CN1927486A - Manufacturing technique of low compression ratio high grade pipe line steel - Google Patents
Manufacturing technique of low compression ratio high grade pipe line steel Download PDFInfo
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Abstract
The invention relates to a method for producing high-strength low-alloy steel. Wherein, it comprises smelting, refining, casting sheet blank, heating blank, removing phosphor, cooling and flattening; the smelting step uses pure steel, low phosphor, and low sulfur; in the casting step, the loose of blank and the aliquation are lower than B0.5level; in the heating step, vanadium+niobium+ titanium0.15%, nickel+chromium+copper<=0.50%, and the heating temperature is 1180-1220Deg. C; in the thermal rolling step, in the crystallize process, the deformation temperature is 1070-1000Deg. C, the deformation amount is 40-60%, and the rolling speed is 1.5-2.5m/s, and in the second step that rolling the non-crystallized area, the pressure is 200-400MPa, the rolling speed is 5-1.5m/s, and the deformation amount is 60-75%; and the interlayer cooling speed in the cooling step is 15Deg. C/s-25Deg. C/s.
Description
Technical field
The present invention relates to the production technology of Aldecor, a kind of specifically manufacturing technique of low compression ratio high grade pipe line steel.
Background technology
Natural gas resource focuses mostly on Yu Haiyang, massif, desert, plateau down to severe cold areas, away from the consumption market.For reducing the fortune cost, to enhance one's market competitiveness, pipe design, the inevitable direction to heavy caliber, high grade of steel, thick tube wall, high discharge pressure of construction develop.Along with the construction of long Distance Gas Transmission Pipeline, more and more deep to the understanding of pipeline safety, timber height quality requirement.In general, long Distance Gas Transmission Pipeline often is accompanied by the characteristic of heavy caliber, high-pressure delivery, heavy wall, tackles coiled sheet mutually and proposes such as high tenacity, high strength requirement, and is especially more and more higher to the requirement of the obdurability of steel plate or coil of strip.
For achieving the above object, guarantee that cumulative deformation, zerolling and the control cooling technology etc. in non-recrystallization district are absolutely necessary.From traditional concept, the production of pipe line steel must guarantee the compression ratio greater than 10, in this case, the ability that the production line that continuous casting billet is thin is not just produced thick specification pipe line steel, for example wanting to obtain qualified thickness is the above production board of 20mm, will possess the above continuous casting line of thickness of strand 200mm, this all is a very big difficult problem for some production lines that do not satisfy the requirements.
Summary of the invention
The objective of the invention is to propose a kind of manufacturing technique of low compression ratio high grade pipe line steel that makes the less production line of script slab thickness can produce the pipe line steel of thicker specification.
Purpose of the present invention can be achieved through the following technical solutions:
Manufacturing technique of low compression ratio high grade pipe line steel mainly comprises operation: smelting, refining, sheet billet continuous casting, slab heating, dephosphorization, hot rolling, roll back cooling, smooth aligning, in the smelting procedure, adopt the metallurgical technology of clean steel, extremely low-phosphorous, utmost point low-sulfur; In the sheet billet continuous casting operation, the loose and segregation of continuous casting billet is less than 0.5 grade of B; In the slab heating process, the content of microalloy element is in the scope of vanadium+niobium+titanium≤0.15%, nickel+chromium+copper≤0.50% time, and heating-up temperature is between 1180～1220 ℃; In the hot-rolled process, in the phase I crystallization operation of rolling again, deformation temperature is 1070～1000 ℃, and deflection is 40～60%, and mill speed is 1.5～2.5m/s; In the second stage non-recrystallization district operation of rolling, pressure is 200～400MPa, and mill speed is 5～1.5m/s, and deflection is 60～75%; Roll in the refrigerating work procedure of back, adopt the laminar flow cooling, the cooling velocity of laminar flow cooling is 15 ℃/s～25 ℃/s.
Purpose of the present invention can also further realize by following technical measures:
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, in the metallurgical technology of wherein said clean steel, extremely low-phosphorous, utmost point low-sulfur, pure nitrogen in steel, hydrogen, oxygen, sulphur, phosphorus content summation are less than 100ppm, and the content of phosphorus is less than 70ppm, and the content of sulphur is less than 6ppm.
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, in the wherein said sheet billet continuous casting operation, continuous casting billet is taked the type of cooling of cooling in heap.
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, in the wherein said slab heating process, the content of niobium is 0.04～0.06% o'clock, the heating-up temperature scope is 1170～1220 ℃.
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, in the wherein said slab heating process, the soaking zone temperature is 1180～1200 ℃, and soaking time was greater than 30 minutes, and total heat time heating time was more than or equal to 150 minutes.
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, in the wherein said slab heating process, with the temperature deviation of piece slab smaller or equal to 10 ℃.
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, in the wherein said slab heating process, the slab tapping temperature is 1180～1200 ℃, temperature homogeneity is smaller or equal to 10 ℃.
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, in the wherein said hot-rolled process, phase I start rolling temperature: 1040～1070 ℃, finishing temperature: 990～1020 ℃, be total to rolling 4 passages, temperature control plate blank thickness: 56～76mm, total deformation: 50%～62%.
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, in the wherein said hot-rolled process, the second stage start rolling temperature: 840～940 ℃, finishing temperature: 790～820 ℃, rolling pass is 9 passages, and total deformation is 68%～72%.
Aforesaid manufacturing technique of low compression ratio high grade pipe line steel, when wherein said laminar flow cooled off, water yield size was 400～1000m
3/ h, the water ratio is 1: 2 up and down.
Advantage of the present invention is: the production flow line steel must guarantee that compression ratio is greater than 10 in the traditional concept, in this case, the ability that the production line that continuous casting billet is thin is not just produced thick specification pipe line steel, for example wanting to obtain qualified thickness is the above production board of 20mm, will possess the above continuous casting line of thickness of strand 200mm, this all is a very big difficult problem for some production lines that do not satisfy the requirements.Pass through the pipe line steel production technology of low compression ratio among the present invention, each link in the production process is carried out strict control, under the lower situation of compression ratio, obtain the production board of excellent combination property, make the thin production line of some continuous casting billets also have the ability of producing thick specification pipe line steel, have great important for the production of the thick specification pipe line steel of high grade of steel.
Description of drawings
Fig. 1 is a process chart of the present invention.
Fig. 2 is the figure of typical organization of embodiment one production board.
Fig. 3 is the figure of typical organization of embodiment two production boards.
The specific embodiment
The present invention is a kind of manufacturing technique of low compression ratio high grade pipe line steel, and particularly the pipe line steel production that the less production line of script slab thickness is carried out thick specification has important effect.Because compression ratio is lower, total deformation is less relatively, therefore must control each link in the production process by strictness and reach in the past crystal grain thinning under the aximal deformation value, the effect of enhanced tissue.From continuous casting, the process slab is the heating period again, carries out the controlled rolling of two stages, rolls the back and controls cooling with the mode of laminar flow cooling, finally obtains the production board of excellent combination property.
Flow chart of the present invention comprises operation as shown in Figure 1: smelting, refining, sheet billet continuous casting, slab heating, dephosphorization, hot rolling, roll back cooling, smooth aligning.
Smelting procedure adopts clean steel (refer generally to N, H, O, S, P content summation is lower than 100ppm or lower), and (S content is lower than 6～8ppm) metallurgical technology, guarantees the structural homogenity of continuous casting billet for low-phosphorous (P content is lower than 70ppm), utmost point low-sulfur.
In the sheet billet continuous casting operation, the defective of strict control strand, the loose and segregation of continuous casting billet is less than 0.5 grade of B; Continuous casting billet is taked the type of cooling of cooling in heap, reduces the content of hydrogen in the continuous casting billet, the internal stress of bringing when minimizing is cooled off by continuous casting billet as far as possible.
In the slab heating process, must guarantee the fully solid solution of carbonitride of microalloy element such as Nb, Ti etc. again in the heating process, and original austenite grains is not grown up.Therefore, the concrete scope of heating-up temperature should be determined that for example the temperature range that the X70 pipe line steel that contains Nb about 0.04～0.06% is heated usually is: 1180～1220 ℃ by the content of microalloy elements such as Nb, Ti in institute's production flow line steel.Simultaneously, even for guaranteeing later distortion, steel plate should guarantee with the temperature homogeneity of block plate better in heating process as far as possible, should be no more than 10 ℃ as the temperature deviation of piece slab.
In the hot-rolled process, carry out the controlled rolling of two stages: in the phase I crystallization operation of rolling again, control suitable deformation temperature, deflection and mill speed, guarantee fully carrying out of dynamic recrystallization, roll in the static recrystallization process in back crystal grain and can not grow up because of overstand; In the second stage non-recrystallization district operation of rolling, should guarantee that enough drafts make fully refinement of austenite crystal, for later phase transition process provides tiny austenite crystal and a large amount of Zona transformans promoting ferritic forming core, and at the suitable deflection of last several passages controls to guarantee good plate shape.Wherein the concrete parameter of rolling procedure need be determined according to factors such as concrete steel grade, mill load abilities jointly as parameters such as passage deformation temperature, mill speed, deflections.
Roll in the refrigerating work procedure of back, the cooling of employing laminar flow, because the cooling velocity that pipe line steel requires is more accurate, should control suitable cooling water temperature, the water yield in the laminar flow cooling procedure, guarantee suitable cooling velocity and return red temperature, finally obtain desirable microstructure and property, for example to the X70 pipe line steel of acicular ferrite structure, the cooling velocity that should guarantee laminar flow cooling is in 15 ℃/s～20 ℃/s scope; Be also noted that simultaneously the size of adjusting the water yield reaches the proportion relation of the water yield up and down, guarantee that as far as possible the water ratio reaches 1: 2 up and down, the unlatching of cooling water should guarantee the continuity of front and back, avoids steel plate wooden dipper song, guarantees good plate shape.Concrete parameter can be determined according to the appointed condition of the steel grade of being produced, laminar flow cooling etc. is common.
Embodiment one
Present embodiment is that compression ratio is the concrete production technology of 6.9 pipe line steel X70.Selected technology is applicable to steekle mill production X70 pipe line steel, and slab thickness is 150mm, and production board thickness is 21～21.5mm, and compression ratio range is 6.9～7.1, total deformation≤85%.
Smelt: adopt the metallurgical technology of clean steel, ultralow P, extremely low S, guarantee the structural homogenity of continuous casting billet, the main chemical composition scope of design of steel sees Table 1:
Table 1 X70 pipe line steel composition design (wt%)
| C | Si | Mn | P | S | Nb | Ti | Mo |
| 0.03~0.0 6 | 0.15-0.3 | 1.55~1.65 | ＜0.01 | ＜0.002 | 0.03~0.0 5 | 0.015~0.02 5 | 0.15-0.25 |
Carry out purified steel after the smelting.The defective of the strict control of sheet billet continuous casting strand should be controlled at B below 0.5 grade as loose and segregation.Continuous casting billet is taked the type of cooling of cooling in heap, reduces the content of hydrogen in the continuous casting billet, the internal stress of bringing when minimizing is cooled off by continuous casting billet as far as possible.
Slab heating: must guarantee the fully solid solution of carbonitride of microalloy element such as Nb, Ti etc. again in the heating process, and original austenite grains is not grown up.Therefore, the concrete scope of heating-up temperature should be determined by the content of microalloy elements such as Nb, Ti in institute's production flow line steel, the temperature range that the X70 pipe line steel that contains Nb about 0.04～0.06% in this example is heated usually is: 1180～1220 ℃, soaking zone temperature: 1180～1200 ℃, soaking time 〉=30 minute, total heat time heating time 〉=150 minute.Simultaneously, even for guaranteeing later distortion, steel plate should guarantee with the temperature homogeneity of block plate better in heating process as far as possible, should be no more than 8 ℃ with the temperature deviation of piece slab.Heating finishes again, and tapping temperature is 1180～1200 ℃, temperature homogeneity≤10 ℃.Dephosphorization is carried out to slab in slab heating back.
Hot rolling: carry out the controlled rolling of two stages: after steel billet was come out of the stove, through one dephosphorize by high pressure water, it was rolling to carry out the phase I.The phase I start rolling temperature: 1040～1070 ℃, finishing temperature: 990～1020 ℃, be total to rolling 4 passages, temperature control plate blank thickness: 68～76mm, total deformation: 50%～55%.In the phase I crystallization operation of rolling again, control suitable deformation temperature, deflection and mill speed, guarantee fully carrying out of dynamic recrystallization, roll in the static recrystallization process in back crystal grain and can not grow up because of overstand.
Through the cooling of certain hour, steel billet temperature carries out the rolling of second stage non-recrystallization district when reaching suitable second stage start rolling temperature.The second stage start rolling temperature: 840～860 ℃, finishing temperature: 790～810 ℃, rolling pass is 9 passages, and total deformation is 68%～72%.In the second stage non-recrystallization district operation of rolling, should guarantee that enough drafts make fully refinement of austenite crystal, for later phase transition process provides tiny austenite crystal and a large amount of Zona transformans promoting ferritic forming core, and at the suitable pass deformation of last several passages controls to guarantee good plate shape.
Roll the back cooling: the size of cooldown rate has conclusive effect to final tissue and performance.Because the cooling velocity that pipe line steel requires is more accurate, should control suitable cooling water temperature, the water yield in the laminar flow cooling procedure, guarantee suitable cooling velocity and return red temperature, finally obtain desirable microstructure and property.Be also noted that simultaneously the size of adjusting the water yield reaches the proportion relation of the water yield up and down, guarantee that as far as possible the water ratio reaches 1: 2 up and down, the unlatching of cooling water should guarantee the continuity of front and back, avoids the wooden dipper song, guarantees good plate shape.
X70 pipe line steel to acicular ferrite structure in this example, steel plate is gone into coolant-temperature gage: 790～800 ℃, the final red temperature of returning is: 520～550 ℃, the cooling velocity that has guaranteed the laminar flow cooling is in 15 ℃/s～20 ℃/s scope, and this also is the proper cooldown rate scope that obtains acicular ferrite structure.In the laminar flow cooling procedure, can adjust the water yield according to the situations such as actual temperature, cooling water temperature and environment temperature of steel plate, adjust the size of side-blown water simultaneously, guarantee that the cooling water on final steel plate surface when going out the laminar flow cooling can purge totally, avoid plate shape wooden dipper song.After rolling the back cooling, steel plate is carried out smooth aligning.
The typical organization of the final finished plate that is obtained by the design of above composition design and processes as shown in Figure 2.The typical final performance of X70 pipe line steel production board sees Table 2:
The typical final performance (embodiment 1) of table 2 X70 pipe line steel production board
| Instance number | Thickness | Compression ratio | R t0.5 | Rm | A％ | Rt0.5/Rm | Ag％ | Drop hammer/-15 ℃ | ||
| 1 | 21.5 | 6.98 | 523 | 617 | 42 | 0.85 | 10 | 90 | 98 | 94 |
| 2 | 21.5 | 6.98 | 524 | 639 | 40 | 0.82 | 9.4 | 98 | 95 | 97 |
| 3 | 21.5 | 6.98 | 531 | 666 | 33 | 0.80 | 8.7 | 90 | 90 | 90 |
| Thickness | Compression ratio | Ballistic work (20 ℃) | The section of shear | |||||||
| 1 | 21.5 | 6.98 | 438 | 414 | 423 | 425 | 100 | 100 | 100 | 100 |
| 2 | 21.5 | 6.98 | 447 | 426 | 393 | 422 | 100 | 100 | 100 | 100 |
| 3 | 21.5 | 6.98 | 441 | 390 | 396 | 409 | 100 | 100 | 100 | 100 |
Organized as can be seen by the scanning of typical pipe line steel X70, the feature of acicular ferrite is apparent in view, and it is indenting that the crystal boundary of ferrite crystal grain is, organize tiny, on the crystal boundary and the inner disperse of crystal grain distributing the MA island tiny.On final typical performance, though compression ratio very little (≤7), but final yield strength, tensile strength, yield tensile ratio, percentage elongation, Charpy-V impact power and DWTT are very good, this proves absolutely, even under the less situation of compression ratio, still can be by the strictness of each link in the production process being controlled the production board of final obtained performance excellence.
Embodiment two
Present embodiment is that compression ratio is the concrete production technology of about 8.5 pipe line steel X70.Selected technology is applicable to steekle mill production X70 pipe line steel, and slab thickness is about 150mm, and production board thickness is about 17～17.5mm, and compression ratio range is 8.2～8.6, total deformation≤89%.
Smelt: adopt the metallurgical technology of clean steel, ultralow P, extremely low S, guarantee the structural homogenity of continuous casting billet, main chemical composition scope of design sees Table 3:
Table 3 X70 pipe line steel composition design (wt%)
| C | Si | Mn | P | S | Nb | Ti | Mo |
| 0.03~0.0 6 | 0.15-0.3 | 1.55~1.6 5 | ＜0.01 | ＜0.002 | 0.03~0.05 | 0.015~0.02 5 | 0.15-0.2 5 |
Carry out purified steel after the smelting.The defective of the strict control strand of sheet billet continuous casting should be controlled at B below 0.5 grade as loose and segregation.Continuous casting billet is taked the type of cooling of cooling in heap, reduces the content of hydrogen in the continuous casting billet, the internal stress of bringing when minimizing is cooled off by continuous casting billet as far as possible.
Slab heating: must guarantee the fully solid solution of carbonitride of microalloy element such as Nb, Ti etc. again in the heating process, and original austenite grains is not grown up.Therefore, the concrete scope of heating-up temperature should be determined by the content of microalloy elements such as Nb, Ti in institute's production flow line steel, the temperature range that the X70 pipe line steel that contains Nb about 0.04～0.06% in this example is heated usually is: 1170～1220 ℃, soaking zone temperature: 1180～1200 ℃, soaking time 〉=30 minute, total heat time heating time 〉=150 minute.Simultaneously, even for guaranteeing later distortion, steel plate should guarantee with the temperature homogeneity of block plate better in heating process as far as possible, should be no more than 8 ℃ with the temperature deviation of piece slab.Heating finishes again, and tapping temperature is 1180～1200 ℃, temperature homogeneity≤10 ℃.Dephosphorization is carried out to slab in slab heating back.
Hot rolling: carry out the controlled rolling of two stages: after steel billet was come out of the stove, through one dephosphorize by high pressure water, it was rolling to carry out the phase I.The phase I start rolling temperature: 1040～1070 ℃, finishing temperature: 990～1020 ℃, be total to rolling 4 passages, temperature control plate blank thickness: 56～62mm, total deformation: 59%～62%.In the phase I crystallization operation of rolling again, control suitable deformation temperature, deflection and mill speed, guarantee fully carrying out of dynamic recrystallization, roll in the static recrystallization process in back crystal grain and can not grow up because of overstand.Through the cooling of certain hour, steel billet temperature carries out the rolling of second stage non-recrystallization district when reaching suitable second stage start rolling temperature.The second stage start rolling temperature: 920～940 ℃, finishing temperature: 800～820 ℃, rolling pass is 9 passages, and total deformation is 68%～72%.In the second stage non-recrystallization district operation of rolling, should guarantee that enough drafts make fully refinement of austenite crystal, for later phase transition process provides tiny austenite crystal and a large amount of Zona transformans promoting ferritic forming core, and at the suitable pass deformation of last several passages controls to guarantee good plate shape.
Roll the back cooling: the size of cooldown rate has conclusive effect to final tissue and performance.Because the cooling velocity that pipe line steel requires is more accurate, should control suitable cooling water temperature, the water yield in the laminar flow cooling procedure, guarantee suitable cooling velocity and return red temperature, finally obtain desirable microstructure and property.Be also noted that simultaneously the size of adjusting the water yield reaches the proportion relation of the water yield up and down, guarantee that as far as possible the water ratio reaches 1: 2 up and down, the unlatching of cooling water should guarantee the continuity of front and back, avoids the wooden dipper song, guarantees good plate shape.
X70 pipe line steel to acicular ferrite structure in this example, steel plate is gone into coolant-temperature gage: 790～800 ℃, the final red temperature of returning is: 520～550 ℃, the cooling velocity that has guaranteed the laminar flow cooling is in 15 ℃/s～20 ℃/s scope, and this also is the proper cooldown rate scope that obtains acicular ferrite structure.In the laminar flow cooling procedure, can adjust the water yield according to the situations such as actual temperature, cooling water temperature and environment temperature of steel plate, adjust the size of side-blown water simultaneously, guarantee that the cooling water on final steel plate surface when going out the laminar flow cooling can purge totally, avoid plate shape wooden dipper song.After rolling the back cooling, steel plate is carried out smooth aligning.
The typical organization of the final finished plate that is obtained by the design of above composition design and processes as shown in Figure 3.Scanning by the typical pipe line steel X70 of last figure is organized as can be seen, and the feature of acicular ferrite is apparent in view, and it is indenting that the crystal boundary of ferrite crystal grain is, organize tiny, on the crystal boundary and the inner disperse of crystal grain distributing the MA island tiny.On final typical performance, though compression ratio less (≤8.6), but final yield strength, tensile strength, yield tensile ratio, percentage elongation, Charpy-V impact power and DWTT are very good, this proves absolutely, even under the less situation of compression ratio, still can be by the strictness of each link in the production process being controlled the production board of final obtained performance excellence.The typical final performance of production board sees Table 4:
The typical final performance (embodiment 2) of table 4 X70 production board
| Instance number | Thickness | Compression ratio | R t0.5 | Rm | A％ | Rt0.5/Rm | Ag％ | Drop hammer-15 ℃ | ||
| 1 | 17.5 | 8.57 | 556 | 631 | 40 | 0.88 | 9.4 | 98 | 98 | 98 |
| 2 | 17.5 | 8.57 | 549 | 632 | 38 | 0.87 | 8.3 | 98 | 95 | 97 |
| 3 | 17.5 | 8.57 | 535 | 597 | 41 | 0.90 | 9.9 | 90 | 90 | 90 |
| Thickness | Compression ratio | Ballistic work (20 ℃) | The section of shear | |||||||
| 1 | 17.5 | 8.57 | 435 | 441 | 438 | 438 | 100 | 100 | 100 | 100 |
| 2 | 17.5 | 8.57 | 444 | 423 | 438 | 435 | 100 | 100 | 100 | 100 |
| 3 | 17.5 | 8.57 | 429 | 438 | 441 | 436 | 100 | 100 | 100 | 100 |
The present invention can also have other embodiment, and the technical scheme that equal replacement of all employings or equivalent transformation form all drops within the scope of protection of present invention.
Claims (10)
1. manufacturing technique of low compression ratio high grade pipe line steel, mainly comprise operation: smelting, refining, sheet billet continuous casting, slab heating, dephosphorization, hot rolling, roll back cooling, smooth aligning, it is characterized in that: in the described smelting procedure, adopt the metallurgical technology of clean steel, extremely low-phosphorous, utmost point low-sulfur; In the described sheet billet continuous casting operation, the loose and segregation of continuous casting billet is less than 0.5 grade of B; In the described slab heating process, the content of microalloy element is in the scope of vanadium+niobium+titanium≤0.15%, nickel+chromium+copper≤0.50% time, and heating-up temperature is between 1180～1220 ℃; In the described hot-rolled process, in the phase I crystallization operation of rolling again, deformation temperature is 1070～1000 ℃, and deflection is 40～60%, and mill speed is 1.5～2.5m/s; In the second stage non-recrystallization district operation of rolling, pressure is 200～400MPa, and mill speed is 5～1.5m/s, and deflection is 60～75%; Described rolling in the refrigerating work procedure of back adopted the laminar flow cooling, and the cooling velocity of described laminar flow cooling is 15 ℃/s～25 ℃/s.
2. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1, it is characterized in that: in the metallurgical technology of described clean steel, extremely low-phosphorous, utmost point low-sulfur, pure nitrogen in steel, hydrogen, oxygen, sulphur, phosphorus content summation are less than 100ppm, the content of phosphorus is less than 70ppm, and the content of sulphur is less than 6ppm.
3. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1 is characterized in that: in the described sheet billet continuous casting operation, continuous casting billet is taked the type of cooling of cooling in heap.
4. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1 is characterized in that: in the described slab heating process, the content of niobium is 0.04～0.06% o'clock, and the heating-up temperature scope is 1170～1220 ℃.
5. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1 is characterized in that: in the described slab heating process, the soaking zone temperature is 1180～1200 ℃, and soaking time was greater than 30 minutes, and total heat time heating time was more than or equal to 150 minutes.
6. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1 is characterized in that: in the described slab heating process, with the temperature deviation of piece slab smaller or equal to 10 ℃.
7. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1 is characterized in that: in the described slab heating process, the slab tapping temperature is 1180～1200 ℃, and temperature homogeneity is smaller or equal to 10 ℃.
8. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1, it is characterized in that: in the described hot-rolled process, phase I start rolling temperature: 1040～1070 ℃, finishing temperature: 990～1020 ℃, be total to rolling 4 passages, temperature control plate blank thickness: 56～76mm, total deformation: 50%～62%.
9. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1, it is characterized in that: in the described hot-rolled process, the second stage start rolling temperature: 840～940 ℃, finishing temperature: 790～820 ℃, rolling pass is 9 passages, and total deformation is 68%～72%.
10. manufacturing technique of low compression ratio high grade pipe line steel as claimed in claim 1 is characterized in that: when described laminar flow cooled off, water yield size was 400～1000m
3/ h, the water ratio is 1: 2 up and down.
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Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56108832A (en) * | 1980-01-31 | 1981-08-28 | Nippon Steel Corp | Manufacture of steel for line pipe excellent in resistant property of rupture propagation |
| JPH0681034A (en) * | 1992-08-31 | 1994-03-22 | Sumitomo Metal Ind Ltd | Production of hot rolled steel strip for steel pipe excellent in hic resistance |
| JP2002129288A (en) * | 2000-10-30 | 2002-05-09 | Nippon Steel Corp | High strength pipe bend and its manufacturing method |
| CN1142309C (en) * | 2000-11-01 | 2004-03-17 | 中国科学院金属研究所 | Ultravlow-carbon high-toughness steel resisting hydrogen sulfide for gas deliver pipeline |
| CN100359035C (en) * | 2005-01-26 | 2008-01-02 | 宝山钢铁股份有限公司 | X65 pipeline steel for use in acid condition and its making process |
| CN100404149C (en) * | 2005-05-20 | 2008-07-23 | 唐山钢铁股份有限公司 | Sheet slab C-Mn excellent high-strength sheet-band steel production process |
-
2006
- 2006-09-28 CN CNB2006100965132A patent/CN100408211C/en not_active Expired - Fee Related
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