CN1302128C - Process for making high-performance ultra-fine needle form ferrite type gas delivery pipe steel - Google Patents
Process for making high-performance ultra-fine needle form ferrite type gas delivery pipe steel Download PDFInfo
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- CN1302128C CN1302128C CNB2003101191008A CN200310119100A CN1302128C CN 1302128 C CN1302128 C CN 1302128C CN B2003101191008 A CNB2003101191008 A CN B2003101191008A CN 200310119100 A CN200310119100 A CN 200310119100A CN 1302128 C CN1302128 C CN 1302128C
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 39
- 239000010959 steel Substances 0.000 title claims abstract description 39
- 229910000859 α-Fe Inorganic materials 0.000 title abstract description 20
- 238000000034 method Methods 0.000 title description 8
- 230000008569 process Effects 0.000 title description 7
- 238000005096 rolling process Methods 0.000 claims abstract description 28
- 238000001816 cooling Methods 0.000 claims abstract description 10
- 238000002360 preparation method Methods 0.000 claims abstract description 5
- 238000009826 distribution Methods 0.000 claims abstract description 4
- 238000010438 heat treatment Methods 0.000 claims abstract description 4
- 230000000930 thermomechanical effect Effects 0.000 claims abstract 2
- 229910001566 austenite Inorganic materials 0.000 claims description 13
- 238000001953 recrystallisation Methods 0.000 claims description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims 2
- 229910052742 iron Inorganic materials 0.000 claims 1
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 239000011159 matrix material Substances 0.000 abstract description 4
- 230000005540 biological transmission Effects 0.000 abstract description 2
- 238000005516 engineering process Methods 0.000 description 19
- 239000007789 gas Substances 0.000 description 11
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 8
- 230000009467 reduction Effects 0.000 description 7
- 239000000126 substance Substances 0.000 description 5
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-UHFFFAOYSA-N 0.000 description 5
- 239000004615 ingredient Substances 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000003345 natural gas Substances 0.000 description 4
- 239000003921 oil Substances 0.000 description 4
- 239000000470 constituent Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 230000002929 anti-fatigue Effects 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 235000009508 confectionery Nutrition 0.000 description 2
- 230000033001 locomotion Effects 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 238000009412 basement excavation Methods 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000010779 crude oil Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 239000003209 petroleum derivative Substances 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
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Abstract
本发明公开一种高性能超细针状铁素体型输气管线钢制备工艺。它采用热机械控轧工艺制度(TMCP)：轧制道次分配为18～22%-18～22%-20～35%-20～32%-25～35%-30～35%-33～36%；加热温度1150℃，开轧温度为1100℃～1050℃，待温温度区间为1020℃-950℃，精轧开始温度890℃～920℃，终轧温度区间为804℃-750℃，终轧后控制冷却；显微组织为在充分细化的针状铁素体AF基体上弥散分布着M/A组元，由本发明得到的管线钢不但具有更高的强度和很高的低温冲击韧性，而且能具有更好的抗疲劳裂纹扩展的能力，用于制造高压、大管径石油天然气输送管线钢。The invention discloses a high-performance ultrafine acicular ferrite type gas transmission pipeline steel preparation process. It adopts the thermomechanical controlled rolling process system (TMCP): the rolling pass distribution is 18～22%-18～22%-20～35%-20～32%-25～35%-30～35%-33～ 36%; heating temperature is 1150°C, starting rolling temperature is 1100°C-1050°C, waiting temperature range is 1020°C-950°C, finish rolling start temperature is 890°C-920°C, finish rolling temperature range is 804°C-750°C, Cooling is controlled after final rolling; the microstructure is that M/A components are dispersed and distributed on the fully refined acicular ferrite AF matrix, and the pipeline steel obtained by the present invention not only has higher strength and high low temperature impact Toughness, and better resistance to fatigue crack growth, used to manufacture high-pressure, large-diameter oil and gas pipeline steel.
Description
Technical field
The invention belongs to the field of low-carbon (LC)/super low carbon microalloy rolling controlled and cooling controlled steel, be mainly used in the preparation technology who makes high pressure, big caliber petroleum gas delivering pipe line steel.
Background technology
Oil and gas is the important component part of national economy, be the basic substance of social development, and pipeline transportation is the mode of movement of a kind of economy, safety and continual large-scale oil, Sweet natural gas.Because the exploitation of offshore oil and gas field, polar region oil-gas field and corrosive environment oil-gas field not only require pipe line steel to have high intensity, and requirement should have good toughness, fatigue crack-resistant performance and corrosion resistance nature.By 2010, the crude oil in China breach reached 7,000 ten thousand tons every year, and the Sweet natural gas breach reaches the 40-50 billion cubic meter.At present, China implement " West-east Gas gas transmission line construction project has been finished most, also will set up thousands of kilometers Sino-Russian line of pipes simultaneously, introduces the external energy.Because the line of pipes major part all will be passed through ice box, the region complexity is carried cost in order to reduce oil gas on the way, adopt big caliber, the high pressure line of big throughput rate is carried, and this just requires the line of pipes steel satisfying under the condition of intensity, has splendid toughness.For avoiding or reducing the pipeline generation fatigue damage of moving under the earthquake load, also require pipe line steel to want the performance of good antifatigue crack propagation simultaneously.For carrying acid gas also to require it to have very high anti-H with pipe line steel
2The S corrosive nature.
For other pipe line steel of level below the X70, generally adopt the microstructure and property of TMCP technology need to obtain; For X80 and other pipe line steel of higher level, it has been generally acknowledged that under TMCP technology now, to be difficult for realizing, need to adopt the pipe line steel of tempered martensite, perhaps on the basis of TMCP technology, add technologies such as rolling the back tempering.And these methods all inevitably can increase the technology difficulty that pipe line steel is produced, and improve production cost.
Summary of the invention
The object of the present invention is to provide a kind of high-strong toughness X70 and above rank High Pressure Gas Transmitting Pipeline production process system with steel, adopt the present invention can be on the basis that existing pipe line steel composition and production unit are not done to change substantially, by traditional TMCP technology is obviously improved, reach the purpose of the performance potential of the existing pipe line steel of abundant excavation.Under new technology, original X70 pipe line steel can be near other level of X90 level.Its structural state is the heterogeneous structure based on the acicular ferrite AF of abundant refinement.
To achieve these goals, technical scheme of the present invention is as follows:
The present invention provides a kind of new hot mechanical controlled rolling process system (TMCP) to X70 level high-pressure natural gas line of pipes with steel, that is:
1. rolling pass is distributed: 18～22%-18～22%-20～35%-20～32%-25～35%-30～35%-33～36%, totally 7 roads: be specially: first reduction in pass is 18～22%, second reduction in pass is 18～22%, the 3rd reduction in pass is 20～35%, the four-pass draught is 20～32%, the 5th reduction in pass is that the 25～35%, the 6th reduction in pass is 30～35%, and last reduction in pass is 33～36%; Wherein respectively in the austenite recrystallization district, non-recrystallization district and austenite/ferrite two-phase region 1～3 passage controlled rolling and controlled cooling, 1150 ℃ of Heating temperatures, start rolling temperature is 1100 ℃～1050 ℃, treat that warm temperature range is 1020 ℃～950 ℃, finish rolling begins 890 ℃～920 ℃ of temperature, the finishing temperature interval is 804 ℃～750 ℃, after the finish to gauge between the controlled chilling to 550 ℃-450 ℃;
2. the type of cooling: water-cooled (20 ℃～30 ℃/s).
The principle of the invention is: on basis of proposition " controlled rolling three stage process " theories such as T.Tanaka, tissue is controlled and abundant crystal grain thinning.Promptly by in austenite recrystallization district/non-recrystallization district and austenite/ferrite two-phase region to carry out the multi-pass of strict control rolling, utilize the deformation induced ferrite transformation that below austenite static transformation temperature, takes place emphatically, cooperate (15 ℃-30 ℃/s), can obtain the heterogeneous structure of disperse distribution M/A constituent element on the acicular ferrite AF matrix of fully refinement of medium speed of cooling again.The pipe line steel microstructure and property that obtains under the process system of the present invention all near or reached the highest level of like product in the world.
The present invention provides a kind of new structural state promptly to the X70 level high-pressure natural gas line of pipes of ultrapure clean smelting with steel: 0 on the acicular ferrite AF organization foundation of fully refinement the disperse M/A constituent element that distributing.
Adopt the foundation of this heterogeneous structure to be: superfine non-disperse distributing cementite and the martensite island of waiting in the axonometer columnar ferrite AF matrix, its substructure has very high dislocation desity.This kind heterogeneous structure structure has very high intensity and toughness.Acicular ferrite AF has the characteristic of continuous surrender, so acicular ferrite AF can weaken the yield strength reduction that causes because of Bauschinger effect.And the acicular ferrite AF of abundant refinement is on the basis of phase transformation strengthening effect, make full use of the effect that refinement is strengthened, increased substantially the mechanical property of conventional needle columnar ferrite AF pipe line steel, can produce that intensity rank and toughness are higher, the better sheet material of fatigue property.Ultra-fine acicular ferrite type steel for gas delivering pipeline preparation technology
The pipe line steel of explained hereafter of the present invention is compared with capital, existing X60 Shan pipe line steel and is had more following advantage:
1. the pipe line steel that technology of the present invention obtains has higher intensity and very high low-temperature impact toughness, also has good antifatigue crack propagation ability simultaneously.Its commercial X60 pipe line steel of fatigue life ratio under simulation pipeline actual motion condition improves more than 70%, improves more than 20% than commercial X70 pipe line steel.
2. the pipe line steel of employing technology of the present invention can obtain the heterogeneous structure of disperse distribution M/A constituent element on the acicular ferrite AF matrix of fully refinement, and its grain-size is significantly less than commercial X60 pipe line steel, and average grain size reaches about 2um.
3. the good combination property of pipe line steel.Employing the present invention be specially: σ
s=649～715MPa, σ
b=605～625MPa, δ
50=21.2～24.6%, CVN
-40 ℃=132～149J, CVN
-100 ℃=119～137J, CVN
-160 ℃=103～107J (half-size scale sample, 55 * 5mm).
Description of drawings
Fig. 1 is one embodiment of the invention metallographic structure figure.
Fig. 2 is another embodiment of the present invention metallographic structure figure.
Fig. 3 is another embodiment metallographic structure of the present invention figure.
Fig. 4 is X60 steel metallographic structure figure in the prior art.
Fig. 5 is X70 steel metallographic structure figure in the prior art.
Fig. 6 is one of the present invention and contrasts routine metallographic structure figure.
Embodiment
Below in conjunction with drawings and Examples the present invention is described in further detail.
Embodiment 1
Two kinds of pipe line steels adopt vacuum induction melting, forging also is machined to the square billet that is of a size of 70 * 80 * 80mm, according to pipe line steel technology of the present invention, carries out hot mechanical controlled rolling and controlled cooling on small section mill, in constant-temperature oven, simulate at last and batch, be rolled into the thick sheet material of 7mm.For present embodiment billet size rolling technology totally 7 roads (20%-20%-33%-20%-33%-30%-36%), 70-56-45-30-24-16-11-7, be specially: first passage is rolled to 56mm from thickness 70mm, second passage is rolled to 45mm from 56mm, the 3rd passage is rolled to 30mm from 45mm, and four-pass is rolled to 24mm from 30mm, and the 5th passage is rolled to 16mm from 24mm, four-pass is rolled to 11mm from 16mm, and last passage is rolled to 7mm from 11mm; 20 ℃/second of water-cooleds.1150 ℃ of Heating temperatures.
Its chemical ingredients sees Table 1, process system of the present invention sees Table 2, the mechanical property of the embodiment of the invention and reference examples sees Table 3, and the embodiment of the invention (in austenite recrystallization district 3 passages, non-recrystallization district 3 passages and austenite/ferrite two-phase region 1 passage) and the fatigue property of reference examples see Table 4.
Present embodiment (its metallographic structure is referring to Fig. 1) is compared with X60 of the prior art, X70 and reference examples (referring to Fig. 4,5,6), and its over-all properties improves greatly, is specially: σ
sCan reach 715Mpa, σ
bCan reach 625MPa, δ
50Can reach 22.3%, CVN
-40 ℃Can reach 132J, CVN
-100 ℃Can reach 129J, CVN
-160 ℃Can reach 103J (half-size scale sample, 55 * 10 * 5mm).
Embodiment 2
Difference from Example 1 is:
Described rolling 7 road technologies are: 70-57-45-34-24-16-10.5-7 (18%-21%-24%-30%-33%-34%-33%), 30 ℃/second of water-cooleds.
Its chemical ingredients sees Table 1, the present embodiment process system sees Table 2, the mechanical property of present embodiment and reference examples sees Table 3, and the present embodiment (in austenite recrystallization district 3 passages, non-recrystallization district 3 passages and austenite/ferrite two-phase region 1 passage) and the fatigue property of reference examples see Table 4.
Present embodiment (its metallographic structure is referring to Fig. 2) is compared σ with X60 of the prior art, X70 and reference examples (referring to Fig. 4,5,6)
sCan reach 698Mpa, σ
bCan reach 612MPa, δ
50Can reach 24.6%, CVN
-40 ℃Can reach 143J, CVN
-100 ℃Can reach 136J, CVN
-160 ℃Can reach 106J (half-size scale sample, 55 * 10 * 5mm).
Embodiment 3
Difference from Example 1 is:
Described rolling 7 road technologies are: 70-56-45-32-22-16-11-7 (20%-20%-29%-31%-27%-31%-36%), 25 ℃/second of water-cooleds.
Its chemical ingredients sees Table 1, process system of the present invention sees Table 2, the mechanical property of the embodiment of the invention and reference examples sees Table 3, and the embodiment of the invention (in austenite recrystallization district 3 passages, non-recrystallization district 3 passages and austenite/ferrite two-phase region 1 passage) and the fatigue property of reference examples see Table 4.
The embodiment of the invention (its metallographic structure is referring to Fig. 3) is compared σ with X60 of the prior art, X70 and reference examples (referring to Fig. 4,5,6)
sCan reach 645Mpa, σ
bCan reach 602MPa, δ
50Can reach 20%, CVN
-40 ℃Can reach 149J, CVN
-100 ℃Can reach 137J, CVN
-160 ℃Can reach 106J (half-size scale sample, 55 * 10 * 5mm).
The chemical ingredients of table 1, embodiment of the invention pipe line steel
| Steel grade | C | Si | Mn | P | S | Mo | Ti | Nb | V | O | N |
| A1 | 0.025 | 0.24 | 1.56 | 0.0020 | 0.0006 | 0.32 | - | 0.039 | 0.019 | 0.0043 | 0.0062 |
Table 2, the embodiment of the invention 1～3 process system
| Test piece number (Test pc No.) | Open rolling | Finish rolling | Finish to gauge | Cooling rate (℃/s) | Final cooling temperature (℃) | ||||
| 70-56 | 56-45 | 45-30 | 30-24 | 24-16 | 16-11 | 11-7 | |||
| A11 | 1050 | 1014 | 974 | 903 | 798 | 21.5 | 535 | ||
| 70-57 | 57-45 | 45-34 | 34-24 | 24-16 | 16-10.5 | 10.5-7 | |||
| A12 | 1052 | 1000 | 957 | 899 | 750 | 26.8 | 530 | ||
| 70-56 | 56-45 | 45-32 | 32-22 | 22-16 | 16-11 | 11-7 | |||
| A13 | 1080 | 1008 | 955 | 893 | 804 | 30 | 477 |
Table 3 mechanical property of materials test-results
| Test piece number (Test pc No.) | σ s(MPa) | σ b(MPa) | Y·R | δ 50(％) | CVN -40℃(J) | CVN -100℃(J) | CVN -160℃(J) |
| A11 | 715.5 | 625.5 | 0.87 | 22.3 | 132 | 129 | 103 |
| A12 | 698.5 | 612 | 0.88 | 24.4 | 143 | 136 | 106 |
| A13 | 645 | 602 | 0.93333 | 20 | 149 | 137 | 106 |
| A1 (not adopting new technology) | 571～589 | 510～528 | 0.89～0.9 | 24～27.5 | 146 | - | - |
Table 4 test result of fatigue life:
| Material | Fatigue loading (MPa) | Fatigue lifetime (Cycle) | Ratio with X60 |
| X60 | 372 | 26482 | 1.00 |
| X70 | 410 | 37310 | 1.40 |
| A1 (not adopting new technology) | 415.8 | 27758 | 1.05 |
| A11 | 450 | 44983 | 1.70 |
| A12 | 443 | 44626 | 1.68 |
| A13 | 436 | 43777 | 1.65 |
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| Application Number | Priority Date | Filing Date | Title |
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| CNB2003101191008A CN1302128C (en) | 2003-12-15 | 2003-12-15 | Process for making high-performance ultra-fine needle form ferrite type gas delivery pipe steel |
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| CNB2003101191008A CN1302128C (en) | 2003-12-15 | 2003-12-15 | Process for making high-performance ultra-fine needle form ferrite type gas delivery pipe steel |
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| CN1302128C true CN1302128C (en) | 2007-02-28 |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP5292784B2 (en) * | 2006-11-30 | 2013-09-18 | 新日鐵住金株式会社 | Welded steel pipe for high-strength line pipe excellent in low temperature toughness and method for producing the same |
| CN103658170B (en) * | 2012-09-26 | 2015-11-18 | 中国石油天然气集团公司 | The milling method of pipe line steel and steel pipe |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06293916A (en) * | 1993-04-07 | 1994-10-21 | Nippon Steel Corp | Production of low alloy steel plate for line pipe excellent in co2 corrosion resisrance |
| JPH08209241A (en) * | 1995-02-02 | 1996-08-13 | Nippon Steel Corp | Method for producing steel sheet for line pipe excellent in CO 2 corrosion resistance and low temperature toughness |
| JPH10265847A (en) * | 1997-03-27 | 1998-10-06 | Nkk Corp | Production of high strength high toughness hot rolled steel plate |
| CN1351187A (en) * | 2000-10-26 | 2002-05-29 | 中国科学院金属研究所 | Process for preparing high-cleanness, high-strength and high-toughness steel for gas delivering pipeline |
| CN1351189A (en) * | 2000-11-01 | 2002-05-29 | 中国科学院金属研究所 | Ultravlow-carbon high-toughness steel resisting hydrogen sulfide for gas deliver pipeline |
-
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06293916A (en) * | 1993-04-07 | 1994-10-21 | Nippon Steel Corp | Production of low alloy steel plate for line pipe excellent in co2 corrosion resisrance |
| JPH08209241A (en) * | 1995-02-02 | 1996-08-13 | Nippon Steel Corp | Method for producing steel sheet for line pipe excellent in CO 2 corrosion resistance and low temperature toughness |
| JPH10265847A (en) * | 1997-03-27 | 1998-10-06 | Nkk Corp | Production of high strength high toughness hot rolled steel plate |
| CN1351187A (en) * | 2000-10-26 | 2002-05-29 | 中国科学院金属研究所 | Process for preparing high-cleanness, high-strength and high-toughness steel for gas delivering pipeline |
| CN1351189A (en) * | 2000-11-01 | 2002-05-29 | 中国科学院金属研究所 | Ultravlow-carbon high-toughness steel resisting hydrogen sulfide for gas deliver pipeline |
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