CN105018862A - High-toughness steel plate 140 mm thick and manufacturing method thereof - Google Patents
High-toughness steel plate 140 mm thick and manufacturing method thereof Download PDFInfo
- Publication number
- CN105018862A CN105018862A CN201510403342.2A CN201510403342A CN105018862A CN 105018862 A CN105018862 A CN 105018862A CN 201510403342 A CN201510403342 A CN 201510403342A CN 105018862 A CN105018862 A CN 105018862A
- Authority
- CN
- China
- Prior art keywords
- temperature
- steel plate
- steel
- heating
- less
- 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.)
- Granted
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a high-toughness steel plate 140 mm thick. The high-toughness steel plate 140 mm thick comprises chemical components including, in percentage by mass, 0.13%-0.15% of C, 0.50%-0.80% of Si, 0.40%-0.65% of Mn, 0.20% of Ni or less, 1.30%-1.50% of Cr, 0.45%-0.65% of Mo, 0.005%-0.020% of Nb, 0.0002% of H or less, 0.0020% of O or less, 0.0040% of N or less, and 0.020%-0.050% of Alt, with the balance being Fe and inevitable impurity elements. The raw materials are sequentially subjected to KR molten iron pretreatment, smelting with a converter, LF refining, RH vacuum degassing, continuous casting, covered slow-cooling, heating, rolling, covered heaped slow cooling and heat treatment. The minus 18 DEG C transverse impact property of the core portion of the obtained steel plate is good, and the performance of a steel billet is excellent after maximum simulation welding and minimum simulation welding.
Description
Technical field
The invention belongs to steel plate and manufacture field, being specifically related to a kind of thickness is 140mm ductility steel plate and manufacture method thereof.
Background technology
1.25Cr0.5MoSi steel plate is widely used in manufacturing oil, chemical industry, coal converting apparatus.It is rapid that current China's oil, chemical industry and coal transform industry development, and scrap build project is more, larger to the demand of this steel.Because this steel is at high temperature, high pressure, is on active service with hydrogen contact environment, working conditions is severe, and likely uses at low ambient temperatures according to operating mode difference, and therefore requirement has higher intensity, good toughness, excellent welding property and anti-temper embrittlement performance.
Summary of the invention
Technical problem to be solved by this invention provides a kind of thickness to be the steel plate of 140mm for existing 1.25Cr0.5MoSi steel plate use situation, use as petrochemical industry equipment steel, there is excellent low-temperature impact toughness, anti-lamellar tearing performance, welding property is good, steel plate thickness direction hardness is even, and comprehensive mechanical property is excellent.
Another technical problem to be solved by this invention provides a kind of manufacture method manufacturing above-mentioned thick tank plate for above-mentioned prior art present situation.
The present invention solves the problems of the technologies described above adopted technical scheme, a kind of 140mm thickness ductility steel plate, the chemical composition of this steel plate is C:0.13 ~ 0.15% by mass percentage, Si:0.50 ~ 0.80%, Mn:0.40 ~ 0.65%, P :≤0.006%, S :≤0.001%, Ni :≤0.20%, Cr:1.30 ~ 1.50%, Mo:0.45 ~ 0.65%, Nb:0.005 ~ 0.020%, Sb :≤0.003%, Sn :≤0.010%, As :≤0.012%, H :≤0.0002%, O :≤0.0020%, N :≤0.0040%, Alt:0.020 ~ 0.050%, surplus is Fe and inevitable impurity element.
Further, 140mm thickness ductility steel plate of the present invention, its-18 DEG C, heart portion horizontal summer than v-notch ballistic work >=120J, steel plate full thickness direction Z-direction performance >=50%.
The chemical composition of 140mm thickness ductility steel plate of the present invention is determined like this:
In steel plate composition, C can significantly improve intensity and the hardness of steel plate, but has disadvantageous effect to plasticity and toughness, and C can increase hardening capacity simultaneously; Si uses mainly as reductive agent during steel-making and reductor, has certain solution strengthening effect, but as the low-temperature flexibility of steel caused to reduce more than 0.80%, so Si controls about 0.6%; Mn improves the intensity of steel by solution strengthening, also favourable to toughness; Ni can improve toughness and the plasticity of steel, also gain in strength, but too high Ni can increase cost simultaneously, and also can destroy the performance of steel plate itself, Ni of the present invention controls below 0.20% simultaneously; The hardening capacity that Cr can significantly improve, improves intensity and the hardness of steel, improves temper resistance, but reduce toughness and the plasticity of steel simultaneously; It is favourable that Cu and Ni forms the high temperature creep property of precipitated phase Ni3Cu to steel; Mo is present in sosoloid and carbide, can improve hardening capacity and intensity, improves temper resistance; P, S are harmful elements, and P increases the fragility of steel, reduce the welding property of steel, reduce plasticity and cold-forming property, and S reduces ductility and the toughness of steel, causes crackle, therefore reduce P, S content as far as possible in hot procedure; Nb forms Nb(N, C) precipitated phase raising recrystallization temperature, fining austenite grains, effectively can improve intensity and the toughness of steel; Sb, Sn, As are harmful elements, easily at grain boundary segregation, reduce the anti-temper embrittlement performance of steel, should reduce as far as possible; O, N elemental gas should reduce as far as possible, improves the purity of steel, reduces inclusion content; H increases the hydrogen embrittlement tendency of steel, should reduce its content as far as possible; Alt and oxygen have very strong avidity to add mainly as reductor, and the AlN that Alt and N is formed can fining austenite grains.
The technical scheme that the present invention solves another technical problem is to provide a kind of manufacture method of above-mentioned 140mm thickness ductility steel plate, specific as follows:
Processing step is as follows: raw materials for metallurgy successively through KR hot metal pretreatment, converter smelting: skim, tapping temperature 1610 ~ 1640 DEG C, converter tapping P≤0.005%, converter tapping temperature is 1610 ~ 1650 DEG C; LF refining: the white slag hold-time is not less than 25min, total refining time is not less than 45min, skims during molten steel S≤0.003%; RH vacuum deaeration refining: vacuum tightness≤66Pa, the vacuum hold-time is broken empty after more than 20min; Continuous casting, produce and meet the continuously cast bloom that chemical composition requires, thickness is 450mm or more, to continuously cast bloom covering slow cooling more than 72 hours, covering is the H content in order to reduce steel billet further, slow cooling terminates to clear up continuously cast bloom surface band temperature afterwards, guarantee that continuously cast bloom surface flawless etc. affects the defect existence of plate surface quality, cleaning temperature remains on more than 100 DEG C; Reheat continuously cast bloom subsequently, adopt zone heating mode: heating rate is 10 ~ 11min/cm, preheating section temperature is 650 ~ 900 DEG C, preheating section insulation 3 ~ 3.5min/cm, and the first heating zone temperature is 1000 ~ 1200 DEG C, first heating zone insulation 3 ~ 3.5min/cm, second heating zone temperature is 1200 ~ 1260 DEG C, second heating zone insulation 2 ~ 3min/cm, and soaking zone temperature is 1150 ~ 1270 DEG C, soaking zone insulation 2 ~ 3min/cm, tapping temperature 1100 ~ 1260 DEG C; Be rolled steel billet after coming out of the stove: start rolling temperature is 1050 ~ 1100 DEG C, single pass draught is 8% ~ 20%, and the overall compression ratio of rolling is 3 ~ 5, finishing temperature 850 ~ 900 DEG C; After rolling completes, steel plate rolls off the production line when surface temperature 400 ~ 500 DEG C, the slow cooling of covering heap, slow cooling more than 48 hours, and the object that steel plate rolls rear slow cooling fully reduces H content residual in steel plate, weakens the harm of H; Finally carry out normalizing and tempering thermal treatment successively to steel billet, wherein, normalizing Heating temperature is 920 ~ 950 DEG C, and normalizing soaking time is 1.8 ~ 3min/mm, is quickly cooled to less than 200 DEG C after coming out of the stove with water, water-cooled speed >=0.5 DEG C/s; Tempering Heating temperature is 710 ~ 750 DEG C, and tempering insulation time is 3 ~ 4.5min/mm, cools after coming out of the stove, and namely obtains steel plate finished product.
Compared with prior art, the present invention has following features:
The present invention relates to a kind of 140mm thickness 1.25Cr0.5MoSi steel plate, this steel plate not only thickness is large, anti-temper embrittlement excellent performance, welding property is good and heart portion low temperature impact properties is very high, it is the best 140mm thickness 1.25Cr0.5MoSi steel plate of current heart portion impact property,-18 DEG C of horizontal summers of thickness of slab 1/2 position are than v-notch ballistic work >=120J, impact value fluctuation is little, steel plate full thickness direction Z-direction performance >=50%, steel plate whole plate hardness is even, steel plate thickness direction difference of hardness≤10HB, Plate Welding is functional, the Main Mechanical of steel plate meets 1.25Cr0.5MoSi, SA387Gr11CL2, the different trade mark of the different standardss such as 14Cr1MoR faces the technical requirements of hydrogen steel plate.
To achieve these goals, the present invention adopts the component of optimization, and the continuously cast bloom that the present invention produces has low center segregation and center porosity, and internal soundness is good.The patent of invention being CN102732810B with notification number adopts VD refining and die casting to compare, and the present invention adopts RH vacuum outgas and continuous casting to produce, and can obtain lower hydrogen richness and guarantee that steel plate has higher resistance against hydrogen cracking ability.The internal soundness of continuously cast bloom is as obviously few than static ingot in segregation, the defect such as loose, is conducive to obtaining excellent steel plate heart portion performance.In addition, continuous casting process is adopted to produce the cost of steel plate also far below die casting process.
Before steel plate rolling, steel plate is reheated, and adopt stepwise heating mode, for the continuous casting steel billet of heavy thickness, the temperature difference in surface and heart portion is larger, temperature is with thickness formula change in gradient, this also causes the crystalline phase of steel to be organized on thickness there are differences, and be difficult to ensure the homogeneous of performance in steel table, especially heart portion performance is difficult to control.Adopt Multi-stage heating mode, Heating temperature and the soaking time in corresponding each stage are set according to the Composition Design of steel, eliminate the temperature difference between steel surface and heart portion as far as possible, ensure that the performance of the whole plate of final steel plate is homogeneous.
In addition, reheating of above-mentioned stepwise heating mode is the prerequisite of the large pressure rolling of high temperature thereupon carried out, all to eliminate difference in table, obtaining the steel rolling of homogeneous microstructure, the large pressure of high temperature fully ensures that rolling load can penetrate into blank heart portion, guarantee the refinement of Plate Steel core structure, improving heart portion performance, laying the first stone for obtaining good anti-temper embrittlement ability.
Owing to adopting the large pressure rolling of high temperature, fully ensure that rolling load can penetrate into blank heart portion, guarantees the refinement of Plate Steel core structure.Other steel mills adopt this steel grade of II type controlled rolling explained hereafter, and shortcoming is that rolling time is long, production efficiency low and also when rolling heavy thickness steel plate draught little, steel plate heart portion performance is difficult to guarantee.
The thermal treatment process of steel plate of the present invention adopts the Particular craft of normalizing+shrend+tempering fast, by normalizing first crystal grain thinning, non-uniform components, then by rational temper, the normalizing formerly carried out and water quenching technology can reduce segregation phenomena and the out-phase organization formation of element in drawing process as much as possible, make last crystalline phase evenly single, thus guarantee the heart portion low-temperature impact toughness of steel plate, enable this steel plate be suitable for being suitable under low temperature severe environment, room temperature tensile and Z-direction excellent property, also improve the anti-temper embrittlement ability of steel simultaneously.
Embodiment
Below in conjunction with embodiment, the present invention is described in further detail.
Embodiment 1
The 140mm thickness ductility steel plate of the present embodiment, its chemical composition is by mass percentage: C:0.14%, Si:0.59%, Mn:0.47%, P:0.004%, S:0.001%, Ni:0.19%, Cr:1.40%, Mo:0.63%, Nb:0.017%, Sb:0.0009%, Sn:0.002%, As:0.0042%, H:0.0001%, O:0.002%, N:0.0035%, Alt:0.028%, surplus is Fe and inevitable impurity element.
The manufacturing process of this steel plate is, by the chemical composition configuration raw materials for metallurgy of above-mentioned steel plate finished product, successively through KR hot metal pretreatment, and converter smelting: skim, tapping temperature 1610 ~ 1640 DEG C, converter tapping P≤0.005%, converter tapping temperature is 1610 ~ 1650 DEG C; LF refining: the white slag hold-time is not less than 25min, total refining time is not less than 45min, skims during molten steel S≤0.003%; RH vacuum deaeration refining: vacuum tightness≤66Pa, the vacuum hold-time is broken empty after more than 20min; Continuous casting, produce and meet that chemical composition requires, thickness is the thick continuously cast bloom of 450mm, to continuously cast bloom covering slow cooling 72 hours, to reduce the H content of steel billet further, slow cooling terminates to clear up continuously cast bloom surface band temperature afterwards, guarantee that continuously cast bloom surface flawless etc. affects the defect existence of plate surface quality, cleaning temperature remains on more than 100 DEG C; Reheat continuously cast bloom subsequently, adopt zone heating mode: heating rate is 11min/cm, preheating section temperature is 800 DEG C, preheating section insulation 3min/cm, and the first heating zone temperature is 1000 DEG C, first heating zone insulation 3.5min/cm, second heating zone temperature is 1260 DEG C, the second heating zone insulation 2min/cm, and soaking zone temperature is 1240 DEG C, soaking zone insulation 2.5min/cm, tapping temperature 1260 DEG C; After coming out of the stove, steel billet is through high pressure water (pressure >=21MPa) de-scaling, is rolled afterwards: start rolling temperature is 1050 ~ 1100 DEG C, and previous three passes adopts large pressure, and single pass draught is 8% ~ 20%, and the overall compression ratio of rolling is 3.16, finishing temperature 850 ~ 900 DEG C; After rolling completes, steel plate rolls off the production line when surface temperature 400 ~ 500 DEG C, the slow cooling of covering heap, slow cooling more than 48 hours, and the object that steel plate rolls rear slow cooling fully reduces H content residual in steel plate, weakens the harm of H; Finally carry out normalizing and tempering thermal treatment successively to steel billet, steel are sent into the thick fire heating of continuous oven, holding temperature 930 DEG C, time inside furnace 2min/mm, use quenching press to quench after coming out of the stove, rapid water is chilled to less than 200 DEG C, water-cooled speed >=0.5 DEG C/s; After water-cooled, enter continuous oven and carry out temper, tempering Heating temperature is 730 DEG C, and tempering time inside furnace is 3.5min/mm, cools after coming out of the stove, and namely obtains steel plate finished product.
Testing identity, the steel plate in the present embodiment has very high low-temperature impact work and numerical fluctuations is less, yield strength >=400MPa, tensile strength >=520MPa.Adopt normalizing (accelerating cooling)+tempering process, the whole plate mechanical property of steel plate is even, and concrete mechanical property is in table 1.
Embodiment 2
The 140mm thickness ductility steel plate of the present embodiment, its chemical composition is by mass percentage: C:0.15%, Si:0.61%, Mn:0.48%, P:0.005%, S:0.001%, Ni:0.18%, Cr:1.42%, Mo:0.62%, Nb:0.016%, Sb:0.001%, Sn:0.0019%, As:0.0042%, H:0.00008%, O:0.0018%, N:0.0030%, Alt:0.030%, surplus is Fe and inevitable impurity element.
The manufacturing process of this steel plate is, by the chemical composition configuration raw materials for metallurgy of above-mentioned steel plate finished product, successively through KR hot metal pretreatment, and converter smelting: skim, tapping temperature 1610 ~ 1640 DEG C, converter tapping P≤0.005%, converter tapping temperature is 1610 ~ 1650 DEG C; LF refining: the white slag hold-time is not less than 25min, total refining time is not less than 45min, skims during molten steel S≤0.003%; RH vacuum deaeration refining: vacuum tightness≤66Pa, the vacuum hold-time is broken empty after more than 20min; Continuous casting, produce and meet that chemical composition requires, thickness is the thick continuously cast bloom of 450mm, to continuously cast bloom covering slow cooling 72 hours, to reduce the H content of steel billet further, slow cooling terminates to clear up continuously cast bloom surface band temperature afterwards, guarantee that continuously cast bloom surface flawless etc. affects the defect existence of plate surface quality, cleaning temperature remains on more than 100 DEG C; Reheat continuously cast bloom subsequently, adopt zone heating mode: heating rate is 10min/cm, preheating section temperature is 750 DEG C, preheating section insulation 3.5min/cm, and the first heating zone temperature is 1180 DEG C, first heating zone insulation 3.5min/cm, second heating zone temperature is 1250 DEG C, the second heating zone insulation 3min/cm, and soaking zone temperature is 1220 DEG C, soaking zone insulation 2.5min/cm, tapping temperature 1260 DEG C; After coming out of the stove, steel billet is through high pressure water (pressure >=21MPa) de-scaling, is rolled afterwards: start rolling temperature is 1050 ~ 1100 DEG C, and previous three passes adopts large pressure, and single pass draught is 8% ~ 20%, and the overall compression ratio of rolling is 3.6, finishing temperature 850 ~ 900 DEG C; After rolling completes, steel plate rolls off the production line when surface temperature 400 ~ 500 DEG C, the slow cooling of covering heap, slow cooling more than 48 hours, and the object that steel plate rolls rear slow cooling fully reduces H content residual in steel plate, weakens the harm of H; Finally carry out normalizing and tempering thermal treatment successively to steel billet, steel are sent into the thick fire heating of continuous oven, holding temperature 920 DEG C, time inside furnace 2.5min/mm, use quenching press to quench after coming out of the stove, rapid water is chilled to less than 200 DEG C, water-cooled speed >=0.5 DEG C/s; After water-cooled, enter continuous oven and carry out temper, tempering Heating temperature is 750 DEG C, and tempering time inside furnace is 3.5min/mm, cools after coming out of the stove, and namely obtains steel plate finished product.
The present embodiment and embodiment 1 check the state of sample blanks there are differences, and concrete difference is as follows:
In order to simulate stress-removal treating processes after Plate Welding, sample blanks from after steel plate is taken off first again in bogey according to 675 DEG C of insulations 26 hours, i.e. maximum analog postweld heat treatment, and then carry out mechanical properties test.
Testing identity, the steel plate in the present embodiment has very high low-temperature impact work and numerical fluctuations is less, yield strength >=380MPa, tensile strength >=550MPa.Adopt normalizing (accelerating cooling)+tempering process, the whole plate mechanical property of steel plate is even, and concrete mechanical property is in table 1.
Embodiment 3
The 140mm thickness ductility steel plate of the present embodiment, its chemical composition is by mass percentage: C:0.15%, Si:0.61%, Mn:0.48%, P:0.005%, S:0.001%, Ni:0.18%, Cr:1.42%, Mo:0.62%, Nb:0.015%, Sb:0.001%, Sn:0.0019%, As:0.004%, H:0.00008%, O:0.0016%, N:0.0033%, Alt:0.030%, surplus is Fe and inevitable impurity element.
The manufacturing process of this steel plate is, by the chemical composition configuration raw materials for metallurgy of above-mentioned steel plate finished product, successively through KR hot metal pretreatment, and converter smelting: skim, tapping temperature 1610 ~ 1640 DEG C, converter tapping P≤0.005%, converter tapping temperature is 1610 ~ 1650 DEG C; LF refining: the white slag hold-time is not less than 25min, total refining time is not less than 45min, skims during molten steel S≤0.003%; RH vacuum deaeration refining: vacuum tightness≤66Pa, the vacuum hold-time is broken empty after more than 20min; Continuous casting, produce and meet that chemical composition requires, thickness is the thick continuously cast bloom of 450mm, to continuously cast bloom covering slow cooling 72 hours, to reduce the H content of steel billet further, slow cooling terminates to clear up continuously cast bloom surface band temperature afterwards, guarantee that continuously cast bloom surface flawless etc. affects the defect existence of plate surface quality, cleaning temperature remains on more than 100 DEG C; Reheat continuously cast bloom subsequently, adopt zone heating mode: heating rate is 10min/cm, preheating section temperature is 750 DEG C, preheating section insulation 3.5min/cm, and the first heating zone temperature is 1180 DEG C, first heating zone insulation 3.5min/cm, second heating zone temperature is 1250 DEG C, the second heating zone insulation 3min/cm, and soaking zone temperature is 1220 DEG C, soaking zone insulation 2.5min/cm, tapping temperature 1260 DEG C; After coming out of the stove, steel billet is through high pressure water (pressure >=21MPa) de-scaling, is rolled afterwards: start rolling temperature is 1050 ~ 1100 DEG C, and previous three passes adopts large pressure, and single pass draught is 8% ~ 20%, and the overall compression ratio of rolling is 3.6, finishing temperature 850 ~ 900 DEG C; After rolling completes, steel plate rolls off the production line when surface temperature 400 ~ 500 DEG C, the slow cooling of covering heap, slow cooling more than 48 hours, and the object that steel plate rolls rear slow cooling fully reduces H content residual in steel plate, weakens the harm of H; Finally carry out normalizing and tempering thermal treatment successively to steel billet, steel are sent into the thick fire heating of continuous oven, holding temperature 920 DEG C, time inside furnace 2.5min/mm, use quenching press to quench after coming out of the stove, rapid water is chilled to less than 200 DEG C, water-cooled speed >=0.5 DEG C/s; After water-cooled, enter continuous oven and carry out temper, tempering Heating temperature is 750 DEG C, and tempering time inside furnace is 3.5min/mm, cools after coming out of the stove, and namely obtains steel plate finished product.
The present embodiment and embodiment 1, embodiment 2 check the state of sample blanks there are differences, and concrete difference is as follows:
In order to simulate stress-removal treating processes after Plate Welding, sample blanks from after steel plate is taken off first again in bogey according to 675 DEG C of insulations 8 hours, i.e. minimum Simulated post-weld heat treatment, and then carry out mechanical properties test.
Testing identity, the steel plate in the present embodiment has very high low-temperature impact work and numerical fluctuations is less, yield strength >=380MPa, tensile strength >=550MPa.Adopt normalizing (accelerating cooling)+tempering process, the whole plate mechanical property of steel plate is even, and concrete mechanical property is in table 1.
The mechanical property of the steel plate that each embodiment of table 1 is produced
In heavy thickness ductility steel plate mechanical property ,-18 DEG C of low-temperature impact toughness are the most implacable performance requriementss, and impact of collision relatively easily meets, but steel plate heart portion (i.e. 1/2 thickness of slab place) transverse impact performance is but difficult to reach.The transverse impact toughness of quenching+tempering state steel plate of the present invention is at more than 198J.As equipment container steel plate, usually require that plate property can not only meet the performance of quenching+tempering condition of delivery, also require that the performance of sample after maximum analog postwelding and minimum Simulated post-weld heat treatment also can reach the performance requriements of condition of delivery, and Simulated post-weld heat treatment can reduce low-temperature impact toughness to some extent.Steel plate of the present invention is at sample after maximum analog postwelding and minimum Simulated post-weld heat treatment, and low-temperature impact toughness mean value is still at more than 189J and do not occur large fluctuation.
The heavy thickness ductility steel plate that the present invention produces also has excellent Z-direction performance.This performance has also reacted its compactness except reacting the anti-lamellar tearing ability of steel plate.The Z-direction performance of the heavy thickness high tenacity tank plate that the present invention produces has exceeded the peak demand of conventional criteria to steel plate Z-direction performance 35%.Show that the heavy thickness high tenacity tank plate that in the present invention, continuously cast bloom is produced not only has high anti-lamellar tearing ability but also has high density, thus ensure that the rigors of steel plate to heart portion performance.
The present invention has the following advantages: 1.-18 DEG C, steel plate heart portion transverse impact performance is better; 2. maximum analog postwelding and minimum simulation postwelding excellent performance; 3. steel plate of the present invention uses converter+continuous casting process, and production cost comparatively electric furnace+die casting is low, is conducive to reducing device fabrication cost.
Claims (2)
1. a 140mm thickness ductility steel plate, it is characterized in that: the chemical composition of this steel plate is C:0.13 ~ 0.15% by mass percentage, Si:0.50 ~ 0.80%, Mn:0.40 ~ 0.65%, P :≤0.006%, S :≤0.001%, Ni :≤0.20%, Cr:1.30 ~ 1.50%, Mo:0.45 ~ 0.65%, Nb:0.005 ~ 0.020%, Sb :≤0.003%, Sn :≤0.010%, As :≤0.012%, H :≤0.0002%, O :≤0.0020%, N :≤0.0040%, Alt:0.020 ~ 0.050%, surplus is Fe and inevitable impurity element.
2. one kind manufactures the method for 140mm thickness ductility steel plate as claimed in claim 1, it is characterized in that: processing step is as follows: raw materials for metallurgy is successively through KR hot metal pretreatment, converter smelting: skim, tapping temperature 1610 ~ 1640 DEG C, converter tapping P≤0.005%, converter tapping temperature is 1610 ~ 1650 DEG C; LF refining: the white slag hold-time is not less than 25min, total refining time is not less than 45min, skims during molten steel S≤0.003%; RH vacuum deaeration refining: vacuum tightness≤66Pa, the vacuum hold-time is broken empty after more than 20min; Continuous casting, produces and meets the continuously cast bloom that chemical composition requires, thickness is 450mm or more, and to continuously cast bloom covering slow cooling more than 72 hours, slow cooling terminated rear to the cleaning of continuously cast bloom surface band temperature, and cleaning temperature remains on more than 100 DEG C; Reheat continuously cast bloom subsequently, adopt zone heating mode: heating rate is 10 ~ 11min/cm, preheating section temperature is 650 ~ 900 DEG C, preheating section insulation 3 ~ 3.5min/cm, and the first heating zone temperature is 1000 ~ 1200 DEG C, first heating zone insulation 3 ~ 3.5 min/cm, second heating zone temperature is 1200 ~ 1260 DEG C, the second heating zone insulation 2 ~ 3 min/cm, and soaking zone temperature is 1150 ~ 1270 DEG C, soaking zone insulation 2 ~ 3 min/cm, tapping temperature 1100 ~ 1260 DEG C; Be rolled steel billet after coming out of the stove: start rolling temperature is 1050 ~ 1100 DEG C, single pass draught is 8% ~ 20%, and the overall compression ratio of rolling is 3 ~ 5, finishing temperature 850 ~ 900 DEG C; After rolling completes, steel plate rolls off the production line when surface temperature 400 ~ 500 DEG C, the slow cooling of covering heap, slow cooling more than 48 hours; Finally carry out normalizing and tempering thermal treatment successively to steel billet, wherein, normalizing Heating temperature is 920 ~ 950 DEG C, and normalizing soaking time is 1.8 ~ 3min/mm, is quickly cooled to less than 200 DEG C after coming out of the stove with water, water-cooled speed >=0.5 DEG C/s; Tempering Heating temperature is 710 ~ 750 DEG C, and tempering insulation time is 3 ~ 4.5 min/mm, cools after coming out of the stove, and namely obtains steel plate finished product.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510403342.2A CN105018862B (en) | 2015-07-11 | 2015-07-11 | A kind of 140mm thickness ductility steel plate and its manufacture method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510403342.2A CN105018862B (en) | 2015-07-11 | 2015-07-11 | A kind of 140mm thickness ductility steel plate and its manufacture method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105018862A true CN105018862A (en) | 2015-11-04 |
| CN105018862B CN105018862B (en) | 2018-02-23 |
Family
ID=54409156
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510403342.2A Active CN105018862B (en) | 2015-07-11 | 2015-07-11 | A kind of 140mm thickness ductility steel plate and its manufacture method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105018862B (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107502705A (en) * | 2017-07-26 | 2017-12-22 | 舞阳钢铁有限责任公司 | A kind of production method for controlling ultra-thick plate performance difference in a thickness direction |
| WO2017219553A1 (en) * | 2016-06-23 | 2017-12-28 | 江阴兴澄特种钢铁有限公司 | 200 mm-thick pressure vessel steel plate resistant against hydrogen-induced cracking and manufacturing method thereof |
| CN109852890A (en) * | 2019-04-09 | 2019-06-07 | 鞍钢股份有限公司 | A method of improving oil transportation pipeline L450M steel plate low-temperature flexibility |
| CN110616372A (en) * | 2019-09-29 | 2019-12-27 | 舞阳钢铁有限责任公司 | Large-thickness 14Cr1MoR steel plate and production method thereof |
| CN111074162A (en) * | 2019-11-28 | 2020-04-28 | 舞阳钢铁有限责任公司 | Steel plate for boiler head and production method thereof |
| CN114411058A (en) * | 2022-01-06 | 2022-04-29 | 南京钢铁股份有限公司 | Heat-resistant steel plate for longitudinal submerged arc welded pipe and production method thereof |
| CN115572918A (en) * | 2022-10-19 | 2023-01-06 | 宝武杰富意特殊钢有限公司 | Method for manufacturing steel for rotating shaft |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06279919A (en) * | 1993-03-30 | 1994-10-04 | Sumitomo Metal Ind Ltd | Cr-mo steel plate for pressure vessel and its production |
| JP2001303173A (en) * | 2000-04-26 | 2001-10-31 | Mitsubishi Seiko Muroran Tokushuko Kk | Steel for carburizing and carbo-nitriding |
| CN102162065A (en) * | 2011-03-27 | 2011-08-24 | 莱芜钢铁集团有限公司 | 550Mpa yield-strength low-carbon bainitic steel for engineering machinery and preparation method thereof |
| CN102732810A (en) * | 2012-06-05 | 2012-10-17 | 舞阳钢铁有限责任公司 | Heavy-gauge hydrogen steel plate and its production method |
| CN103045966A (en) * | 2012-12-30 | 2013-04-17 | 南阳汉冶特钢有限公司 | High-quality and high-yield strength structural steel S620QL1 steel plate and production method thereof |
| CN104357755A (en) * | 2014-10-17 | 2015-02-18 | 江阴兴澄特种钢铁有限公司 | Large-thickness and high-strength steel plate applicable to low temperature and manufacturing method thereof |
-
2015
- 2015-07-11 CN CN201510403342.2A patent/CN105018862B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06279919A (en) * | 1993-03-30 | 1994-10-04 | Sumitomo Metal Ind Ltd | Cr-mo steel plate for pressure vessel and its production |
| JP2001303173A (en) * | 2000-04-26 | 2001-10-31 | Mitsubishi Seiko Muroran Tokushuko Kk | Steel for carburizing and carbo-nitriding |
| CN102162065A (en) * | 2011-03-27 | 2011-08-24 | 莱芜钢铁集团有限公司 | 550Mpa yield-strength low-carbon bainitic steel for engineering machinery and preparation method thereof |
| CN102732810A (en) * | 2012-06-05 | 2012-10-17 | 舞阳钢铁有限责任公司 | Heavy-gauge hydrogen steel plate and its production method |
| CN103045966A (en) * | 2012-12-30 | 2013-04-17 | 南阳汉冶特钢有限公司 | High-quality and high-yield strength structural steel S620QL1 steel plate and production method thereof |
| CN104357755A (en) * | 2014-10-17 | 2015-02-18 | 江阴兴澄特种钢铁有限公司 | Large-thickness and high-strength steel plate applicable to low temperature and manufacturing method thereof |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2017219553A1 (en) * | 2016-06-23 | 2017-12-28 | 江阴兴澄特种钢铁有限公司 | 200 mm-thick pressure vessel steel plate resistant against hydrogen-induced cracking and manufacturing method thereof |
| CN107502705A (en) * | 2017-07-26 | 2017-12-22 | 舞阳钢铁有限责任公司 | A kind of production method for controlling ultra-thick plate performance difference in a thickness direction |
| CN109852890A (en) * | 2019-04-09 | 2019-06-07 | 鞍钢股份有限公司 | A method of improving oil transportation pipeline L450M steel plate low-temperature flexibility |
| CN110616372A (en) * | 2019-09-29 | 2019-12-27 | 舞阳钢铁有限责任公司 | Large-thickness 14Cr1MoR steel plate and production method thereof |
| CN111074162A (en) * | 2019-11-28 | 2020-04-28 | 舞阳钢铁有限责任公司 | Steel plate for boiler head and production method thereof |
| CN114411058A (en) * | 2022-01-06 | 2022-04-29 | 南京钢铁股份有限公司 | Heat-resistant steel plate for longitudinal submerged arc welded pipe and production method thereof |
| CN114411058B (en) * | 2022-01-06 | 2022-11-18 | 南京钢铁股份有限公司 | Heat-resistant steel plate for longitudinal submerged arc welded pipe and production method thereof |
| CN115572918A (en) * | 2022-10-19 | 2023-01-06 | 宝武杰富意特殊钢有限公司 | Method for manufacturing steel for rotating shaft |
| CN115572918B (en) * | 2022-10-19 | 2024-01-26 | 宝武杰富意特殊钢有限公司 | Manufacturing method of steel for rotating shaft |
Also Published As
| Publication number | Publication date |
|---|---|
| CN105018862B (en) | 2018-02-23 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103725986B (en) | The special thick rack steel plate of the high tenacity F level used under low temperature and manufacture method thereof | |
| CN105018862B (en) | A kind of 140mm thickness ductility steel plate and its manufacture method | |
| CN105861941B (en) | A kind of hydrogen-contacting equipment ultra-thick steel plate and preparation method thereof | |
| CN103695803B (en) | The heavy thickness rack steel that low-carbon-equivalent low-temperature uses and manufacture method thereof | |
| CN104988435B (en) | Low-carbon high-tenacity super-thick steel plate and manufacturing method thereof | |
| CN104862616B (en) | A kind of big thickness high tenacity tank plate and manufacture method thereof | |
| US20160230247A1 (en) | Non quenched and tempered steel and manufacturing process thereof | |
| CN109112423B (en) | Super-thick alloy steel plate with excellent low-temperature toughness and preparation method thereof | |
| CN109652733B (en) | 690 MPa-grade super-thick steel plate and manufacturing method thereof | |
| CN105755375A (en) | Low-compression-ratio high-performance ultra-thick steel plate produced by continuous casting billet and manufacturing method of steel plate | |
| CN102676920B (en) | Large-thickness steel plate for low-temperature pressure container and production method thereof | |
| CN107794451B (en) | A kind of plastic die steel 718 and its production technology | |
| CN109023119A (en) | A kind of abrasion-resistant stee and its manufacturing method with excellent plasticity and toughness | |
| CN109207854B (en) | Super-wide-specification high-strength high-toughness steel for ocean engineering and manufacturing method thereof | |
| CN102400043A (en) | Large-thickness steel plate for oceaneering and production method thereof | |
| CN106834946B (en) | Big thickness protects Testing Tensile Strength at Elevated Temperature steel plate SA299GrB and preparation method thereof | |
| CN104962828A (en) | Large-thickness SA738GrA steel plate and production method thereof | |
| CN112226687B (en) | Rack steel plate with low rolling compression ratio and manufacturing method thereof | |
| CN115181911B (en) | Super-thick Q500qE bridge steel plate and production method thereof | |
| CN111270169A (en) | Ni-containing alloy steel plate with excellent low-temperature toughness and production method thereof | |
| CN113667881A (en) | Production method of high-performance wear-resistant steel plate NM500E | |
| CN115261746B (en) | Super-thick Q420qE bridge steel plate and production method thereof | |
| CN103602892B (en) | The production method of thick steel plates | |
| CN110565027A (en) | Steel plate with ultrahigh hardness and excellent low-temperature toughness and production method thereof | |
| CN102732802B (en) | Boiler-steam-drum-use steel with thickness no lower than 80mm, and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |