CN102121060B - Method for improving strength and toughness of high-strength steel for coal machine by utilizing ultra-fast cooling and steel plate self-tempering technologies - Google Patents
Method for improving strength and toughness of high-strength steel for coal machine by utilizing ultra-fast cooling and steel plate self-tempering technologies Download PDFInfo
- Publication number
- CN102121060B CN102121060B CN 201110040675 CN201110040675A CN102121060B CN 102121060 B CN102121060 B CN 102121060B CN 201110040675 CN201110040675 CN 201110040675 CN 201110040675 A CN201110040675 A CN 201110040675A CN 102121060 B CN102121060 B CN 102121060B
- Authority
- CN
- China
- Prior art keywords
- temperature
- tempering
- steel plate
- self
- strength
- 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.)
- Expired - Fee Related
Links
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a method for improving the strength and toughness of the high-strength steel for a coal machine by utilizing the ultra-fast cooling and steel plate self-tempering technologies. The method is characterized by comprising the following steps: heating a plate blank, performing rough rolling, performing finish rolling, performing ultra-fast cooling and performing steel plate self-tempering. Particularly, the soaking temperature and soaking time of the plate blank, the rough rolling initial rolling temperature, the rough rolling single-pass reduction ratio, the finish rolling initial rolling temperature, the finish rolling single-pass reduction ratio, the ultra-fast cooling initial cooling temperature, the ultra-fast cooling final cooling temperature, the ultra-fast cooling speed, the self-tempering stacking temperature, the self-tempering time and other parameters are controlled. Therefore, the produced high-strength steel for the coal machine has excellent combination of strength and toughness and the ductile transition temperature is below -60 DEG C. The hard phase content of the duplex structure can reach 30-40%, the tensile strength of the steel plate is 1200-1350MPa, and the yield ratio is lower and is about 0.80. By adopting the self-tempering treatment, the internal stress of the structure can be eliminated, so that the structure has 60-70% of soft phase, the plasticity index can be obviously increased and the elongation rate can reach 25%.
Description
Technical field:
What the present invention relates to is the Technology that improves the steel plate obdurability, is a kind of method of utilizing ultrafast cold-peace steel plate self-tempering technology to improve coal machine usefulness high-strength steel obdurability.
Background technology:
Prick in the cooling control technology in traditional control, because control cold energy power is limited, must accumulate more strain energy in the operation of rolling, mostly be to adopt that low temperature is depressed greatly, intense plastic strain, two-phase region are rolling etc. technique realizes, particularly in the cold stage of control, the convective exchange coefficient of water coolant and hot steel plate is much larger than the heat-conduction coefficient of steam and hot steel plate, and steam film is difficult for being broken, and does not have the cold effect of desirable control.Simultaneously, because inhomogeneous cooling is even, also easily cause camber of sheet.On performance index, the modal disadvantage of UFG technique is that the unit elongation of steel plate is low, does not have yield-point, and plasticity is poor.The practices well that addresses the aforementioned drawbacks at present is to remedy by thermal treatment process, but has increased cost, has prolonged the manufacturing cycle.
Summary of the invention:
The objective of the invention is the weak point for present routine techniques, provide the ultrafast cold-peace steel plate of a kind of usefulness self-tempering technology to improve the method that the coal machine is used the high-strength steel obdurability, obtain hard phase martensite and the heterogeneous structures such as soft mutually granular bainite, the method flow process is short, efficient is high, easy to operate.
The technical solution used in the present invention, the processing step that comprises has: slab reheats; Roughing; Finish rolling; Ultrafast cold; The steel plate self-tempering; Air cooling gets finished steel plate; Wherein:
The soaking temperature scope that described slab reheats is 1100-1150 ℃, and the soaking time scope is 2.5-4.0 hour; Suppress Austenite Grain Growth by TiN particle and the low-temperature heat that utilizes small and dispersed, obtain tiny and uniform austenite crystal;
The start rolling temperature of described roughing is 1050-1100 ℃, and the single pass draft is greater than 20%; By recrystallization softening austenite crystal repeatedly;
The start rolling temperature scope of described finish rolling is 880-900 ℃, and the single pass draft is greater than 15%; Impose aximal deformation value in crystallization austenitic area not, make austenite crystal be drawn into deformation bands;
The described ultrafast cold cold temperature of opening is not less than 760 ℃, and final cooling temperature is lower than 420 ℃, and the speed of cooling scope is 30-45 ℃/s; Form the high-density substructure, obtain tiny uniform complex phase microstructure;
Described steel plate self-tempering: utilize the waste heat of steel plate to carry out the stacking covering, the stacking temperature is 280～330 ℃, and soaking time is controlled at 1.5-2.0min/mm.
Further, utilize ultrafast cold-peace steel plate self-tempering technology to improve the method that the coal machine is used the high-strength steel obdurability, its processing parameter is that described slab soaking temperature is: 1120 ℃; Soaking time: 3.0 hours; Roughing start rolling temperature: 1080 ℃; Roughing single pass draft: greater than 22%; Finish rolling start rolling temperature: 890 ℃; Finish rolling single pass draft: greater than 16%; The ultrafast cold cold temperature of opening: 770 ℃; Ultrafast cold final cooling temperature: 390 ℃; Ultrafast cold but speed: 38 ℃/s; Self-tempering stacking temperature: 320 ℃; Self-tempering time 50min.
Further, utilize ultrafast cold-peace steel plate self-tempering technology to improve the method that the coal machine is used the high-strength steel obdurability, its processing parameter is that described slab soaking temperature is: 1150 ℃; Soaking time: 2.8 hours; Roughing start rolling temperature: 1120 ℃; Roughing single pass draft: greater than 20%; Finish rolling start rolling temperature: 900 ℃; Finish rolling single pass draft: greater than 18%; The ultrafast cold cold temperature of opening: 790 ℃; Ultrafast cold final cooling temperature: 400 ℃; Ultrafast cold but speed: 35 ℃/s; Self-tempering stacking temperature: 300 ℃; Self-tempering time 50min.
Further, utilize ultrafast cold-peace steel plate self-tempering technology to improve the method that the coal machine is used the high-strength steel obdurability, its processing parameter is that described slab soaking temperature is: 1100 ℃; Soaking time: 3.5 hours; Roughing start rolling temperature: 1070 ℃; Roughing single pass draft: greater than 25%; Finish rolling start rolling temperature: 880 ℃; Finish rolling single pass draft: greater than 20%; The ultrafast cold cold temperature of opening: 800 ℃; Ultrafast cold final cooling temperature: 390 ℃; Ultrafast cold but speed: 42 ℃/s; Self-tempering stacking temperature: 320 ℃; Self-tempering time 60min.
Further, utilize ultrafast cold-peace steel plate self-tempering technology to improve the method that the coal machine is used the high-strength steel obdurability, its processing parameter is that described slab soaking temperature is: 1130 ℃; Soaking time: 3.6 hours; Roughing start rolling temperature: 1100 ℃; Roughing single pass draft: greater than 30%; Finish rolling start rolling temperature: 900 ℃; Finish rolling single pass draft: greater than 18%; The ultrafast cold cold temperature of opening: 775 ℃; Ultrafast cold final cooling temperature: 420 ℃; Ultrafast cold but speed: 36 ℃/s; Self-tempering stacking temperature: 330 ℃; Self-tempering time 40min.
Further, utilize ultrafast cold-peace steel plate self-tempering technology to improve the method that the coal machine is used the high-strength steel obdurability, its processing parameter is that described slab soaking temperature is: 1120 ℃; Soaking time: 4.0 hours; Roughing start rolling temperature: 1090 ℃; Roughing single pass draft: greater than 22%; Finish rolling start rolling temperature: 900 ℃; Finish rolling single pass draft: greater than 19%; The ultrafast cold cold temperature of opening: 790 ℃; Ultrafast cold final cooling temperature: 400 ℃; Ultrafast cold but speed: 30 ℃/s; Self-tempering stacking temperature: 330 ℃; Self-tempering time 35min.
The invention has the beneficial effects as follows: the coal machine that adopts the present invention to produce has reached excellent obdurability coupling with high-strength steel, and tough brittle transition temperature is below-60 ℃.Hard phase content in the heterogeneous structure can reach 30-40%, and the tensile strength scope of steel plate is at 1200-1350MPa, and yield tensile ratio is lower, about 0.80.Process by self-tempering, eliminated and organized internal stress, the soft phase constitution of 60-70% is arranged in the tissue in addition, obviously improved plasticity index, unit elongation can reach 25%.This shows that the present invention compared with prior art has substantial progress, implementation result is remarkable.
Embodiment:
The invention will be further described below in conjunction with the implementation example, but be not construed as limiting the invention.
Slab melting composition is:
C:0.05%, Si:0.38%, Mn:1.72%, P:0.010%, S:0.007%, Mo:0.25%, Al:0.033%, B:0.0011%, Nb:0.052%, Ti:0.013%, Ni:0.26%, all the other are Fe and inevitable impurity.
Embodiment 1
The slab soaking temperature (℃): 1120; Soaking time (hour): 3.0; The roughing temperature (℃): 1080; Roughing single pass draft (%): greater than 22; Final rolling temperature (℃): 890; Finish rolling single pass draft (%): greater than 16; Ultrafast cold open cold temperature (℃): 770; Ultrafast cold final cooling temperature (℃): 390; Ultrafast cold but speed (℃/s): 38; Self tempering temperature (℃): 320; The self-tempering time (min): 50.
Rolling steel plate mechanical property:
Specification: steel plate thickness 30mm; Yield strength (MPa): 980; Tensile strength (MPa): 1209; Yield tensile ratio: 0.81; Elongation after fracture (%): 22.5; Clod wash: qualified; V-type impact of collision merit (40 ℃): 180J, 182J, 193J; V-type impact of collision merit (60 ℃): 132J, 152J, 161J.
Embodiment 2
The slab soaking temperature (℃): 1150; Soaking time (hour): 2.8; The roughing temperature (℃): 1120; Roughing single pass draft (%): greater than 20; Final rolling temperature (℃): 900; Finish rolling single pass draft (%): greater than 18; Ultrafast cold open cold temperature (℃): 790; Ultrafast cold final cooling temperature (℃): 400; Ultrafast cold but speed (℃/s): 35; Self tempering temperature (℃): 300; The self-tempering time (min): 50.
Rolling steel plate mechanical property:
Specification: steel plate thickness 28mm; Yield strength (MPa): 950; Tensile strength (MPa): 1202; Yield tensile ratio: 0.79; Elongation after fracture (%): 20.5; Clod wash: qualified; V-type impact of collision merit (40 ℃): 150J, 132J, 173J; V-type impact of collision merit (60 ℃): 112J, 103J, 122J.
Embodiment 3
The slab soaking temperature (℃): 1100; Soaking time (hour): 3.5; The roughing temperature (℃): 1070; Roughing single pass draft (%): greater than 25; Final rolling temperature (℃): 880; Finish rolling single pass draft (%): greater than 20; Ultrafast cold open cold temperature (℃): 800; Ultrafast cold final cooling temperature (℃): 390; Ultrafast cold but speed (℃/s): 42; Self tempering temperature (℃): 320; The self-tempering time (min): 60.
Rolling steel plate mechanical property:
Specification: steel plate thickness 35mm; Yield strength (MPa): 1078; Tensile strength (MPa): 1315; Yield tensile ratio: 0.82; Elongation after fracture (%): 19.5; Clod wash: qualified; V-type impact of collision merit (40 ℃): 99J, 115J, 133J; V-type impact of collision merit (60 ℃): 92J, 105J, 116J.
Embodiment 4
The slab soaking temperature (℃): 1130; Soaking time (hour): 3.6; The roughing temperature (℃): 1100; Roughing single pass draft (%): greater than 30; Final rolling temperature (℃): 900; Finish rolling single pass draft (%): greater than 18; Ultrafast cold open cold temperature (℃): 775; Ultrafast cold final cooling temperature (℃): 420; Ultrafast cold but speed (℃/s): 36; Self tempering temperature (℃): 330; The self-tempering time (min): 40.
Rolling steel plate mechanical property:
Specification: steel plate thickness 22mm; Yield strength (MPa): 1065; Tensile strength (MPa): 1330; Yield tensile ratio: 0.80 elongation after fracture (%): 23.0; Clod wash: qualified; V-type impact of collision merit (40 ℃): 125J, 151J, 133J; V-type impact of collision merit (60 ℃): 100J, 122J, 107J.
Embodiment 5
The slab soaking temperature (℃): 1120; Soaking time (hour): 4.0; The roughing temperature (℃): 1090; Roughing single pass draft (%): greater than 22; Final rolling temperature (℃): 900; Finish rolling single pass draft (%): greater than 19; Ultrafast cold open cold temperature (℃): 790; Ultrafast cold final cooling temperature (℃): 400; Ultrafast cold but speed (℃/s): 30; Self tempering temperature (℃): 330; The self-tempering time (min): 35.
Rolling steel plate mechanical property:
Specification: steel plate thickness 18mm; Yield strength (MPa): 990; Tensile strength (MPa): 1285; Yield tensile ratio: 0.77; Elongation after fracture (%): 25.0; Clod wash: qualified; V-type impact of collision merit (40 ℃): 112J, 162J, 113J; V-type impact of collision merit (60 ℃): 100J, 127J, 101J.
Claims (2)
1. one kind is utilized ultrafast cold-peace steel plate self-tempering technology to improve the method that the coal machine is used the high-strength steel obdurability, and its processing step comprises: slab reheats; Roughing; Finish rolling; Ultrafast cold; The steel plate self-tempering; Air cooling gets finished steel plate, and the tensile strength scope of steel plate is 1200-1350MPa; Wherein:
The soaking temperature scope that described slab reheats is 1100-1150 ℃, and the soaking time scope is 2.5-4.0 hour; Suppress Austenite Grain Growth by TiN particle and the low-temperature heat that utilizes small and dispersed, obtain tiny and uniform austenite crystal;
The start rolling temperature of described roughing is 1050-1100 ℃, and the single pass draft is greater than 20%; By recrystallization softening austenite crystal repeatedly;
The start rolling temperature scope of described finish rolling is 880-900 ℃, and the single pass draft is greater than 15%; Impose aximal deformation value in crystallization austenitic area not, make austenite crystal be drawn into deformation bands;
The described ultrafast cold cold temperature of opening is not less than 760 ℃, and final cooling temperature is lower than 420 ℃, and the speed of cooling scope is 35-45 ℃/s; Form the high-density substructure, obtain tiny uniform complex phase microstructure;
Described steel plate self-tempering: utilize the waste heat of steel plate to carry out the stacking covering, the stacking temperature is 280～330 ℃, and soaking time is controlled at 1.5-2.0min/mm;
Described slab melting composition is by weight percentage: C:0.05%, Si:0.38%, Mn:1.72%, P:0.010%, S:0.007%, Mo:0.25%, Al:0.033%, B:0.0011%, Nb:0.052%, Ti:0.013%, Ni:0.26%, all the other are Fe and inevitable impurity.
