gs, wherein the frequency of the stirring current is 2.4 Hz;
an electromagnetic stirring device is arranged between the secondary cooling zone and the solidification tail end, and the installation position of the electromagnetic stirring device is an area with a solidification linearity ratio of 0.45-0.47; actually measuring the Gaussian intensity of the stirring magnetic field, and setting the stirring current intensity according to the practical Gaussian intensity of the magnetic field of 200 +/-25 Gs, wherein the stirring current frequency is 7.0 Hz; the specific water amount of secondary cooling is 0.301L kg-1 Steel～0.323L·kg-1 SteelSetting is carried out;
for the 1 st heat of tundish casting, controlling the superheat degree of casting molten steel at 25-45 ℃; controlling the superheat degree of the casting molten steel at 15-35 ℃ for the 2 nd-N heats of the tundish casting;
the pulling speed is controlled between 0.45m/min and 0.55 m/min.
2. The continuous casting production method of a cogged bloom steel slab according to claim 1, characterized by: the corner fillet size of the tubular crystallizer is R20 mm.
3. The continuous casting production method of a cogged bloom steel slab according to claim 1, characterized by: the cooling water path of the tubular crystallizer is two-in and two-back, and is provided with two water inlets and two water outlets.
4. A continuous casting production method of a cogged steel ingot according to any one of claims 1 to 3, characterized by: the thickness of the blank shell is controlled to be 16-20 mm.
5. A continuous casting production method of a cogged steel ingot according to any one of claims 1 to 3, characterized by: the installation position of the electromagnetic stirring equipment between the secondary cooling zone and the solidification tail end is within a range of 10.0-11.0 m away from the liquid level of the crystallizer steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810700707.1A CN108705052B (en) | 2018-06-29 | 2018-06-29 | Continuous casting production method of cogged steel billets in bloom |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810700707.1A CN108705052B (en) | 2018-06-29 | 2018-06-29 | Continuous casting production method of cogged steel billets in bloom |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN108705052A CN108705052A (en) | 2018-10-26 |
| CN108705052B true CN108705052B (en) | 2020-02-04 |
Family
ID=63873309
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810700707.1A Active CN108705052B (en) | 2018-06-29 | 2018-06-29 | Continuous casting production method of cogged steel billets in bloom |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN108705052B (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109317628B (en) * | 2018-11-26 | 2021-02-19 | 攀钢集团攀枝花钢铁研究院有限公司 | YQ450NQR 1B-shaped steel bloom corner crack control method |
| CN109332619B (en) * | 2018-11-26 | 2021-02-19 | 攀钢集团攀枝花钢铁研究院有限公司 | YQ450NQR 1B-shaped steel bloom shell quality control method |
| CN109175279B (en) * | 2018-11-26 | 2021-02-09 | 攀钢集团攀枝花钢铁研究院有限公司 | YQ450NQR 1B-shaped steel bloom continuous casting production method |
| CN109382490B (en) * | 2018-11-26 | 2021-02-19 | 攀钢集团攀枝花钢铁研究院有限公司 | YQ450NQR 1B-shaped steel bloom surface quality control method |
| CN112151129B (en) * | 2020-09-01 | 2022-07-12 | 河钢乐亭钢铁有限公司 | Technological method for accurately setting width dimension of lower opening of continuous casting slab crystallizer |
| CN113953477B (en) * | 2021-10-27 | 2023-03-24 | 张家港宏昌钢板有限公司 | Core high-density continuous casting thick plate blank and production method thereof |
| CN115255304B (en) * | 2022-06-14 | 2023-10-10 | 江阴兴澄特种钢铁有限公司 | Continuous casting method for controlling macroscopic inclusion in steel |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104942252B (en) * | 2015-07-23 | 2017-03-08 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of method improving Properties of Heavy Rail Steel bloom internal soundness |
| CN105215309A (en) * | 2015-11-11 | 2016-01-06 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of method that big cross section Properties of Heavy Rail Steel center segregation of casting blank controls |
| CN105803149B (en) * | 2016-03-23 | 2018-05-25 | 攀钢集团攀枝花钢铁研究院有限公司 | The 35CrMo circular pipe blank equiaxial crystal ratio control methods of φ 280mm |
| CN107457379B (en) * | 2017-07-26 | 2019-07-23 | 山东钢铁股份有限公司 | A kind of production method of high-carbon high-alloy bearing steel large round billet |
| CN107790666A (en) * | 2017-10-27 | 2018-03-13 | 攀钢集团攀枝花钢铁研究院有限公司 | Large section Properties of Heavy Rail Steel continuous casting control method |
-
2018
- 2018-06-29 CN CN201810700707.1A patent/CN108705052B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN108705052A (en) | 2018-10-26 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108705052B (en) | Continuous casting production method of cogged steel billets in bloom | |
| CN109338035B (en) | Steel for wind driven generator gear box bearing and production method thereof | |
| CN110983178B (en) | Steel for ball screw bearing and manufacturing method thereof | |
| CN101289731B (en) | CrMnTi narrow hardenability strip pinion steels and method of manufacture | |
| CN102492894B (en) | The corrosion-resistant martensitic steel of high-dimensional stability and steel structure material preparation method thereof | |
| CN107619995A (en) | A kind of major diameter engineering mechanical hydraulic oil cylinder piston rod round steel and its manufacture method | |
| WO2017117883A1 (en) | Microalloyed steel for car carbon wheel hub bearing and manufacturing method therefor | |
| CN106048415B (en) | A kind of Ni microalloyings stone oil drill collar steel and preparation method thereof | |
| CN103276298A (en) | High-hardness high-tenacity cold and hot work die steel and production method thereof | |
| CN110983190A (en) | 645 MPa-level high-strength anti-seismic ribbed steel bar and production method thereof | |
| CN110000362B (en) | High-tungsten-vanadium high-speed steel wear-resistant roller and manufacturing method thereof | |
| CN115612920B (en) | Steel for flexible bearing of robot harmonic reducer and production method of steel | |
| WO2023029282A1 (en) | Production method for high-strength steel plate for engineering machinery | |
| CN114134403B (en) | Steel for large-specification wind power bearing rolling body and production method thereof | |
| CN110396648A (en) | A kind of special thick alloy mold steel plate of continuous casting billet production and its manufacturing method | |
| CN110205542A (en) | A kind of cold roll tool steel and preparation method thereof | |
| CN106834959A (en) | High hardness wear-resisting ball material steel and its production method | |
| CN111590040B (en) | Continuous casting production method of small square billets for improving quality of gear steel | |
| CN114150218A (en) | Q355NE hot-rolled round steel for high-speed rail bogie and production process | |
| CN106086682B (en) | A kind of high-strength die steel and its processing method | |
| CN108772542A (en) | The method that bloom continuous casting produces 20CrMo pinion steels | |
| CN108687315A (en) | The method that bloom continuous casting produces 22CrMo pinion steels | |
| CN108705051A (en) | 20CrMnTiH pinion steel bloom continuous casting production methods | |
| CN114892070B (en) | Sulfur-containing gear steel and production method thereof | |
| CN105568178A (en) | New manufacturing process of hot-rolled bar for carburized and quenched gear shaft of automobile transmission |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |