CN111270042A - Hydrogen induced crack control method for high-carbon equivalent steel - Google Patents
Hydrogen induced crack control method for high-carbon equivalent steel Download PDFInfo
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Abstract
The invention relates to a hydrogen induced crack control method of high-carbon equivalent steel, belonging to the technical field of metallurgy and rolling. The method comprises the following specific steps: (1) KR molten iron pretreatment and scrap steel preparation; (2) smelting in a converter; (3) LF refining; (4) RH vacuum refining; (5) continuous casting and pouring; (6) cutting the continuous casting blank with temperature; (7) stacking the continuous casting billets for slow cooling; (8) stacking the formed steel plates for slow cooling; (9) and (5) cutting the steel plate after slow cooling. Aiming at the characteristics of high-carbon equivalent steel, the invention realizes the hydrogen control of the whole process of the steelmaking process by the hydrogen absorption characteristics of each process of the converter smelting process and the dehydrogenation analysis of casting blanks, ensures that the hydrogen content of the high-carbon equivalent steel is effectively controlled, and performs classified slow cooling dehydrogenation after rolling aiming at high-carbon equivalent steel plates with different thickness specifications, thereby finally realizing the effective control of the hydrogen of the high-carbon equivalent steel plates; meanwhile, the cutting process is optimized and adjusted for solving the problem that hydrogen-induced cracks are generated in the high-carbon-equivalent steel plate in the machining process, and the occurrence probability of the hydrogen-induced cracks of the high-carbon-equivalent steel plate is reduced.
Description
Technical Field
The invention belongs to the technical field of metallurgy and rolling, and particularly relates to a hydrogen induced crack control method for high-carbon equivalent steel.
Background
At present, the knowledge of the influence of hydrogen-induced cracking of steel sheets on steel is well recognized in the industry. In order to ensure that the welding performance of the steel is controlled as low as possible, the hydrogen induced cracking control of the low-carbon equivalent steel is deeply researched and analyzed, and a corresponding control method is provided. The high-carbon equivalent steel has high content of easily segregated elements and strong crack sensitivity, so that hydrogen is easy to diffuse to a core segregation accumulation area in the steel and is more unfavorable for dehydrogenation; and the existence of hydrogen is superposed with the crack sensitivity of steel, so that the risk of hydrogen-induced cracking is further increased.
The invention patent CN107876720A discloses a production process of hydrogen-induced crack resistant C-Mn steel, wherein in the slab production process, high-superheat-degree and low-drawing-speed casting is adopted, and a strong cooling process is adopted to accelerate the solidification process and inhibit the segregation degree of carbon and manganese elements. And (3) rapidly cooling after rolling, wherein the cooling starting temperature is before austenite is transformed, and the cooling finishing temperature is after austenite is completely transformed, and the diffusion of elements is inhibited again through a large cooling rate. The invention controls the heat treatment of continuous casting and steel rolling, but does not describe how to control hydrogen in high carbon equivalent steel.
The invention discloses a Chinese patent (CN 108330411A) for producing high-quality C-Mn steel with hydrogen-induced cracking resistance, which improves the uniformity of a steel plate by reducing the segregation degree of the center of the steel plate, and the C-Mn steel produced by the method has good hydrogen-induced cracking resistance. However, specific control of hydrogen and crack-sensitive high carbon equivalent steel hydrogen induced cracking control are not explicitly described.
The Chinese invention patent (CN 105886909A) discloses a hydrogen induced cracking resistant steel plate for a pressure vessel and a manufacturing method thereof, which mainly have corresponding control requirements in the aspects of component design, smelting control, steel rolling process and heat treatment, but do not discuss the aspects of specific hydrogen control of molten steel, dehydrogenation of the steel plate and processing treatment on the steel with higher carbon equivalent and stronger crack sensitivity.
Disclosure of Invention
In order to solve the problem of hydrogen induced cracking of high carbon equivalent steel, a hydrogen induced cracking control method of high carbon equivalent steel is provided, and the hydrogen induced cracking control of the high carbon equivalent steel is realized through the processes of whole process hydrogen control of a converter flow, casting blank segregation control, slow cooling after rolling of steel plates with different specifications and thicknesses, steel plate preheating treatment before cutting and the like.
A hydrogen induced crack control method of high carbon equivalent steel comprises the following specific steps:
(1) KR molten iron pretreatment and scrap steel preparation; (2) smelting in a converter; (3) LF refining; (4) RH vacuum refining; (5) continuous casting and pouring; (6) cutting the continuous casting blank with temperature; (7) stacking the continuous casting billets for slow cooling; (8) stacking the formed steel plates for slow cooling; and (9) cutting the steel plate after slow cooling.
Preferably, the KR molten iron pretreatment and the scrap steel preparation are used for controlling the charging quality of molten iron and scrap steel, creating conditions for converter smelting and subsequent refining treatment, and preventing the function loss of a previous process from being superposed to a subsequent process, so that additional hydrogen addition and dehydrogenation of molten steel are caused; the S content of the molten iron after KR treatment is less than or equal to 0.003 percent, the molten iron is subjected to slag skimming treatment, and the exposed bright surface is more than or equal to 90 percent; the scrap steel is high-quality dry scrap steel.
Preferably, the cooling material in the converter smelting process adopts sintered ore, double-slag-making tapping is carried out, the end point (P) is less than or equal to 0.015 percent, the converter tapping (O) is less than or equal to 300ppm, the slag amount under the converter is strictly controlled to be less than or equal to 2 kg/ton steel, a turnover steel ladle is adopted, bottom blowing by-pass argon blowing is carried out before tapping, argon is normally blown in the tapping process, alloying is completed in the molten steel tapping process, the alloying must reach the lower limit of the required component requirement of a finished product, and the molten steel is prevented from being turned over greatly after tapping, and the diameter of the liquid level of the exposed molten steel is less than 10.
Preferably, hydrogen is effectively controlled in the LF refining process, alloying fine adjustment is completed in the early stage after LF refining molten steel enters a station, the molten steel is prevented from being exposed in the LF treatment process, the electrode is well submerged, feeding is prevented in the electrode heating process, the phenomenon that material crystal water is decomposed by electric arc heating to cause hydrogen increase of the molten steel is avoided, the argon is blown above the molten steel of an accident argon gun for protection, micro-positive pressure is formed, contact with air is prevented, the hydrogen is increased, and the soft blowing time after treatment is more than or equal to 15 min.
Preferably, the RH vacuum refining is carried out, the vacuum degree is less than or equal to 100Pa, and the RH end point H content is less than or equal to 1.5 ppm.
Preferably, in the continuous casting process, before the casting machine is started, argon is blown into the tundish, and after the liquid level of the tundish reaches 1/3, the tundish is started to be cast; covering agents are added for heat preservation treatment, and the steel liquid level of the tundish is prevented from being exposed in the pouring process; the tundish cover is sealed, argon is blown around the tundish cover for protection, the micro-positive pressure state in the tundish is realized, the process hydrogen increasing is less than 0.5ppm, and the tundish hydrogen determining (H) is less than or equal to 2 ppm; the pulling speed is constant, the superheat degree of the molten steel is less than or equal to 20 ℃ for pouring, and the fluctuation of the liquid level of the crystallizer is less than 2 mm; the single terms of A-type, B-type, C-type, D-type and Ds-type nonmetallic inclusions are less than or equal to 1.0 level, the sum of the single terms is less than or equal to 3.5 levels, and the casting blank segregation B-type is controlled to be less than or equal to 1.5 levels.
Preferably, the temperature of the continuous casting billet with the temperature is 250-400 ℃.
Preferably, the continuous casting billet stacking slow cooling process is carried out grading pit cooling according to carbon equivalent and thickness specifications. The carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, the thickness specification of the finished steel plate is more than or equal to 50mm, and the steel plate is slowly cooled for 96 hours in a temperature range of 460-650 ℃ (the hydrogen diffusion capability in the steel plate is strongest in the temperature range); the carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, the thickness specification of the finished steel plate is less than 50mm, and the steel plate is slowly cooled for 72 hours at the temperature of 460-650 ℃; the carbon equivalent CE is less than 0.60 percent and more than 0.40 percent, the thickness specification of the finished steel plate is more than or equal to 50mm, and the steel plate is slowly cooled for 72 hours at the temperature of 460-650 ℃; 0.40 percent and less than 0.60 percent of carbon equivalent CE, the thickness specification is less than 50mm, and the steel plate is slowly cooled for 48 hours at the temperature of 460-650 ℃.
Preferably, the formed steel plate stack is subjected to graded slow cooling dehydrogenation treatment according to different carbon equivalent and specifications. The carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, the thickness specification of the finished steel plate is more than or equal to 50mm, and the slow cooling is more than or equal to 96 hours in a temperature range of 460-650 ℃ (the diffusion capacity of hydrogen in the steel plate is strongest in the temperature range); the carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, the thickness specification is less than 50mm, and the slow cooling is carried out for more than or equal to 72 hours at the temperature of 460-650 ℃; the carbon equivalent CE is less than 0.60 percent and more than 0.40 percent, the thickness specification of the finished steel plate is more than or equal to 50mm, and the slow cooling is carried out for more than or equal to 72 hours at the temperature range of 460-650 ℃; the carbon equivalent CE is less than 0.40 percent and less than 0.60 percent, the thickness specification of the finished steel plate is less than 50mm, and the slow cooling is carried out for more than or equal to 48 hours at the temperature of 460-650 ℃.
Preferably, the graded preheating cutting is realized by combining the carbon equivalent distribution interval and the steel plate thickness specification in the steel plate cutting process after slow cooling.
Preferably, the steel sheet cutting of slowly-cooling back selects for use the operation of the double-cutting dolly of same rail, and concrete operating procedure is:
the front cutting trolley is used for preheating a high-carbon-equivalent steel plate, the rear cutting trolley is used for flame cutting, the steel plates with different carbon equivalents and thickness specifications (△ h) are preheated and cut, and the front and rear trolley distance (△ L), the moving speed (V) of the cutting trolley and the flame of the front cutting trolley are respectively utilized to adjust and control the contact surface (△ a) of the steel plates, so that the high-carbon-equivalent steel plate is cut and preheated, and hydrogen induced cracks are eliminated.
1)0.60 percent to 0.90 percent of carbon equivalent CE, and 50mm below specification of steel plates: the distance between the front trolley and the rear trolley is 400-800 mm, the cutting speed is 200-400 mm/min as an adjusting range, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front trolley and the rear trolley and the cutting speed are cooperatively adjusted according to the thickness of the steel plate, the distance gradually takes the upper limit as the specification is smaller, and the cutting speed is faster;
2) the carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, and the steel plate with the specification of more than 50 mm: the distance between the front and rear trolley spray heads is 0-400 mm, the cutting speed is 100-300 mm/min as an adjusting range, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front and rear trolleys and the cutting speed are adjusted cooperatively according to the thickness of the steel plate, the larger the specification, the lower limit is gradually taken, and the cutting speed is slowed down;
3) 0.40% < carbon equivalent CE < 0.60%, 50mm or less of steel plate: the distance between the spray heads of the front trolley and the rear trolley is 400-1000 mm, the cutting speed is 200-600 mm/min as an adjusting range, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front trolley and the rear trolley and the cutting speed are cooperatively adjusted according to the thickness of the steel plate, the distance gradually gets the upper limit when the specification is smaller, and the cutting speed is faster;
4) 0.40% < carbon equivalent CE < 0.60%, and 50mm or more of steel sheet: the distance between the front and rear car spray nozzles is 0-500 mm, the cutting speed is 100-400 mm/min as an adjusting range, the flame of the front car is preferably not blown to damage the steel plate surface, the distance between the front and rear cars and the cutting speed are adjusted cooperatively according to the thickness of the steel plate, the larger the specification, the lower limit is gradually taken, and the cutting speed is slowed down.
Preferably, the specific composition of the high carbon equivalent steel is as follows:
c: 0.12-0.30%, Si: 0.20 to 0.50%, Mn: 0.90-1.50%, Cr: 0.40-1.20%, Ni: 0.20 to 0.50%, Mo: 0.20-0.30%, V: 0.020 to 0.040%, Ti: 0.020 to 0.025%, Nb: 0.012-0.020%, B: 0.0010-0.0020%; the balance of Fe and inevitable impurity elements; the carbon equivalent CE is more than or equal to 0.40 percent and less than or equal to 0.90 percent, and the carbon equivalent calculation formula is Ceq ═ C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15.
The invention has the beneficial effects that:
(1) the system is used for systematically combing the hydrogen induced cracking conditions of high-carbon equivalent steel in the aspects of smelting, continuous casting, casting blank slow cooling, steel plate slow cooling, cutting and the like, and full-flow control measures and requirements are provided.
(2) The invention provides beneficial reference for smelting high-carbon equivalent steel in the converter process and controlling hydrogen in the steel plate cutting and processing process. The high carbon equivalent steel has higher content of easily segregated elements and crack sensitivity, and provides more strict requirements for hydrogen content, aiming at the characteristics of the high carbon equivalent steel, the invention realizes hydrogen control of the whole process of a steelmaking process by hydrogen absorption characteristics of each process of a converter smelting process and dehydrogenation analysis of a casting blank, ensures that the hydrogen content of molten steel and the casting blank is effectively controlled in the smelting and pouring processes of the high carbon equivalent steel, and provides guidance for avoiding hydrogen induced cracks of subsequent products; classified slow cooling dehydrogenation is carried out after high-carbon equivalent steel plates with different thickness specifications are rolled, and finally effective control of hydrogen of the high-carbon equivalent steel plates is realized; meanwhile, the cutting process of the high-carbon equivalent steel plate is optimized and adjusted for solving the problem that hydrogen-induced cracks are generated in the processing process of the high-carbon equivalent steel plate. The hydrogen control of the high carbon equivalent steel is realized, and the hydrogen-induced crack occurrence probability of the high carbon equivalent steel plate is reduced.
Drawings
In order to more clearly illustrate the embodiments or technical solutions in the prior art of the present invention, the drawings used in the description of the embodiments or prior art will be briefly described below, and it is obvious for those skilled in the art that other drawings can be obtained based on these drawings without creative efforts.
FIG. 1 is a schematic top plan view of a high carbon equivalent steel cutting preheat;
FIG. 2 is a schematic front view of the preheating of high carbon equivalent steel cutting.
In the figure, 1-high carbon equivalent steel plate, 2-trolley track, 3-front trolley, 4-rear trolley, 5-front trolley spray head and 6-rear trolley spray head.