2. the method for utilizing ultrafast cold-peace steel plate self-tempering technology to improve coal machine usefulness high-strength steel obdurability according to claim 1 is characterized in that described slab soaking temperature is: 1120 ℃; Soaking time: 3.0 hours; Roughing start rolling temperature: 1080 ℃; Roughing single pass draft: greater than 22%; Finish rolling start rolling temperature: 890 ℃; Finish rolling single pass draft: greater than 16%; The ultrafast cold cold temperature of opening: 770 ℃; Ultrafast cold final cooling temperature: 390 ℃; Ultrafast cold but speed: 38 ℃/s; Self-tempering stacking temperature: 320 ℃; Self-tempering times 50 min.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201110040675 CN102121060B (en) | 2011-02-18 | 2011-02-18 | Method for improving strength and toughness of high-strength steel for coal machine by utilizing ultra-fast cooling and steel plate self-tempering technologies |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201110040675 CN102121060B (en) | 2011-02-18 | 2011-02-18 | Method for improving strength and toughness of high-strength steel for coal machine by utilizing ultra-fast cooling and steel plate self-tempering technologies |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102121060A CN102121060A (en) | 2011-07-13 |
| CN102121060B true CN102121060B (en) | 2013-02-13 |
Family
ID=44249726
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 201110040675 Expired - Fee Related CN102121060B (en) | 2011-02-18 | 2011-02-18 | Method for improving strength and toughness of high-strength steel for coal machine by utilizing ultra-fast cooling and steel plate self-tempering technologies |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102121060B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107674954B (en) * | 2017-09-20 | 2019-04-09 | 武汉科技大学 | The method for improving multi-phase Steels comprehensive performance using deformation Substructure after hot rolling |
| CN110468330A (en) * | 2019-08-27 | 2019-11-19 | 南京钢铁股份有限公司 | Exempt to be heat-treated single-track turnout weather-resistant steel plate and preparation method |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101153370A (en) * | 2006-09-27 | 2008-04-02 | 鞍钢股份有限公司 | Low-alloy high-strength steel plate capable of being welded at high heat input and manufacturing method thereof |
| CN101397625A (en) * | 2007-09-24 | 2009-04-01 | 宝山钢铁股份有限公司 | Superfine grain steel sheet with yield strength of 420 MPa grade and method for producing the same |
| CN101906585A (en) * | 2009-06-08 | 2010-12-08 | 鞍钢股份有限公司 | High-performance fire-resistant steel plate for building structure and manufacturing method thereof |
-
2011
- 2011-02-18 CN CN 201110040675 patent/CN102121060B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101153370A (en) * | 2006-09-27 | 2008-04-02 | 鞍钢股份有限公司 | Low-alloy high-strength steel plate capable of being welded at high heat input and manufacturing method thereof |
| CN101397625A (en) * | 2007-09-24 | 2009-04-01 | 宝山钢铁股份有限公司 | Superfine grain steel sheet with yield strength of 420 MPa grade and method for producing the same |
| CN101906585A (en) * | 2009-06-08 | 2010-12-08 | 鞍钢股份有限公司 | High-performance fire-resistant steel plate for building structure and manufacturing method thereof |
Non-Patent Citations (5)
| Title |
|---|
| 叶建军等.新型调质高强钢WH80Q的研制开发.《宽厚板》.2006,第12卷(第1期),35-38. |
| 康健等.工程机械用960MPa级调质钢板的淬火工艺研究.《东北大学学报（自然科学版）》.2011,第32卷(第1期),52-55. * |
| 新型调质高强钢WH80Q的研制开发;叶建军等;《宽厚板》;20060228;第12卷(第1期);35-38 * |
| 程四华等.100kg级超高强贝氏体钢的拉伸性能分析.《2009高品质特殊钢技术与市场论坛》.2009,143-146. * |
| 胡淑娥等.高强度结构钢直接淬火回火工艺试验研究.《山东冶金》.2010,第32卷(第3期),45-47. * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102121060A (en) | 2011-07-13 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101613828B (en) | Super-thick steel plate for low yield ratio buildings with 460 MPa grade yield strength and manufacturing method | |
| CN103014554B (en) | Low-yield-ratio high-tenacity steel plate and manufacture method thereof | |
| CN103233183B (en) | A kind of yield strength 960MPa grade super strength steel plate and manufacture method thereof | |
| CN101613831B (en) | Non-hardened and non-tempered high-hardness hot rolled steel, manufacturing method thereof and application thereof | |
| CN106811698A (en) | High-strength steel plate based on fine structure control and manufacturing method thereof | |
| CN103352167A (en) | Low-yield ratio and high-strength steel for bridges and manufacturing method thereof | |
| CN102943169A (en) | Quenching and annealing preparation method of ultrahigh-strength thin steel plate for automobiles | |
| CN104498821B (en) | Medium-manganese high-strength steel for automobiles and production method thereof | |
| CN104294160A (en) | High-hardness high-toughness low-carbon martensite stainless steel and manufacturing method thereof | |
| CN102286695A (en) | High-plasticity high-toughness and ultra-high-intensity steel plate and production method thereof | |
| CN102492823B (en) | Continuous annealing process of cold rolling low alloy high-strength steel plate with yield strength at grade of 420 MPa | |
| CN101649420A (en) | Ultra-strength, high toughness and low yield ratio steel and steel plate and manufacturing method thereof | |
| CN102676945A (en) | Easily-weldable tempered high-strength ductile steel plate used in hydroelectric projects and production method thereof | |
| CN103320701A (en) | Ferrite bainite advanced high strength steel plate and manufacturing method thereof | |
| CN103255340A (en) | Vehicle high strength and toughness hot-forming steel plate and preparation method thereof | |
| CN104846293A (en) | High-strength high-toughness steel plate and preparation method thereof | |
| CN101831594B (en) | Method for manufacturing high-strength steel plate used in low-temperature environment | |
| CN113546960A (en) | Micro-alloying-free rolling and cooling control method for slitting rolling of bar deformed steel bar | |
| CN102260823B (en) | Economic high-strength steel plate with yield strength of 690MPa, and manufacture method thereof | |
| CN102121060B (en) | Method for improving strength and toughness of high-strength steel for coal machine by utilizing ultra-fast cooling and steel plate self-tempering technologies | |
| CN103276315A (en) | 900MPa-level ultrahigh-tenacity high-toughness pipeline steel plate and manufacturing method thereof | |
| CN103882335B (en) | Hot-rolled high-strength steel with yield strength of 800MPa and production method thereof | |
| CN102534419A (en) | Super-martensitic stainless steel and preparation method thereof | |
| CN102560244B (en) | Microalloying and heat treatment method for 20MnMo steel | |
| CN102154585B (en) | High-intensity quake-resistant steel bar for buildings and manufacturing method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C53 | Correction of patent for invention or patent application | ||
| CB03 | Change of inventor or designer information |
Inventor after: Sun Weihua Inventor after: Han Qibiao Inventor after: Chu Shihao Inventor after: Hou Dengyi Inventor after: Xiao Fengqiang Inventor after: Hu Shue Inventor after: Sun Hao Inventor after: Bi Zhichao Inventor after: Li Meiguang Inventor after: Wang Nanhui Inventor after: Jia Huiling Inventor before: Sun Weihua Inventor before: Han Qibiao Inventor before: Chu Shihao Inventor before: Sun Hao Inventor before: Hu Shue Inventor before: Zhang Jiming Inventor before: Hou Dengyi Inventor before: Xiao Fengqiang Inventor before: Feng Yong Inventor before: Jiang Shanyu Inventor before: Jia Huiling |
|
| COR | Change of bibliographic data |
Free format text: CORRECT: INVENTOR; FROM: SUN WEIHUA SUN HAO HU SHUE ZHANG JIMING HOU DENGYI XIAO FENGQIANG FENG YONG JIANG SHANYU JIA HUILING HAN QIBIAO CHU SHIHAO TO: SUN WEIHUA HOU DENGYI XIAO FENGQIANG HU SHUE SUN HAO BI ZHICHAO LI MEIGUANG WANG NANHUI JIA HUILING HAN QIBIAO CHU SHIHAO |
|
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20130213 Termination date: 20190218 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |