CN104726665B - Hot rolling technique of X80 pipeline steel coil plate - Google Patents
Hot rolling technique of X80 pipeline steel coil plate Download PDFInfo
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- CN104726665B CN104726665B CN201510157835.2A CN201510157835A CN104726665B CN 104726665 B CN104726665 B CN 104726665B CN 201510157835 A CN201510157835 A CN 201510157835A CN 104726665 B CN104726665 B CN 104726665B
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Abstract
The invention discloses a hot rolling technique of an X80 pipeline steel coil plate, which solves the problem of poor DWTT performance stability of the X80 pipeline steel coil plate with the thickness of at least 20mm produced in the prior art. The hot rolling technique comprises the steps of slab heating, rough rolling, finish rolling, post-rolling cooling and coiling. In the rough rolling, 5-8-pass rough rolling is performed, the rolling temperature of the next-to-last pass is lower than or equal to 980 DEG C, the rolling reduction of the next-to-last pass is greater than or equal to 20%, the rolling temperature of the last pass is lower than or equal to 950 DEG C, and the rolling reduction of the last pass is greater than or equal to 23%; in the finish rolling step, the finish rolling inlet temperature is lower than or equal to 920 DEG C, the finish rolling accumulative rolling reduction is greater than or equal to 62%, and the finish rolling finishing temperature is Ar3+0-30 DEG C (Ar3 is phase-change temperature); and in the post-rolling cooling step, ultra-fast cooling is performed in the ultra-fast cooling system, the ultra-fast cooling finishing temperature is 480-560 DEG C, the average cooling rate is greater than or equal to 40 DEG C/second, and the coiling temperature is 200-400 DEG C. The technique effectively enhances the DWTT fracture toughness on the premise of ensuring the strength of the steel coil.
Description
Technical field
The invention belongs to hot rolling technology field, more particularly to a kind of hot rolling technology of X80 pipe line steels roll bending.
Background technology
With oil, the development of gas industry, the demand of pipe line steel increasingly increases, and its mining area is typically remote
Area, bad environments, during long-distance transportation, geomorphological structure is complicated, and service condition goes from bad to worse.Meanwhile, in order to reduce pipeliner
The cost of journey, long distance line develop to high pressure, heavy caliber.Therefore current pipeline steel is just towards think gauge, Hi-grade steel, high tough
The direction of property is developed.
DWTT (drop weight tear test, DWTT) performance is the one of steel for gas delivering pipeline prescription
Individual important and indispensable index.This is due to the increase of thickness, CVN (the Charpy V-notched of Hi-grade steel pipe line steel
Impact test, v-notch impact test) dependency that extends with ductility crack of performance no longer substantially, and using complete thick
The DWTT performance evaluations mode of degree being capable of truer, more accurately reaction material fracture toughness.But DWTT performances are thick to coil of strip
Degree is very sensitive, and research shows, for X80 pipe line steels, when thickness is more than 15mm, low temperature DWTT performances become extremely unstable.
Especially for the production of hot continuous rolling coil of strip, its middle base limits generally only 58～60mm, Ovshinsky in the thickness of finish rolling entrance
Body becomes weakened configuration and is difficult to reach enough grain refining effects.
At present, the hot rolling technology for improving DWTT performances for pipe line steel is only capable of the roll bending for thickness less than 20mm and gives birth to
Produce, and prior art is used for when producing the X80 pipe line steel roll bendings of thickness >=20mm, still can there is DWTT stabilities poor
Problem.
The content of the invention
It is an object of the invention to provide a kind of hot rolling technology of X80 pipe line steels roll bending, in solving prior art, production is thick
DWTT stabilities poor problem during the X80 pipe line steel roll bendings of degree >=20mm.
The hot rolling technology of pipe line steel roll bending provided by the present invention, through heating of plate blank step, roughing step, finish rolling step
Suddenly, roller repairing step and step is batched, in the roughing step：5～8 passage roughing are carried out, wherein, passage second from the bottom
Rolling temperature≤980 DEG C, drafts >=20% of the passage second from the bottom, rolling temperature≤950 DEG C of extreme trace time, the end
Drafts >=23% of passage；In the finish rolling step：Entry temperature at finishing≤920 DEG C, finish rolling add up drafts >=62%, essence
It is Ar3+0～30 DEG C to roll finishing temperature, wherein, the Ar3 is phase transition temperature；In the roller repairing step：Through ultrafast cold
System carries out ultrafast cooling, wherein, ultrafast cold final cooling temperature is 480～560 DEG C, average cooling rate >=40 DEG C/s.
Preferably, it is described to batch in step：Coiling temperature is 200～400 DEG C.
Preferably, in the roughing step：Using two-stand mills, 5～8 passage roughing are carried out altogether.
Preferably, the thickness of the middle base for being formed after the roughing step is 58～60mm.
Technical scheme carries out Hot-roller from the details control of roughing step, finish rolling step and cooling step
The improvement of skill, is carried out with deformation so as to surround the refinement of austenite structure, while refining room temperature ferritic structure, is realized and is being protected
DWTT fracture toughnesses are effectively improved while card coil of strip intensity.Can be in thickness so as to pass through hot rolling technology provided by the present invention
Specification still can keep good DWTT performances in the case of improving, and then can produce using hot rolling technology provided by the present invention
Go out the hot-rolled steel coiled sheet of more think gauge.
Description of the drawings
The austenite structure of the X80 pipe line steel roll bendings that Fig. 1 is produced for the hot rolling technology in the embodiment of the present invention 2；
Fig. 2 is the austenite structure of the X80 pipe line steel roll bendings that existing hot rolling technology is produced.
Specific embodiment
A kind of hot rolling technology of X80 pipe line steels roll bending is embodiments provided, production is thick in solving prior art
DWTT stabilities poor problem during the X80 pipe line steel roll bendings of degree >=20mm, total thinking are as follows：
Technical scheme carries out Hot-roller from the details control of roughing step, finish rolling step and cooling step
The improvement of skill, is carried out with deformation so as to surround the refinement of austenite structure, while refining room temperature ferritic structure, is realized and is being protected
DWTT fracture toughnesses are effectively improved while card coil of strip intensity.Can be in thickness so as to pass through hot rolling technology provided by the present invention
Specification still can keep good DWTT performances in the case of improving, and then can produce using hot rolling technology provided by the present invention
Go out the hot-rolled sheet coil of more think gauge.
To make purpose, technical scheme and the advantage of the embodiment of the present invention clearer, below in conjunction with the embodiment of the present invention
In accompanying drawing, the technical scheme in the embodiment of the present invention is clearly and completely described, it is clear that described embodiment is
The a part of embodiment of the present invention, rather than the embodiment of whole.Based on the embodiment in the present invention, those of ordinary skill in the art
The every other embodiment obtained under the premise of creative work is not made, belongs to the scope of protection of the invention.
The hot rolling technology of pipe line steel roll bending provided by the present invention, comprises the steps：
A, heating of plate blank step：Austenite grain size is controlled in the case where the abundant solid solution of microalloy element is ensured, is had
In body implementation process, the design parameter of heating of plate blank step may be referred to prior art, succinct for description, not enter herein
Row is repeated.
B, roughing step：In order to complete the osmotic effect that austenite is sufficiently recrystallized and increases deformation, the present invention is implemented
Example carries out 5～8 passage roughing.Due to austenite roughing temperature it is relatively low, base is thick relatively thin when deformation osmotic effect more preferably, this
The technical scheme of inventive embodiments is to improve the deformation technique of last two passage.Specifically, the rolling of passage second from the bottom
Temperature≤980 DEG C, drafts >=20% of passage second from the bottom, rolling temperature≤950 DEG C of extreme trace time, the drafts of extreme trace time
>=23%.
C, finish rolling step：Entry temperature at finishing≤920 DEG C, finish rolling add up drafts >=62%, and finish rolling finishing temperature is Ar3
+ 0～30 DEG C, wherein, Ar3 is phase transition temperature.Preferably, the thickness of the middle base for being formed after roughing step is 58～60mm.It is logical
The flattening degree that the finish rolling step improves austenite is crossed, finish rolling compression ratio is increased as far as possible.
D, roller repairing step；Ultrafast cooling is carried out through ultrafast cooling system, wherein, ultrafast cold final cooling temperature be 480～
560 DEG C, average cooling rate >=40 DEG C/s.So as to compensate for ausforming and the deficiency of refinement in rolling, fully refine
Ferritic structure, and make full use of ultrafast cooling rate to refine the hard phase constitution such as tissue Zhong MA islands.
E, batch step：Coiling temperature is 200～400 DEG C.
Preferably, roughing step is carried out using two-stand mills in specific implementation process, carry out altogether 5～8 passages thick
Roll.
The hot rolling technology specific embodiment of the pipe line steel roll bending of X80 steel-grade is provided below, but is not used in and is limited this
Bright, those skilled in the art can be drawing other embodiment according to technical solution of the present invention.
Embodiment 1：
Steel 1：Carbon content is 0.055%, and content of niobium is 0.08%, and molybdenum content is 0.15%, and cupro-nickel content is respectively
0.12%, and also include other alloying elements.
Hot rolling technology comprises the steps：
A, heating of plate blank step：Austenite grain size is controlled in the case where the abundant solid solution of microalloy element is ensured：Will
Slab is heated in loading heating furnace, and soaking time is 50min, heating-up temperature to 1190 DEG C.
B, roughing technique：The slab heated through step A feeding two-stand mills are carried out into roughing, the road number of times of a roughing
For 3 passages, the road number of times of two roughing is 5 passages.Wherein, the drafts of the four-pass (i.e. R2-4) of two roughing is 21%, is become
Shape temperature is 970 DEG C；The drafts of roughing extreme trace time (R2-5) is 23%, and deformation temperature is 930 DEG C.
C, finish rolling step：Entry temperature at finishing is 920 DEG C, and the thickness for sending into the middle base of finish rolling entrance is 58mm, is added up
Drafts is 63%, 810 DEG C of finishing temperature, wherein, about 780 DEG C of phase transition temperature Ar3 temperature.
D, roller repairing step：Ultrafast cold final cooling temperature is 520 DEG C, average cooling rate >=40 DEG C/s.
E, batch step：Coiling temperature is 200～400 DEG C.
X80 pipe line steel roll bending of the product that the present embodiment 1 is produced for thickness 21.4, the 21.4X80 pipe line steel roll bendings
DWTT performances be shown in Table 1 in steel 1.
Embodiment 2：
Steel 2：Carbon content is 0.05%, and content of niobium is 0.075%, and molybdenum content is 0.15%, and cupro-nickel content is respectively
0.15%, and other alloying elements.
Hot rolling technology comprises the steps：
A, heating of plate blank step：Austenite grain size is controlled in the case where the abundant solid solution of microalloy element is ensured：Will
Slab is heated in loading heating furnace, and soaking time is 50min, heating-up temperature to 1195 DEG C.
B, roughing step：The slab heated through step A feeding two-stand mills are carried out into roughing, the road number of times of a roughing
For 3 passages, the road number of times of two roughing is 5 passages.Wherein, the drafts of the four-pass (i.e. R2-4) of two roughing is 22%, is rolled
Temperature processed is 970 DEG C；5th passage (i.e. R2-5, extreme trace time) of two roughing, drafts be 24%, rolling temperature is 930 DEG C.
C, finish rolling step：Entry temperature at finishing is 920 DEG C, and the workpiece thickness of finish rolling entrance is 58mm, and finish rolling is accumulative to press
Lower amount is 62%, and finishing temperature is 810 DEG C, wherein, about 780 DEG C of phase transition temperature Ar3.
D, roller repairing step, ultrafast cold final cooling temperature are 500 DEG C, average cooling rate >=40 DEG C/s.
E, batch step：Coiling temperature is 200～400 DEG C.
X80 pipe line steel roll bending of the product that the present embodiment 2 is produced for thickness 22mm, the 22mm X80 pipe line steel roll bendings
DWTT performances be shown in Table 1 in steel 2.
The DWTT performance comparisons of the product that table 1, the present invention are produced with existing process.
In table 1 DWTT result of the tests be tested using ZCJ-40000 type drop hammer testers obtained by.By above-mentioned examination
Hot rolling technology that result can be seen that in the present invention is tested compared with existing hot rolling technology, can effectively improve think gauge X80's
DWTT performances, especially still ensure that good even preferably DWTT performances in the case of specification raising.
Ovshinsky of the thickness that the hot rolling technology in embodiment 2 with reference to shown in Fig. 1 is produced for the pipe line steel roll bending of 22mm
Body is organized, and the austenite structure of the pipe line steel roll bending of 18.4mm that the existing hot rolling technology shown in Fig. 2 is produced, by Fig. 1
Can be seen that with the contrast of Fig. 2 and austenite flattening degree, specifically, 2 phase of embodiment can be refined using hot rolling technology of the present invention
Than existing hot rolling technology, Ovshinsky body thickness is refined to 5.2 μm or so by 6.9 μm, fundamentally improves DWTT performances.
Meanwhile, may certify that by test, in the hot rolling technology of the present invention, adopt ultrafast cold processing step, coil of strip surface,
Can control within 1 μm with the grain size difference of center portion at 1/4 so that grain structure microstructure homogenization effect in a thickness direction
Fruit is preferably.
It can be seen that, think gauge X80 pipe line steel roll bendings can be produced using the technical scheme in the present invention in actual applications
Practical process, effect is significant.
, but those skilled in the art once know basic creation although preferred embodiments of the present invention have been described
Property concept, then can make other change and modification to these embodiments.So, claims are intended to be construed to include excellent
Select embodiment and fall into the had altered of the scope of the invention and change.
Obviously, those skilled in the art can carry out the essence of various changes and modification without deviating from the present invention to the present invention
God and scope.So, if these modifications of the present invention and modification belong to the scope of the claims in the present invention and its equivalent technologies
Within, then the present invention is also intended to comprising these changes and modification.
Claims (1)
1. a kind of hot rolling technology of X80 pipe line steels roll bending, through heating of plate blank step, roughing step, finish rolling step, roller repairing
Step and batch step, it is characterised in that
In the roughing step：8 passage roughing are carried out, wherein, rolling temperature≤980 DEG C of passage second from the bottom, the inverse
Drafts >=20% of the second passage, rolling temperature≤950 DEG C of extreme trace time, drafts >=23% of the extreme trace time；
In the finish rolling step：Entry temperature at finishing≤920 DEG C, finish rolling add up drafts >=62%, and finish rolling finishing temperature is Ar3
+ 0～30 DEG C, wherein, the Ar3 is phase transition temperature；
In the roller repairing step：Ultrafast cooling is carried out through ultrafast cooling system, wherein, ultrafast cold final cooling temperature be 480～
560 DEG C, average cooling rate >=40 DEG C/s；
Wherein, for carbon content be 0.055%, content of niobium is 0.08%, and molybdenum content is 0.15%, and cupro-nickel content is respectively
0.12%, and the X80 pipe line steel roll bendings also including other alloying elements, in A, heating of plate blank step：Ensureing microalloy unit
Austenite grain size is controlled in the case of plain fully solid solution：Slab is loaded in heating furnace and is heated, soaking time is 50min,
Heating-up temperature to 1190 DEG C；In B, roughing technique：The slab heated through step A feeding two-stand mills are carried out into roughing, one
The road number of times of roughing is 3 passages, and the road number of times of two roughing is 5 passages；Wherein, the drafts of the four-pass of two roughing is
21%, deformation temperature is 970 DEG C；The drafts of roughing extreme trace time is 23%, and deformation temperature is 930 DEG C；In C, finish rolling step：Essence
Inlet temperature is rolled for 920 DEG C, the thickness for sending into the middle base of finish rolling entrance is 58mm, it is 63% to add up drafts, finishing temperature
810 DEG C, wherein, about 780 DEG C of phase transition temperature Ar3 temperature；D, roller repairing step：Ultrafast cold final cooling temperature is 520 DEG C, averagely
Rate of cooling >=40 DEG C/s；In E, batch step：Coiling temperature is 200～400 DEG C.
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| Application Number | Priority Date | Filing Date | Title |
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| CN201510157835.2A CN104726665B (en) | 2015-04-03 | 2015-04-03 | Hot rolling technique of X80 pipeline steel coil plate |
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| Application Number | Priority Date | Filing Date | Title |
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| CN201510157835.2A CN104726665B (en) | 2015-04-03 | 2015-04-03 | Hot rolling technique of X80 pipeline steel coil plate |
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| CN104726665A CN104726665A (en) | 2015-06-24 |
| CN104726665B true CN104726665B (en) | 2017-05-03 |
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| CN104998901A (en) * | 2015-08-10 | 2015-10-28 | 首钢总公司 | Hot rolling technology for pipeline rolled steel plate |
| CN106040749B (en) * | 2016-06-21 | 2018-06-22 | 首钢京唐钢铁联合有限责任公司 | A kind of roughing mill pace control method |
| CN108546885B (en) * | 2018-07-03 | 2019-09-20 | 鞍钢股份有限公司 | A kind of the L555M pipe line steel and its manufacturing method of excellent in low temperature toughness |
| CN111910126B (en) * | 2020-08-06 | 2022-02-01 | 东北大学 | Thick high-toughness X80 pipeline steel and production method thereof |
| CN114086073A (en) * | 2021-11-19 | 2022-02-25 | 安徽工业大学 | Production method of hot-rolled high-strength structural steel |
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| CN101545079B (en) * | 2009-05-15 | 2011-09-21 | 首钢总公司 | X80 hot rolled steel plate with good toughness, high strength and low tensile ratio and production method thereof |
| CN102172619A (en) * | 2010-12-31 | 2011-09-07 | 武汉钢铁(集团)公司 | Hot rolling process capable of improving high-grade thick pipeline steel fracture toughness |
| CN102277530B (en) * | 2011-08-15 | 2013-03-20 | 武汉钢铁(集团)公司 | Pipeline steel with thickness more than or equal to 25mm for deep sea and production method thereof |
| CN104141099B (en) * | 2014-08-12 | 2016-05-18 | 北京首钢股份有限公司 | A kind of manufacture method of super thick specification X70 hot-rolled sheet coil |
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Address after: 100041 Shijingshan Road, Beijing, No. 68, No. Patentee after: Shougang Group Co. Ltd. Address before: 100041 Shijingshan Road, Beijing, No. 68, No. Patentee before: Capital Iron & Steel General Company |