Detailed Description
In order to make those skilled in the art better understand the technical solution of the present invention, the technical solution in the embodiment of the present invention will be clearly and completely described below with reference to the drawings in the embodiment of the present invention, and it is obvious that the described embodiment is only a part of the embodiment of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
A hydrogen induced cracking control method for high carbon equivalent steel comprises the following components:
c: 0.12%, Si: 0.20%, Mn: 0.90%, Cr: 0.40%, Ni: 0.20%, Mo: 0.20%, V: 0.020%, Ti: 0.020%, Nb: 0.012%, B: 0.0010%; the balance of Fe and inevitable impurity elements.
The method comprises the following specific steps:
(1) KR molten iron pretreatment and scrap steel preparation: the steel scrap is high-quality dry steel scrap, after KR treatment, the molten iron (S) is 0.002%, and slag removal treatment is carried out on the molten iron, so that the exposed bright surface is more than or equal to 90%.
(2) Smelting in a converter: the cooling material adopts sintered ore, double-slag-making tapping is carried out, the end point (P) is 0.012%, the converter tapping (O) is 260ppm, the converter slag-off quantity is 108kg, a turnover ladle is adopted, bottom blowing by-pass argon blowing is carried out before tapping, argon blowing is normally carried out in the tapping process, alloying is completed in the molten steel tapping process, and the diameter of the exposed molten steel liquid level is less than 10cm after tapping.
(3) LF refining: after molten steel enters a station, alloying fine adjustment is completed in the early stage, molten steel is prevented from being exposed in the LF treatment process, the submerged arc of the electrode is good, feeding is prevented in the electrode heating process, micro-positive pressure is formed by blowing argon over the molten steel of an accident argon gun for protection, and the soft blowing time is 15min after treatment.
(4) RH vacuum refining: controlling the vacuum degree to be 100Pa, the vacuum treatment time to be 20min and the H content at the RH end point to be 1.4 ppm.
(5) Continuous casting pouring: blowing argon in the tundish before casting by the casting machine, and after the liquid level of the tundish reaches 1/3, starting casting; covering agents are added for heat preservation treatment, and the steel liquid level of the tundish is prevented from being exposed in the pouring process; the tundish cover is sealed, argon is blown around the tundish cover for protection, the micro-positive pressure state in the tundish is realized, the process hydrogen increasing is less than 0.5ppm, and the tundish hydrogen determining (H) is 2 ppm; pouring at 20 ℃ with low superheat degree, keeping the pulling speed constant, and keeping the single items of nonmetallic inclusions of A class, B class, C class, D class and Ds class less than or equal to 1.0 grade and the sum less than or equal to 3.5 grade; controlling the casting blank segregation B class to be below 1.5 grade.
(6) Cutting the continuous casting blank with temperature: the cutting temperature was 310 ℃.
(7) Stacking and slow cooling of continuous casting billets: and (4) performing pit cooling on the finished steel plate, wherein the carbon equivalent CE is 0.41%, and the thickness specification of the steel plate is 40 mm. And after the casting blank is off line, slowly cooling the casting blank in a slow cooling pit at the temperature range of 460-650 ℃ for 48 h.
(8) Stacking and slow cooling the formed steel plates: and (4) carrying out slow cooling dehydrogenation treatment on the formed steel plate. Slowly cooling for 48 hours at the temperature of 460-650 ℃.
(9) And (2) slowly cooling the rear steel plate, namely, selecting a same-rail double-cutting trolley for operation, preheating the high-carbon equivalent steel plate by using a front cutting trolley, preheating and cutting the steel plate with different carbon equivalent and thickness specifications (△ h), and adjusting and controlling the distance (△ L) of the front and rear trolleys, the moving speed (V) of the cutting trolley and the contact surface (△ a) of the flame of the front cutting trolley and the steel plate to realize the cutting and preheating of the high-carbon equivalent steel plate and eliminate hydrogen-induced cracks, wherein the thickness (△ h) of the formed steel plate is 40mm, the carbon equivalent is 0.41%, the CE is less than 0.60% according to the carbon equivalent of 0.40% < CE, and the steel plate with the specification less than 50mm is that the distance between the front and rear trolley is 400-1000 mm, the cutting speed is adjusted within the range of 200-600 mm/min, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front and rear trolley and the cutting speed are cooperatively adjusted according to the thickness of the steel plate, the smaller distance gradually gets the upper limit, the cutting speed is 400 mm/600 mm, and.
Example 2
A hydrogen induced cracking control method for high carbon equivalent steel comprises the following components:
c: 0.21%, Si: 0.35%, Mn: 1.2%, Cr: 0.8%, Ni: 0.35%, Mo: 0.25%, V: 0.030%, Ti: 0.023%, Nb: 0.016%, B: 0.0015 percent; the balance of Fe and inevitable impurity elements.
The method comprises the following specific steps:
(1) KR molten iron pretreatment and scrap steel preparation: the steel scrap is high-quality dry steel scrap, after KR treatment, the molten iron (S) is 0.002%, and slag removal treatment is carried out on the molten iron, so that the exposed bright surface is more than or equal to 90%.
(2) Smelting in a converter: the cooling material adopts sintered ore, double-slag-making tapping is carried out, the end point (P) is 0.011 percent, the converter tapping (O) is 240ppm, the converter slag-off quantity is 105kg, a turnover ladle is adopted, bottom blowing by-pass argon blowing is carried out before tapping, argon is normally blown in the tapping process, alloying is completed in the molten steel tapping process, and the diameter of the exposed molten steel liquid level is less than 10cm after tapping.
(3) LF refining: after molten steel enters a station, alloying fine adjustment is completed in the early stage, molten steel is prevented from being exposed in the LF treatment process, the submerged arc of the electrode is good, feeding is prevented in the electrode heating process, micro-positive pressure is formed by blowing argon over the molten steel of an accident argon gun for protection, and the soft blowing time after treatment is 20 min.
(4) RH vacuum refining: controlling the vacuum degree to be 100Pa, the vacuum treatment time to be 25min and the H content at the RH end point to be 1.6 ppm.
(5) Continuous casting pouring: blowing argon in the tundish before casting by the casting machine, and after the liquid level of the tundish reaches 1/3, starting casting; covering agents are added for heat preservation treatment, and the steel liquid level of the tundish is prevented from being exposed in the pouring process; the tundish cover is sealed, argon is blown around the tundish cover for protection, the micro-positive pressure state in the tundish is realized, the process hydrogen increasing is less than 0.5ppm, and the tundish hydrogen determining (H) is 2 ppm; pouring at 20 ℃ with low superheat degree, keeping the pulling speed constant, and keeping the single items of nonmetallic inclusions of A class, B class, C class, D class and Ds class less than or equal to 1.0 grade and the sum less than or equal to 3.5 grade; controlling the casting blank segregation B class to be below 1.5 grade.
(6) Cutting the continuous casting blank with temperature: the cutting temperature was 280 ℃.
(7) Stacking and slow cooling of continuous casting billets: and (3) carrying out pit cooling on the finished steel plate, wherein the carbon equivalent CE is 0.65%, the thickness of the steel plate is 40mm, and after the casting blank is off-line, the casting blank is slowly cooled in a slow cooling pit for 72h at the temperature range of 460-650 ℃.
(8) Stacking and slow cooling the formed steel plates: and (3) carrying out slow cooling dehydrogenation treatment on the formed steel plate, and carrying out slow cooling for 72h at the temperature of 460-650 ℃.
(9) And (2) slowly cooling the rear steel plate, namely, selecting a same-rail double-cutting trolley for operation, preheating the high-carbon equivalent steel plate by using a front cutting trolley, preheating and cutting the steel plate with different carbon equivalent and thickness specifications (△ h), and adjusting and controlling the distance (△ L) of the front and rear trolleys, the moving speed (V) of the cutting trolley and the contact surface (△ a) of the flame of the front cutting trolley and the steel plate to realize the cutting and preheating of the high-carbon equivalent steel plate and eliminate hydrogen-induced cracks, wherein the thickness (△ h) of the formed steel plate is 40mm, the carbon equivalent is 0.65%, the CE (CE) of the carbon equivalent is less than or equal to 0.90% according to the ratio of 0.60% to 50mm, the distance between the front trolley and the rear trolley is 400-800 mm, the cutting speed is adjusted within the range of 200-400 mm/min, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front trolley and the rear trolley and the cutting speed are cooperatively adjusted according to the thickness of the steel plate, the distance between the smaller and the specification, the gradually increasing the cutting speed is 600 mm/.
Example 3
A hydrogen induced cracking control method for high carbon equivalent steel comprises the following components:
c: 0.30%, Si: 0.50%, Mn: 1.50%, Cr: 1.20%, Ni: 0.50%, Mo: 0.30%, V: 0.040%, Ti: 0.025%, Nb: 0.020%, B: 0.0020 percent; the balance of Fe and inevitable impurity elements.
The method comprises the following specific steps:
(1) KR molten iron pretreatment and scrap steel preparation: the steel scrap is high-quality dry steel scrap, after KR treatment, the molten iron (S) is 0.002%, and slag removal treatment is carried out on the molten iron, so that the exposed bright surface is more than or equal to 90%.
(2) Smelting in a converter: the cooling material adopts sintered ore, double-slag-making tapping is carried out, the end point (P) is 0.013%, the converter tapping (O) is 260ppm, the converter slag-off quantity is 110kg, a turnover ladle is adopted, bottom blowing by-pass argon blowing is carried out before tapping, argon blowing is normally carried out in the tapping process, alloying is completed in the molten steel tapping process, and the diameter of the exposed molten steel liquid level is less than 10cm after tapping.
(3) LF refining: after molten steel enters a station, alloying fine adjustment is completed in the early stage, molten steel is prevented from being exposed in the LF treatment process, the submerged arc of the electrode is good, feeding is prevented in the electrode heating process, micro-positive pressure is formed by blowing argon over the molten steel of an accident argon gun for protection, and the soft blowing time after treatment is 20 min.
(4) RH vacuum refining: controlling the vacuum degree to be 100Pa, the vacuum treatment time to be 30min and the H content at the RH end point to be 1.5 ppm.
(5) Continuous casting pouring: blowing argon in the tundish before casting by the casting machine, and after the liquid level of the tundish reaches 1/3, starting casting; covering agents are added for heat preservation treatment, and the steel liquid level of the tundish is prevented from being exposed in the pouring process; the tundish cover is sealed, argon is blown around the tundish cover for protection, the micro-positive pressure state in the tundish is realized, the process hydrogen increasing is less than 0.5ppm, and the tundish hydrogen determining (H) is 1.8 ppm; pouring at 20 ℃ with low superheat degree, keeping the pulling speed constant, and keeping the single items of nonmetallic inclusions of A class, B class, C class, D class and Ds class less than or equal to 1.0 grade and the sum less than or equal to 3.5 grade; controlling the casting blank segregation B class to be below 1.5 grade.
(6) Cutting the continuous casting blank with temperature: the cutting temperature was 310 ℃.
(7) Stacking and slow cooling of continuous casting billets: and (5) pit cooling the finished steel plate. The carbon equivalent CE is 0.89%, the thickness of the steel plate is 60mm, and the casting blank is subjected to slow cooling for 96 hours in a slow cooling pit at the temperature range of 460-650 ℃ after being off line.
(8) Stacking and slow cooling the formed steel plates: and (4) carrying out slow cooling dehydrogenation treatment on the formed steel plate. Slowly cooling for 96 hours at the temperature of 460-650 ℃.
(9) And (2) slowly cooling the rear steel plate, namely, selecting a same-rail double-cutting trolley for operation, preheating the high-carbon equivalent steel plate by using a front cutting trolley, preheating and cutting the steel plate with different carbon equivalent and thickness specifications (△ h), and adjusting and controlling the distance (△ L) of the front and rear trolleys, the moving speed (V) of the cutting trolley and the contact surface (△ a) of the flame of the front cutting trolley and the steel plate to realize the cutting and preheating of the high-carbon equivalent steel plate and eliminate hydrogen-induced cracks, wherein the thickness (△ h) of the formed steel plate is 60mm, the carbon equivalent is 0.89%, the carbon equivalent CE is more than or equal to 0.60% and less than or equal to 0.90%, the steel plate with the specification of more than 50mm is obtained by cooperatively adjusting the distance between the front and the rear trolley and the front trolley by taking the distance between the front and rear trolley and the front trolley, the cutting speed is 100-300 mm/min, the flame of the front trolley does not blow the steel plate surface, the distance between the front and the cutting speed is 300mm/min, the lower limit is obtained by cooperatively adjusting the distance according to the thickness of.
Comparative example
The high-carbon equivalent steel comprises the following components in percentage by weight:
c: 0.12%, Si: 0.20%, Mn: 0.90%, Ni: 0.20%, Mo: 0.25%, V: 0.025%, and the balance of Fe and inevitable impurity elements.
The method comprises the following specific steps:
(1) KR molten iron pretreatment and scrap steel preparation: the waste steel adopts high-quality dry waste steel, the molten iron (S) after KR treatment is 0.002 percent, the molten iron is subjected to slag skimming treatment, and the slag is removed after organization.
(2) Smelting in a converter: and (3) adopting ore as a cooling material, making double slag and tapping, wherein the final point (P) is 0.018%, the tapping (O) in the converter is 370ppm, the slag discharging amount in the converter is 250kg, adopting a turnover ladle, and blowing argon after tapping.
(3) LF refining: after molten steel enters a station, alloying fine adjustment is completed in the early stage, molten steel is prevented from being exposed in the LF treatment process, the submerged arc of the electrode is good, feeding is prevented in the electrode heating process, and the soft blowing time is 20min after treatment.
(4) RH vacuum refining: controlling the vacuum degree to be 100Pa, the vacuum treatment time to be 30min and the H content at the RH end point to be 2.1 ppm.
(5) Continuous casting pouring: blowing argon into the tundish before casting by a casting machine, adding a covering agent for heat preservation treatment, and completely eradicating the steel liquid level of the tundish from being exposed in the casting process; pouring at 25 ℃ with low superheat degree, keeping the pulling speed constant, and keeping the single items of nonmetallic inclusions of A class, B class, C class, D class and Ds class less than or equal to 1.0 grade and the sum less than or equal to 3.5 grade; controlling the casting blank segregation B class to be below 1.5 grade.
(6) Cutting the continuous casting blank with temperature: the cutting temperature was 280 ℃.
(7) Stacking and slow cooling of continuous casting billets: and (5) pit cooling the finished steel plate. The carbon equivalent CE is 0.34 percent, the thickness of the steel plate is 60mm, and after the casting blank is off-line, the casting blank is slowly cooled for 50 hours in a slow cooling pit at the temperature range of 460-650 ℃.
(8) And (3) cutting the steel plate after slow cooling: and cutting by adopting a single cutting trolley.
The products prepared in example 1, example 2, example 3 and comparative example were tested and the test results are shown in table 1 below:
TABLE 1 results of the measurements
| Detecting items | Example 1 | Example 2 | Example 3 | Comparative example |
| Percentage of weld cracking% | 0 | 0 | 0 | 0.5 |
| Percent of pass of flaw detection | 100 | 100 | 100 | 98.8 |
As can be seen from the detection data in Table 1, the hydrogen induced cracking control method for the high carbon equivalent steel can effectively avoid the occurrence of hydrogen induced cracking.
Although the present invention has been described in detail by referring to the drawings in connection with the preferred embodiments, the present invention is not limited thereto. Various equivalent modifications or substitutions can be made on the embodiments of the present invention by those skilled in the art without departing from the spirit and scope of the present invention, and these modifications or substitutions are within the scope of the present invention/any person skilled in the art can easily conceive of the changes or substitutions within the technical scope of the present invention. Therefore, the protection scope of the present invention shall be subject to the protection scope of the claims.
Claims (10)
1. A hydrogen induced crack control method of high carbon equivalent steel is characterized by comprising the following specific steps:
(1) KR molten iron pretreatment and scrap steel preparation; (2) smelting in a converter; (3) LF refining; (4) RH vacuum refining; (5) continuous casting and pouring; (6) cutting the continuous casting blank with temperature; (7) stacking the continuous casting billets for slow cooling; (8) stacking the formed steel plates for slow cooling; (9) and (5) cutting the steel plate after slow cooling.
2. The method for controlling the hydrogen induced cracking of the high carbon equivalent steel according to claim 1, wherein the KR molten iron pretreatment and the scrap steel preparation are used for controlling the charging quality of the molten iron and the scrap steel, the S (S) of the molten iron after the KR treatment is less than or equal to 0.003 percent, the molten iron is subjected to slag removal treatment, and the bright surface exposure is more than or equal to 90 percent; the waste steel is high-quality dry waste steel.
3. The method for controlling hydrogen induced cracking of high carbon equivalent steel according to claim 1, wherein the cooling material in the converter smelting process adopts sintered ore to produce double-slag steel, the end point [ P ] is less than or equal to 0.015 percent, the converter steel tapping [ O ] is less than or equal to 300ppm, the slag amount in the converter is strictly controlled to be less than or equal to 2 kg/ton of steel, a turnover ladle is adopted, bottom blowing is carried out before steel tapping, argon is blown by bypass, the argon is normally blown in the steel tapping process, and the diameter of the liquid level of the exposed molten steel after steel tapping is less than 10 cm.
4. The method for controlling the hydrogen induced cracking of the high carbon equivalent steel as claimed in claim 1, wherein alloying fine adjustment is completed in the early stage after refined molten steel enters a station in the LF refining process, molten steel is prevented from being exposed in the LF treatment process, argon is blown above the molten steel of an accident argon gun for protection, and the soft blowing time after treatment is more than or equal to 15 min.
5. The method for controlling hydrogen induced cracking of high carbon equivalent steel according to claim 1, wherein the RH vacuum refining is performed with a degree of vacuum of 100Pa or less and an RH end point H content of 1.5ppm or less.
6. The method for controlling hydrogen induced cracking of high carbon equivalent steel according to claim 1, wherein in the continuous casting process, before the casting machine starts casting, the tundish blows argon, and after the liquid level of the tundish reaches 1/3, the structure starts casting; covering agents are added for heat preservation treatment, and the steel liquid level of the tundish is prevented from being exposed in the pouring process; the tundish cover is sealed, the periphery is protected by blowing argon, and the hydrogen (H) of the tundish is less than or equal to 2 ppm; the pulling speed is constant, the superheat degree of the molten steel is less than or equal to 20 ℃ for pouring, and the fluctuation of the liquid level of the crystallizer is less than 2 mm; the single terms of A-type, B-type, C-type, D-type and Ds-type nonmetallic inclusions are less than or equal to 1.0 level, the sum of the single terms is less than or equal to 3.5 levels, and the casting blank segregation B-type is controlled to be less than or equal to 1.5 levels.
7. The method for controlling hydrogen induced cracking of high carbon equivalent steel according to claim 1, wherein the slab temperature cutting temperature is 250 to 400 ℃.
8. The method for controlling hydrogen induced cracking of high carbon equivalent steel according to claim 1, wherein the slab stacking slow cooling process is classified pit cooling according to carbon equivalent and thickness specifications; the carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, the thickness specification of the finished steel plate is more than or equal to 50mm, and the steel plate is slowly cooled for 96 hours at the temperature of 460-650 ℃; the carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, the thickness specification of the finished steel plate is less than 50mm, and the steel plate is slowly cooled for 72 hours at the temperature of 460-650 ℃; the carbon equivalent CE is less than 0.60 percent and more than 0.40 percent, the thickness specification of the finished steel plate is more than or equal to 50mm, and the steel plate is slowly cooled for 72 hours at the temperature of 460-650 ℃; 0.40 percent and less than 0.60 percent of carbon equivalent CE, the thickness specification is less than 50mm, and the steel plate is slowly cooled for 48 hours at the temperature of 460-650 ℃.
9. The method for controlling hydrogen induced cracking of high carbon equivalent steel according to claim 1, wherein the formed steel plate stack is subjected to graded slow cooling dehydrogenation treatment according to different carbon equivalent and specification; the carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, the thickness specification of the finished steel plate is more than or equal to 50mm, and the slow cooling is carried out for more than or equal to 96 hours at the temperature of 460-650 ℃; the carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, the thickness specification is less than 50mm, and the slow cooling is carried out for more than or equal to 72 hours at the temperature of 460-650 ℃; the carbon equivalent CE is less than 0.60 percent and more than 0.40 percent, the thickness specification of the finished steel plate is more than or equal to 50mm, and the slow cooling is carried out for more than or equal to 72 hours at the temperature range of 460-650 ℃; the carbon equivalent CE is less than 0.40 percent and less than 0.60 percent, the thickness specification of the finished steel plate is less than 50mm, and the slow cooling is carried out for more than or equal to 48 hours at the temperature of 460-650 ℃.
10. The method for controlling hydrogen induced cracking of high carbon equivalent steel according to claim 1, wherein graded preheating cutting is realized in combination with a carbon equivalent distribution interval and a steel plate thickness specification in the steel plate cutting process after slow cooling;
further preferably, the steel plate cutting after slow cooling selects the operation of the same-rail double-cutting trolley, and the specific operation steps are as follows:
the front cutting trolley is used for preheating the high-carbon-equivalent steel plate, the rear cutting trolley is used for flame cutting, the steel plates with different carbon equivalents and thicknesses of △ h are preheated and cut, and the cutting preheating of the high-carbon-equivalent steel plate is realized and hydrogen-induced cracks are eliminated by respectively adjusting and controlling the distance △ L between the front and rear trolleys, the moving speed V of the cutting trolley and the contact surface △ a of the flame of the front cutting trolley and the steel plates;
1)0.60 percent to 0.90 percent of carbon equivalent CE, and 50mm below specification of steel plates: the distance between the front trolley and the rear trolley is 400-800 mm, the cutting speed is 200-400 mm/min as an adjusting range, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front trolley and the rear trolley and the cutting speed are cooperatively adjusted according to the thickness of the steel plate, the distance gradually takes the upper limit as the specification is smaller, and the cutting speed is faster;
2) the carbon equivalent CE is more than or equal to 0.60 percent and less than or equal to 0.90 percent, and the steel plate with the specification of more than 50 mm: the distance between the front and rear trolley spray heads is 0-400 mm, the cutting speed is 100-300 mm/min as an adjusting range, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front and rear trolleys and the cutting speed are adjusted cooperatively according to the thickness of the steel plate, the larger the specification, the lower limit is gradually taken, and the cutting speed is slowed down;
3) 0.40% < carbon equivalent CE < 0.60%, 50mm or less of steel plate: the distance between the spray heads of the front trolley and the rear trolley is 400-1000 mm, the cutting speed is 200-600 mm/min as an adjusting range, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front trolley and the rear trolley and the cutting speed are cooperatively adjusted according to the thickness of the steel plate, the distance gradually gets the upper limit when the specification is smaller, and the cutting speed is faster;
4) 0.40% < carbon equivalent CE < 0.60%, and 50mm or more of steel sheet: the distance between the front and rear trolley spray heads is 0-500 mm, the cutting speed is 100-400 mm/min as an adjusting range, the flame of the front trolley is preferably not blown to damage the steel plate surface, the distance between the front and rear trolleys and the cutting speed are adjusted cooperatively according to the thickness of the steel plate, the larger the specification, the lower limit is gradually taken, and the cutting speed is slowed down;
further preferably, the high carbon equivalent steel has the following specific component proportions:
c: 0.12-0.30%, Si: 0.20 to 0.50%, Mn: 0.90-1.50%, Cr: 0.40-1.20%, Ni: 0.20 to 0.50%, Mo: 0.20-0.30%, V: 0.020 to 0.040%, Ti: 0.020 to 0.025%, Nb: 0.012-0.020%, B: 0.0010-0.0020%; the balance of Fe and inevitable impurity elements; the carbon equivalent CE is more than or equal to 0.40 percent and less than or equal to 0.90 percent.
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