CN106563695B - A kind of production method of low yield strength ratio high-strength line-pipe steel - Google Patents

A kind of production method of low yield strength ratio high-strength line-pipe steel Download PDF

Info

Publication number
CN106563695B
CN106563695B CN201610975595.1A CN201610975595A CN106563695B CN 106563695 B CN106563695 B CN 106563695B CN 201610975595 A CN201610975595 A CN 201610975595A CN 106563695 B CN106563695 B CN 106563695B
Authority
CN
China
Prior art keywords
temperature
rolling
steel
austenite
cooling
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
CN201610975595.1A
Other languages
Chinese (zh)
Other versions
CN106563695A (en
Inventor
朱坦华
李玉谦
杜琦铭
刘红艳
梅东贵
姚宙
成慧梅
郝宾宾
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
HBIS Co Ltd Handan Branch
Original Assignee
HBIS Co Ltd Handan Branch
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by HBIS Co Ltd Handan Branch filed Critical HBIS Co Ltd Handan Branch
Priority to CN201610975595.1A priority Critical patent/CN106563695B/en
Publication of CN106563695A publication Critical patent/CN106563695A/en
Application granted granted Critical
Publication of CN106563695B publication Critical patent/CN106563695B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/222—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a rolling-drawing process; in a multi-pass mill
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/48—Tension control; Compression control
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • B21B37/76—Cooling control on the run-out table
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by hot-rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

A kind of production method of low yield strength ratio high-strength line-pipe steel of the present invention, including steel-making continuous casting, heating strand, strand controlled rolling, steel plate control cooling and the straight process of straightener sedan-chair, single pass reduction ratio is not less than 16% when austenite recrystallization area elongation rolling in rolling process, it accumulates effective reduction ratio and is not less than 70%, austenite Unhydrated cement single pass reduction ratio is not higher than 18%；It controls austenite Unhydrated cement start rolling temperature in cooling process and is less than 20 ~ 30 DEG C of Ar3 temperature, rolling temperature range is made to be located at " austenite+ferrite " coexistence region, begin to cool temperature and be less than Ar1 temperature, avoid generating larger transformation stress in cooling procedure.The pipeline steel product of present invention process production, not only there is higher intensity, there is good toughness and excellent yield tensile ratio range simultaneously, solve the contradiction between steel industry pipe line steel series of products " high intensity " and " low yield strength ratio " performance, reach domestic type of industry best level.

Description

A kind of production method of low yield strength ratio high-strength line-pipe steel
Technical field
The present invention relates to a kind of production methods of low yield strength ratio high-strength line-pipe steel, belong to metal rolled technical field.
Background technology
Raw material of the pipe line steel as transfer oil and natural gas line, safety is most important, and yield tensile ratio is characterization material The deformability being broken to the end from starting plastic deformation, so yield tensile ratio is mechanical performance index important in pipe line steel.It bends By force than smaller, the deformability of material is bigger, and strength margin is bigger；Yield tensile ratio is bigger, and the plastic range after material yield is smaller, More easy to produce rupture failure.It is born before internal pressure is deformed into rupture in steel pipe, circumferential deformation is there are a limiting value, and the value is with steel The yield tensile ratio of pipe increases and reduces.So for the security consideration to pipeline, the general requirement of yield tensile ratio of pipe line steel cannot be more than A certain particular value.Currently, requirement of each pipeline specifications to this index both at home and abroad is not quite similar, general X65 ranks are claimed below Requirement of the pipeline of 0.85, X70 or higher level to yield tensile ratio, which cannot be more than, can be loosened to 0.90 or even 0.93.
For pipeline steel product, with the increase of intensity rank, the increase of yield strength Rt0.5 is much larger than tensile strength Rm Increase, directly result in the super upper limit of high intensity levels pipeline steel product yield tensile ratio.For pipe line steel production field, long-standing problem is wide The problem of big steel enterprise the contradiction between " high intensity " and " low yield strength ratio " performance；It is exceeded then tight that yield tensile ratio occurs in pipe line steel Prohibit and use, causes greatly to perplex to tubulation producer and vast iron and steel enterprise.
Invention content
Technical problem to be solved by the invention is to provide a kind of production methods of low yield strength ratio high-strength line-pipe steel, pass through Controlled rolling and cooling technique change the percentage composition of tiny acicular ferrite+bainite two-phase in pipe line steel, steel plate are made to have Good toughness is had both while high intensity, achievees the purpose that finally to control pipe line steel yield tensile ratio.
Used technical solution is the present invention to solve above-mentioned technical problem：
A kind of production method of low yield strength ratio high-strength line-pipe steel, including the control of steel smelting-continuous casting, heating strand, strand are rolled System, steel plate control is cooling and the straight process of straightener sedan-chair, improvements are：
In the controlled rolling process, the first rolling process austenite recrystallization area uses big reduction system, single when elongation rolls Percentage pass reduction is not less than 16%, accumulates effective reduction ratio and is not less than 70%, the second rolling process austenite Unhydrated cement single pass pressure Lower rate is not higher than 18%；
In the control cooling process, the second rolling process austenite Unhydrated cement start rolling temperature is less than Ar3 temperature 20 ~ 30 DEG C, so that rolling temperature range is located at " austenite+ferrite " coexistence region, operation of rolling steel plate no longer recrystallizes；Start cold But temperature is less than Ar1 temperature, avoids generating larger transformation stress in cooling procedure.
A kind of production method of above-mentioned low yield strength ratio high-strength line-pipe steel, the first rolling process is difficult to understand in the controlled rolling process The big reduction system that family name's body recrystallization zone uses for：Strand broadening rolling after, elongation rolling when the first percentage pass reduction not Less than 16%, each percentage pass reduction is stepped up to 20 ~ 25% later, is accumulated effective reduction ratio and is not less than 70%；Second rolling process Last percentage pass reduction of austenite Unhydrated cement is not higher than 12%；
In the control cooling process, the start rolling temperature of the second rolling process austenite Unhydrated cement is 780 ~ 810 DEG C, is started Cooling temperature is 670 ~ 690 DEG C；It controls chill formula and uses DQ+ACC two-stage coolings, it is fast that DQ controls the cold section of cooling rate with 20 ~ 30 DEG C/s Speed obtains the bainite of corresponding proportion by bainite transformation temperature area；ACC is controlled the cold section of cooling rate with 10 ~ 20 DEG C/s and is cooled to 150 ~ 220 DEG C of final cooling temperature reduces ACC and controls cold section of steel plate thermal stress while avoiding generating martensitic structure, obtains good Strip shape quality.
A kind of production method of above-mentioned low yield strength ratio high-strength line-pipe steel, the formulation foundation of the controlled rolling process For：It uses the research of 3500 hot modeling test machines of Gleeble to obtain the level pipeline pipeline steel hyperthermia stress-strain curve first, determines Deformation temperature is at 950 ~ 1050 DEG C, and rate of deformation is in 5 ~ 10s-1, the critical compresibility that dynamic recrystallization occurs is 16 ~ 20%, thus Formulate the soft reduction process in austenite recrystallization area and Unhydrated cement；
In the control cooling process, the level pipeline pipeline steel Ovshinsky is obtained using 3500 thermal modeling tests of Gleeble first Body continuous cooling transformation (CCT) curve obtains Ar3 temperature and Ar1 temperature and sets start rolling temperature and begin to cool temperature accordingly.
A kind of production method of above-mentioned low yield strength ratio high-strength line-pipe steel, the first rolling process austenite recrystallization area Effective reduction ratio refers to the reduction ratio of percentage pass reduction >=16%, ensures that austenite can recrystallize.
A kind of production method of above-mentioned low yield strength ratio high-strength line-pipe steel, strand ingredient in the steel smelting-continuous casting process Weight percentage ranges are：C：0.03 ~ 0.07%, Si：≤ 0.10%, Mn：1.50 ~ 1.70%, P：≤ 0.025%, S：≤ 0.015%, Als：0.015 ~ 0.045%, Nb：0.055 ~ 0.070%, Ti：0.010 ~ 0.030%, Cr：0.20~0.30%；Pcm：0.12 ~ 0.18%；The rolling process is rolled using double rolling processes, first, by heating strand to 1100 ~ 1150 DEG C, keeps the temperature 320 ~ 360min； De-scaling high pressure water is fully open, and de-scaling water pressure is 20 ~ 30Mpa, thoroughly removes surface stove life oxide skin；Then first is carried out to roll Journey austenite recrystallization area rolls, and start rolling temperature is 1020~1080 DEG C, the first percentage pass reduction >=16%, later each passage pressure Lower rate is stepped up to 20 ~ 25%, accumulates effective reduction ratio >=70%, the second rolling process austenite Unhydrated cement start rolling temperature temperature Ranging from 780 ~ 810 DEG C, single pass reduction ratio≤18%, last percentage pass reduction≤12%.It is 670 ~ 690 to open cold temperature range DEG C, DQ controls the cold section of cooling rate with 20 ~ 30 DEG C/s and is quickly cooled to 400 ~ 430 DEG C, and it is cold that ACC controls the cold section of cooling rate with 10 ~ 20 DEG C/s But 150 ~ 220 DEG C of final cooling temperature is arrived；1 ~ 4 passage is aligned subsequently into straightener, straightening temperature is 100 ~ 200 DEG C.
The present invention show that the level pipeline pipeline steel hyperthermia stress-strain is bent using the research of 3500 hot modeling test machines of Gleeble Line determines first rolling process austenite recrystallization area's deformation temperature at 950 ~ 1050 DEG C, and rate of deformation is in 5 ~ 10s-1, austenite occurs The critical compresibility of dynamic recrystallization is 16 ~ 20%, in order to make pipe line steel that dynamic recrystallization, the effective reduction ratio setting of passage occur It is >=16%, obtains original fine austenite crystal grain；Second rolling process austenite Unhydrated cement is in order to make pipe line steel not move State recrystallizes, and percentage pass reduction is set as≤18%, prevents steel plate deformed from dynamic recrystallization occurs, and retains in metal inside Distort energy, provides more ferrite nucleation points.
Second rolling process austenite Unhydrated cement start rolling temperature of the invention is 780 ~ 810 DEG C, and rolling temperature range is located at " difficult to understand Family name's body+ferrite " coexistence region, operation of rolling steel plate are not recrystallizing, and distortion energy is retained inside steel plate, and main purpose is to increase Add ferrite nucleation point, forms tiny acicular ferrite after a certain proportion of flattening during the rolling process, it is tiny to finally obtain Acicular ferrite and bainite duplex structure prepare.
The high tensile pipeline steel cut deal product produced using present invention process, heterogeneous microstructure are：30 ~ 45% needle-shaped iron + 0 ~ 5% islands MA of ferritic+40 ~ 65% bainite；485 ~ 635MPa of yield strength, 560 ~ 760MPa of tensile strength, elongation percentage（A50） >=24%, yield tensile ratio range is 0.78 ~ 0.83, -20 DEG C of sections of shear 100% of dropping hammer, -30 DEG C of impact shear areas 100%, steel plate Vickers hardness range in lateral cross section（200~240）HV10.
The positive effect of the present invention：
Present invention process production pipeline steel product, not only have higher intensity, while have good toughness and Excellent yield tensile ratio range solves the lance between steel industry pipe line steel series of products " high intensity " and " low yield strength ratio " performance Shield reaches domestic type of industry best level.In high tensile pipeline steel production technical field, played well for China's steel industry Take the lead and exemplary role, the successful experience for being worth reference is provided for whole nation same type production line, social benefit is huge.
Description of the drawings
Fig. 1 is that target steel grade strain rate of the embodiment of the present invention is 5s-1When, load-deformation curve under different rolling temperatures；
Fig. 2 is target steel grade austenite Continuous Cooling Transformation Curve of the embodiment of the present invention；
Fig. 3 is the microstructure at 1 pipe line steel 1/4 of the embodiment of the present invention；
Fig. 4 is the microstructure at 1 pipe line steel 1/2 of the embodiment of the present invention；
Fig. 5 is the microstructure at 2 pipe line steel 1/4 of the embodiment of the present invention；
Fig. 6 is the microstructure at 2 pipe line steel 1/2 of the embodiment of the present invention；
Fig. 7 is the microstructure at 3 pipe line steel 1/4 of the embodiment of the present invention；
Fig. 8 is the microstructure at 3 pipe line steel 1/2 of the embodiment of the present invention.
Specific implementation mode
The present invention provides a kind of production method of low yield strength ratio high-strength line-pipe steel, uses 3500 hot-dies of Gleeble first Quasi- testing machine goal in research pipe line steel hyperthermia stress-strain curve, obtains rate of deformation in 5 ~ 10s-1, deformation temperature 950 ~ 1050 DEG C, the critical compresibility that Austenite Dynamic Recrystallization occurs is 16 ~ 20%, in order to make pipe line steel that austenite dynamic occur again Crystallization, the first effective reduction ratio of rolling process austenite recrystallization area passage should be greater than being equal to 16%, be set as >=16%, obtain original Fine austenite crystal grain, the second rolling process austenite Unhydrated cement, in order to make pipe line steel that dynamic recrystallization, passage pressure not occur Rate answers≤18%；Secondly target pipeline steel austenite Continuous Cooling Transformation Curve is obtained using 3500 thermal modeling tests of Gleeble, Obtaining Ar3 and Ar1 temperature, the second rolling process austenite Unhydrated cement start rolling temperature ratio Ar3 temperature of setting is 20 ~ 30 DEG C low, i.e., and 780 ~ 810 DEG C, rolling temperature range is located at " austenite+ferrite " coexistence region, to finally obtain tiny acicular ferrite and bainite Duplex structure prepares；It opens cold temperature and is less than Ar1 temperature, be set as 670 ~ 690 DEG C, avoid generating larger phase transformation in cooling procedure Stress improves strip shape quality in cooling procedure；Controlling chill formula uses two-stage cooling, first segment DQ to control cold section with 20 ~ 30 DEG C/s Cooling rate quickly through bainite transformation temperature area, be cooled to 400 ~ 430 DEG C, obtain the bainite of corresponding proportion, second segment ACC It controls the cold section of cooling rate with 10 ~ 20 DEG C/s and is cooled to 150 ~ 220 DEG C of final cooling temperature, the second cooling section slow cooling can avoid generating geneva While body tissue, the second cooling section steel plate thermal stress is reduced, good strip shape quality is obtained.
The specific production technology of the present invention includes：Steel smelting-continuous casting process produces strand, heating strand process eliminates strand temperature Spend gradient, strand controlled rolling process, steel plate control cooling process and the straight process of straightener sedan-chair；Strand ingredient weight in continuous casting working procedure Measuring percentage range is：C：0.03 ~ 0.07%, Si：≤ 0.10%, Mn：1.50 ~ 1.70%, P：≤ 0.025%, S：≤ 0.015%, Als：0.015 ~ 0.045%, Nb：0.055 ~ 0.070%, Ti：0.010 ~ 0.030%, Cr：0.20~0.30%；Pcm：0.12~ 0.18%；In double rolling process rolling process, first, by heating strand to 1100 ~ 1150 DEG C, 320-360min is kept the temperature；De-scaling high pressure water Fully open, de-scaling water pressure is 20 ~ 30Mpa, thoroughly removes surface stove life oxide skin；Then the first rolling process austenite is carried out again Crystal region rolls, and start rolling temperature is 1020~1080 DEG C, the first percentage pass reduction >=16%, and each passage is stepped up later 20 ~ 25%, effective 780 ~ 810 DEG C of reduction ratio >=70%, the second rolling process austenite Unhydrated cement start rolling temperature temperature range is accumulated, Single pass reduction ratio≤18%, last percentage pass reduction≤12%；It is 670 ~ 690 DEG C to open cold temperature range, DQ control cold section with 20 ~ The cooling rate of 30 DEG C/s is quickly cooled to 400 ~ 430 DEG C, ACC control the cold section of cooling rate with 10 ~ 20 DEG C/s be cooled to final cooling temperature 150 ~ 220℃；1 ~ 4 passage is aligned subsequently into straightener, straightening temperature is 100 ~ 200 DEG C.
By the following examples, the invention will be further described, and it is that 485MPa ranks are high that following embodiment, which tests steel grade, Strong pipeline steel medium plate product；The level pipeline pipeline steel requirements of the national standard yield strength 485-635MPa, tensile strength 570- 760MPa, yield tensile ratio is not more than 0.93, due to the particularity of high-grade pipe line steel product use environment（It is required that low-temperature resistance, anti- The performances such as shake）, user generally requires yield tensile ratio 0.83-0.88, improves the safety of pipe line steel used.
3500 hot modeling test machine goal in research pipe line steel hyperthermia stress-strain curves of Gleeble are used first, obtain change Shape rate is in 5 ~ 10s-1, for deformation temperature at 950 ~ 1050 DEG C, the critical compresibility that Austenite Dynamic Recrystallization occurs is 15 ~ 20%； Secondly target pipeline steel austenite Continuous Cooling Transformation Curve is obtained using 3500 thermal modeling tests of Gleeble, according to above-mentioned knot Fruit carries out the formulation in austenite recrystallization area and austenite Unhydrated cement reduction system；Carry out austenite Unhydrated cement temperature The formulation of control system；Carry out the formulation that DQ+ACC opens cold temperature and final cooling temperature system and cooling rate；Below by way of three Embodiment is specifically addressed：
Embodiment 1：Obtain purer molten steel by smelting, after by conticaster be casting continuously to form strand, Ingredients Weight hundred Point ratio is：C：0.03%, Si：0.025%, Mn：1.50%, P：0.0018%, S：0.006%, Als：0.015%, Nb：0.055%, Ti： 0.030%, Cr：0.20%；Pcm：0.13%；By heating strand to 1100 DEG C, 320min is kept the temperature；De-scaling high pressure water is fully open, removes Squama water pressure is 22Mpa, thoroughly removes surface stove life oxide skin；Then the rolling of the first rolling process austenite recrystallization area is carried out, is opened It is 1020 DEG C to roll temperature, after strand broadening rolling, is rolled using four-pass when elongation rolls, percentage pass reduction is respectively 16%, 18%, 18%, 25%, effective reduction ratio 77% is accumulated, the second 780 DEG C of rolling process start rolling temperature temperature range is rolled using four-pass System, percentage pass reduction is respectively 13%, 15%, 17%, 10%；670 DEG C of cold temperature is opened, DQ controls the fast quickly cooling of the cold section of cooling rate with 20 DEG C/s But to 400 DEG C, ACC controls the cold section of cooling rate with 10 DEG C/s and is cooled to 150 DEG C of final cooling temperature；3 passages are aligned subsequently into straightener, Straightening temperature is 140 DEG C.
The pipe line steel heterogeneous microstructure of production is：+ 64% lath of 34% acicular ferrite and the islands granular bainite+2%MA； Yield strength 565MPa, tensile strength 681MPa, elongation percentage（A50）30%, yield tensile ratio range is 0.83, -20 DEG C of shear surfaces that drop hammer Product 100%, -30 DEG C of impact shear areas 100%, Vickers hardness 208HV10 in steel plate lateral cross section；Fully meet 485MPa ranks Pipe line steel " low yield strength ratio particular service requirement " requirement.
Embodiment 2：Obtain purer molten steel by smelting, after by conticaster be casting continuously to form strand, Ingredients Weight hundred Point ratio is：C：0.05%, Si：0.06%, Mn：1.61%, P：0.013%, S：0.005%, Als：0.025%, Nb：0.059, Ti： 0.020%, Cr：0.26%；Pcm：0.15%；By heating strand to 1130 DEG C, 340min is kept the temperature；De-scaling high pressure water is fully open, removes Squama water pressure is 26Mpa, thoroughly removes surface stove life oxide skin；Then the rolling of the first rolling process austenite recrystallization area is carried out, is opened It is 1050 DEG C to roll temperature, after strand broadening rolling, is rolled using four-pass when elongation rolls, percentage pass reduction is respectively 16%, 17%, 19%, 20%, effective reduction ratio 72% is accumulated, the second 795 DEG C of rolling process austenite Unhydrated cement start rolling temperature uses Four-pass rolls, and percentage pass reduction is respectively 12%, 14%, 16%, 10%.685 DEG C of cold temperature is opened, DQ controls cold section with 27.3 DEG C/s's Cooling rate is quickly cooled to 415 DEG C, and ACC controls the cold section of cooling rate with 15.5 DEG C/s and is cooled to 200 DEG C of final cooling temperature；Subsequently into aligning Machine aligns 1 passage, and straightening temperature is 160 DEG C；
The pipe line steel heterogeneous microstructure of production is：+ 57% islands bainite+3%MA of 40% acicular ferrite；Yield strength 540MPa, tensile strength 683MPa, elongation percentage（A50）34%, yield tensile ratio range is 0.79, -20 DEG C of sections of shear 100% of dropping hammer, - 30 DEG C of impact shear areas 100%, Vickers hardness range 213HV10 in steel plate lateral cross section；Fully meet 485MPa level pipeline pipelines Steel " low yield strength ratio particular service requirement " requirement.
Embodiment 3：Obtain purer molten steel by smelting, after by conticaster be casting continuously to form strand, Ingredients Weight hundred Point ratio is：C：0.07%, Si：0.08%, Mn：1.70%, P：0.025%, S：≤ 0.007%, Als：0.045%, Nb：0.070%, Ti： 0.010%, Cr：0.30%；Pcm：0.18%；By heating strand to 1150 DEG C, 360min is kept the temperature；De-scaling high pressure water is fully open, removes Squama water pressure is 30Mpa, thoroughly removes surface stove life oxide skin；Then the rolling of the first rolling process austenite recrystallization area is carried out, is opened It is 1080 DEG C to roll temperature, after strand broadening rolling, is rolled using four-pass when elongation rolls, percentage pass reduction is respectively 17%, 18%, 19%, 22%, accumulate effective reduction ratio 76%, the second rolling process austenite Unhydrated cement start rolling temperature temperature range 810 DEG C, it is rolled using four-pass, percentage pass reduction is respectively 12%, 15%, 15%, 10%, opens 690 DEG C of cold temperature, and DQ controls cold section with 30 DEG C/cooling rate of s is quickly cooled to 430 DEG C, ACC controls the cold section of cooling rate with 20 DEG C/s and is cooled to 220 DEG C of final cooling temperature；Subsequently into Straightener aligns 4 passages, and straightening temperature is 200 DEG C.
The pipe line steel heterogeneous microstructure of production is：+ 55% islands bainite+0%MA of 45% acicular ferrite；Yield strength 515MPa, tensile strength 636MPa, elongation percentage（A50）33%, yield tensile ratio range is 0.81, -20 DEG C of sections of shear 100% of dropping hammer, - 30 DEG C of impact shear areas 100%, Vickers hardness 220HV10 in steel plate lateral cross section, fully meet 485MPa level pipeline pipeline steels " low yield strength ratio particular service requirement " requirement.

Claims (3)

1. a kind of production method of low yield strength ratio high-strength line-pipe steel, including steel smelting-continuous casting, heating strand, strand controlled rolling, Steel plate control cooling and the straight process of straightener sedan-chair, it is characterised in that：
In the controlled rolling process, the first rolling process austenite recrystallization area uses big reduction system, strand broadening rolling to terminate Afterwards, the first percentage pass reduction is not less than 16% when elongation rolling, and each percentage pass reduction is stepped up 20-25% later, and accumulation has It imitates reduction ratio and is not less than 70%；Second rolling process austenite Unhydrated cement single pass reduction ratio is not higher than 18%, last a time pressure Lower rate is not higher than 12%；
In the control cooling process, the second rolling process austenite Unhydrated cement start rolling temperature is less than 20-30 DEG C of Ar3 temperature, makes Rolling temperature range is located at " austenite+ferrite " coexistence region, and operation of rolling steel plate no longer recrystallizes；Begin to cool temperature Less than Ar1 temperature, avoid generating larger transformation stress in cooling procedure；Specifically, the second rolling process austenite Unhydrated cement Start rolling temperature be 780-810 DEG C, begin to cool temperature be 670-690 DEG C；It controls chill formula and uses DQ+ACC two-stage coolings, DQ The cold section of cooling rate with 20-30 DEG C/s is controlled quickly through bainite transformation temperature area, obtains the bainite of corresponding proportion；ACC controls are cold Section is cooled to 150-220 DEG C of final cooling temperature with the cooling rate of 10-20 DEG C/s, while avoiding generating martensitic structure, reduces ACC Control cold section of steel plate thermal stress.
2. a kind of production method of low yield strength ratio high-strength line-pipe steel as described in claim 1, it is characterised in that：The control The formulation of rolling process is according to being：The research of 3500 hot modeling test machines of Gleeble is used to obtain 485MPa level pipeline pipeline steels first Hyperthermia stress-strain curve determines deformation temperature at 950-1050 DEG C, and rate of deformation is in 5-10s-1, facing for dynamic recrystallization occurs Boundary's reduction ratio is 16-20%, thus formulates the soft reduction process in austenite recrystallization area and Unhydrated cement；
In the control cooling process, show that the level pipeline pipeline steel austenite connects using 3500 thermal modeling tests of Gleeble first Continuous cooling transformation curve obtains Ar3 temperature and Ar1 temperature and sets start rolling temperature and begin to cool temperature accordingly.
3. a kind of production method of low yield strength ratio high-strength line-pipe steel as claimed in claim 1 or 2, it is characterised in that：It is described Strand composition by weight percent is ranging from steel smelting-continuous casting process：C：0.03-0.07%, Si：≤ 0.10%, Mn：1.50- 1.70%, P：≤ 0.025%, S：≤ 0.015%, Als：0.015%-0.045%, Nb：0.055-0.070%, Ti：0.010- 0.030%, Cr：0.20-0.30%；Pcm：0.12 -0.18%；The rolling process is rolled using double rolling processes, first, by strand plus Heat arrives 1100-1150 DEG C, keeps the temperature 320-360min；De-scaling high pressure water is fully open, and de-scaling water pressure is 20-30Mpa, thoroughly clear Except surface stove gives birth to oxide skin；Then the rolling of the first rolling process austenite recrystallization area is carried out, start rolling temperature is 1020~1080 DEG C, the A time reduction ratio >=16%, later each percentage pass reduction be stepped up 20-25%, accumulate effective reduction ratio >=70%, the second and roll Ranging from 780-810 DEG C of journey austenite Unhydrated cement start rolling temperature, single pass reduction ratio≤18%, last percentage pass reduction ≤ 12%, it is 670-690 DEG C to open cold temperature range, and DQ controls the cold section of cooling rate with 20-30 DEG C/s and is quickly cooled to 400-430 DEG C, ACC controls the cold section of cooling rate with 10-20 DEG C/s and is cooled to 150-220 DEG C of final cooling temperature；1-4 passages are aligned subsequently into straightener, Straightening temperature is 100-200 DEG C.
CN201610975595.1A 2016-11-07 2016-11-07 A kind of production method of low yield strength ratio high-strength line-pipe steel Active CN106563695B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201610975595.1A CN106563695B (en) 2016-11-07 2016-11-07 A kind of production method of low yield strength ratio high-strength line-pipe steel

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201610975595.1A CN106563695B (en) 2016-11-07 2016-11-07 A kind of production method of low yield strength ratio high-strength line-pipe steel

Publications (2)

Publication Number Publication Date
CN106563695A CN106563695A (en) 2017-04-19
CN106563695B true CN106563695B (en) 2018-10-16

Family

ID=58540158

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201610975595.1A Active CN106563695B (en) 2016-11-07 2016-11-07 A kind of production method of low yield strength ratio high-strength line-pipe steel

Country Status (1)

Country Link
CN (1) CN106563695B (en)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107475634A (en) * 2017-06-29 2017-12-15 河钢股份有限公司邯郸分公司 Inexpensive FH460 levels ship and offshore engineering structure steel and its production method
CN107604259A (en) * 2017-08-31 2018-01-19 包头钢铁（集团）有限责任公司 A kind of X70 line steel hot rollings coiled sheet and its production method
CN107587072A (en) * 2017-09-01 2018-01-16 包头钢铁（集团）有限责任公司 A kind of X60 pipe line steels and preparation method thereof
CN107641768B (en) * 2017-09-08 2019-03-22 河钢股份有限公司邯郸分公司 The production method of big wall thickness straight-line joint submerged arc welding tube line steel plate
CN109735698B (en) * 2019-01-31 2019-11-19 东北大学 Manganese TRIP steel and its method of low temperature process forming in a kind of high-performance
CN113637922A (en) * 2020-04-27 2021-11-12 宝山钢铁股份有限公司 Economical low-yield-ratio high-strength steel and manufacturing method thereof
CN111842546A (en) * 2020-07-10 2020-10-30 首钢集团有限公司 Equipment and method for improving TMCP wide and thick plate secondary plate shape

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3399983B2 (en) * 1992-08-25 2003-04-28 株式会社神戸製鋼所 Method for producing high-strength steel sheet with excellent weldability and low yield ratio of 570 N / mm2 or more
CN100398684C (en) * 2005-12-22 2008-07-02 宝山钢铁股份有限公司 Superhigh strength X100 pipeline steel and its hot rolled plate making process
CN101962733A (en) * 2010-10-29 2011-02-02 北京科技大学 Low-cost and high-toughness X80 pipe steel with high deformation resistance and manufacture method thereof
CN102304667B (en) * 2011-09-22 2013-01-09 首钢总公司 X100 pipeline steel plate with good low temperature toughness and preparation method thereof
CN105624383B (en) * 2016-01-04 2017-09-15 河北钢铁股份有限公司邯郸分公司 A kind of production method for improving high-strength cut deal product surface quality

Also Published As

Publication number Publication date
CN106563695A (en) 2017-04-19

Similar Documents

Publication Publication Date Title
CN106563695B (en) A kind of production method of low yield strength ratio high-strength line-pipe steel
CN107475620B (en) Low-temperature pressure container quenching and tempering type A537Cl2 steel plate and its production method
CN104532126B (en) A kind of super high strength hot rolled Q＆P steel of low yield strength ratio and its manufacture method
CN103014554B (en) Low-yield-ratio high-tenacity steel plate and manufacture method thereof
CN105506494B (en) A kind of yield strength 800MPa grade high ductilities hot-rolling high-strength steel and its manufacture method
CN104789863B (en) X80 pipeline steel with good anti-strain aging property, pipeline pipe and manufacturing method of pipeline pipe
CN100395368C (en) Niobium titanium -combined microalloying steel for cooling-control reinforced bar and method for producing same
CN105803327B (en) The X90 Pipeline Steel Plates and its manufacture method of a kind of economical hic resistance
CN102605242B (en) Steel capable of resisting hydrogen-induced cracking for pressure containers and manufacturing method for steel
CN106319390B (en) A kind of X70 large-deformation-resistance pipeline steels and manufacture method
CN104561818A (en) Super-thick steel plate with thickness of more than 150 mm for boiler drum and production method for super-thick steel plate
CN102560284B (en) High-strength high-toughness X100 pipeline steel hot-rolled steel strip and manufacturing method thereof
CN110468350A (en) A kind of high-strength high durable Q420GJNHEZ35 steel plate for building and its production method
CN104250713B (en) X80-grade large-deformation-resistant pipeline steel plate and manufacturing method thereof
JP2018532883A (en) High toughness seamless steel pipe and manufacturing method thereof
CN101965414A (en) High-strength steel plate excellent in low-temperature toughness, steel pipe, and processes for production of both
CN102011047A (en) Production method of steel plate for pressure vessel with low cost and high performance
CN103469098B (en) A kind of X80 pipe line steel and production method thereof with good Properties of HIC resistance
CN108342655A (en) A kind of quenching and tempering type acid-resistant pipeline steel and its manufacturing method
CN107988547A (en) A kind of effective X52MS hot-rolled coils of high-frequency resistance welding (HFRW) and its manufacture method
CN107109590A (en) The high strength steel and its manufacture method for the resistant expansibility excellent of resistance to brittle crack
CN102912250A (en) Economical low-yield-ratio steel for pipe fittings for oil and gas transmission and method for producing economical low-yield-ratio steel
CN110408862A (en) Seamless steel pipe, manufacturing method and its application
CN103993243B (en) A kind of ultra-high strength bainite plate and preparation method thereof
CN104480384A (en) Steel plate for 510MPa-grade hydrogen induced cracking resistant pressure vessel and production method of steel plate

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant