CN105803174A - Production method of low-yield-ratio Q460GJ steel plate - Google Patents
Production method of low-yield-ratio Q460GJ steel plate Download PDFInfo
- Publication number
- CN105803174A CN105803174A CN201610369051.0A CN201610369051A CN105803174A CN 105803174 A CN105803174 A CN 105803174A CN 201610369051 A CN201610369051 A CN 201610369051A CN 105803174 A CN105803174 A CN 105803174A
- Authority
- CN
- China
- Prior art keywords
- steel plate
- rolling
- production method
- tempering
- ratio
- 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.)
- Pending
Links
Classifications
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0231—Warm 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/28—Normalising
-
- 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
- C21D2211/002—Bainite
-
- 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
Abstract
The invention discloses a production method of a low-yield-ratio Q460GJ steel plate. The production method comprises (1) a rolling process: an II-type controlled rolling process is adopted, and low-temperature rolling is adopted in the phase II, with the rolling starting temperature less than or equal to 760 DEG C; (2) thermal treatment process: a normalization process conducted twice and a tempering process are adopted, with the tempering temperature of 500 +/- 20 DEG C and the total heating time of 200 min to 300 min. According to the production method, rolling and cooling parameters are strictly controlled, so that various mechanical property indexes meeting the requirements of technical conditions are obtained, and the production cost is reduced; meanwhile, a thinner and smaller tissue structure and higher welding performance are achieved.
Description
Technical field
The present invention relates to a kind of low yield strength ratio Q460GJ Plate Production method, belong to technical field of metal.
Background technology
It is gradually increased along with high-strength steel at home manufacturing present consumption, especially with the fast development of steel building, and at present China can't produce greater strength rank height in batches and builds with steel, such as steel plate more than 550Mpa rank, the thickness of steel plate for building, toughness, yield tensile ratio, weldability etc. are had higher requirement by portions of client, some iron and steel producer domestic can only produce maximum 100mm thickness Q460GJ steel plate, it is impossible to meets growing high-strength, the slab market demand.
Chinese patent CN101613828A discloses " yield strength 460MPa level super-thick steel plate for low yield ratio buildings and manufacture method thereof ", continuous casting billet rolls through two-stage control, two-phase section quenching and tempering heat treatment, the final yield strength that obtains reaches more than 440MPa, yield tensile ratio<0.72, thickness>steel plate for building of 80mm, performance meets GB/T19879-2005 requirement.Maximum of its sheet metal thickness arrives 100mm, it is difficult to meet the market demand of more than 150mm slab, and it adopts two-phase section quenching and tempering heat treatment process, relatively costly.
Summary of the invention
The present invention provides a kind of low yield strength ratio Q460GJ Plate Production method, strict controlled rolling and cooling parameter, after the thermally treated process of steel plate, not only obtain every mechanical performance index of technical conditions requirement but also reduce production cost, obtain more tiny organizational structure and welding performance more preferably simultaneously.
The technical solution used in the present invention is:
A kind of low yield strength ratio Q460GJ Plate Production method, rolling mill practice adopts II type controlled rolling process, and the II stage adopts zerolling, start rolling temperature≤760 DEG C；
Technology for Heating Processing: adopt 2 times normalizing process+tempering process, tempering process temperature: 500 DEG C ± 20 DEG C, total heat time heating time: 200min～300min.
Preferably, the thickness of steel plate is 150mm～180mm.
It is further preferred that steel plate yield tensile ratio≤0.83.
Zerolling technique is to roll for common controlled rolling, and its start rolling temperature is in two-phase section, and the purpose of do so is in that better fining ferrite, bainite crystal grain, belongs to ultra fine nlicrostructures technique.For F+P+B organization type steel plate, common controlled rolling steel plate start rolling temperature is lower than 920 DEG C, and zerolling technique will lower than 800 DEG C, and in the present invention, start rolling temperature requires lower, controlled rolling below 760 DEG C.
The present invention adopts low temperature open rolling at rolling sequence, it is possible to complete continuous large deformation and strain accumulation in the temperature range being suitable to deformation, the deformed austenite tissue more refined；After rolling, austenite is to ferrite or bainitic transformation, and grain size can be more tiny.Compared with common controlled rolling process, this technique can effectively break water-cooled steam film, realize controlled rolling steel plate is carried out the cooling of more high uniformity, fully refine the grain size of original austenite, ferrite after structural transformation or about 35 μm of bainite crystallite dimension after two-phase section rolling, grain size is more than 9 grades, and this grain size is for very tiny 150mm 180mm slab, and the ferritic phase of refinement advantageously reduces yield tensile ratio and steel plate toughness index.Follow-up Technology for Heating Processing adopts 2 times normalizing process, and meeting refinement again, uniform formation, the hard phase constitution in tempering after-tack surface, the processing type being conducive to product is good.The technique of the present invention can not only the product of excellent, and save alloy, reduce cost.
The steel plate of the present invention is Nb-V-Cr system microalloy element steel.
The low yield strength ratio Q460GJ steel plate of the present invention is through special Technology for Heating Processing, it is thus achieved that good obdurability coupling, does not reduce again the welding performance of slab simultaneously.It is main that light plate of the present invention is organized as F, and then can reduce yield tensile ratio further.And the tempering B of nodularization organizes and passes through ultralow temperature rolling refined grains, it is possible to improve the intensity of steel plate.The condition of delivery of steel plate of the present invention is normalizing+tempering.
Adopt the strict controlled rolling of method and the cooling parameter of the present invention, after the thermally treated process of steel plate, not only obtain every mechanical performance index of technical conditions requirement but also reduce production cost, obtain more tiny organizational structure and welding performance more preferably simultaneously；Maximum gauge specification 180mm, meets home and abroad building and constantly increases the demand of market consumption.
The mechanical property of the steel plate of the present invention reaches following requirements after testing: surrender: 460～580MPa, tension: 550～720MPa, extends: >=17%, yield tensile ratio≤0.83 ,-40 DEG C of thickness of slab 1/4 place impact of collision >=120J.Steel plate adopts normalizing+tempering heat treatment process, obtains uniform F+P+ tempering B tissue.
The invention have the advantages that (1) steel plate yield tensile ratio≤0.83, the horizontal low-temperature good toughness in-40 DEG C of place of (2) thickness of slab 1/4；
Adopt and have the beneficial effects that produced by technique scheme:
The strict controlled rolling of the present invention and cooling parameter, after the thermally treated process of steel plate, not only obtain every mechanical performance index of technical conditions requirement but also reduce production cost, obtain more tiny organizational structure and welding performance more preferably simultaneously；Maximum gauge specification 180mm, meets home and abroad building and constantly increases the demand of market consumption.
Accompanying drawing illustrates:
The metallographic 500X at steel plate thickness of slab 1/4 place of Fig. 1, Fig. 2 respectively embodiment 1 preparation and 100X micro-organization chart；
The metallographic 500X at steel plate thickness of slab 1/4 place of Fig. 3, Fig. 4 respectively embodiment 2 preparation and 100X micro-organization chart；
The metallographic 500X at steel plate thickness of slab 1/4 place of Fig. 5, Fig. 6 respectively embodiment 3 preparation and 100X micro-organization chart；
The metallographic 500X at steel plate thickness of slab 1/4 place of Fig. 7, Fig. 8 respectively embodiment 4 preparation and 100X micro-organization chart.
Detailed description of the invention
Below in conjunction with embodiment, the present invention is described further；
Embodiment 1
In the present embodiment, the thickness that rolls into of Q460GJC steel plate is: 150mm.
Prepare by following technique:
(1) rolling mill practice: adopting II type controlled rolling process, the II stage adopts zerolling, start rolling temperature 740 DEG C.
(2) Technology for Heating Processing: adopt 2 times normalizing process+tempering process.Wherein tempering process temperature is at 520 DEG C, heat time heating time 200min.
Pick test, its mechanical property: yield strength 485MPa, tensile strength 650MPa, extend: 27%, thickness of slab 1/4 place ,-40 DEG C of ballistic work AKV(are longitudinally) and 273J, 289J, 202J, yield tensile ratio: 0.75, obtain qualified finished steel plate.The metallographic 500X at Fig. 1, Fig. 2 respectively steel plate thickness of slab 1/4 place and 100X micro-organization chart, as seen from Figure 1, Figure 2, be organized as F+P+ tempering B, even tissue, and the grain size of thickness of slab 1/4 place tissue is about 9.5 grades.
Embodiment 2
In the present embodiment, the thickness that rolls into of Q460GJC steel plate is: 165mm.
Prepare by following technique:
(1) rolling mill practice: adopting II type controlled rolling process, the II stage adopts zerolling, start rolling temperature 760 DEG C.
(2) Technology for Heating Processing: adopt 2 times normalizing process+tempering process.Wherein tempering process temperature is at 500 DEG C, heat time heating time 250min.
Pick test, its mechanical property: yield strength 495MPa, tensile strength 640MPa, extend: 27.5%, thickness of slab 1/4 place ,-40 DEG C of ballistic work AKV(are longitudinally) and 193J, 189J, 132J, yield tensile ratio: 0.77, obtain qualified finished steel plate.The metallographic 500X at Fig. 3, Fig. 4 respectively steel plate thickness of slab 1/4 place and 100X micro-organization chart, by Fig. 3, Fig. 4 it can be seen that be organized as F+P+ tempering B, even tissue, the grain size of thickness of slab 1/4 place tissue is about 9.5 grades.
Embodiment 3
In the present embodiment, the thickness that rolls into of Q460GJC steel plate is: 177.5mm.
Prepare by following technique:
(1) rolling mill practice: adopting II type controlled rolling process, the II stage adopts zerolling, start rolling temperature 720 DEG C.
(2) Technology for Heating Processing: adopt 2 times normalizing process+tempering process.Wherein tempering process temperature is at 520 DEG C, heat time heating time 270min.
Pick test, its mechanical property: yield strength 465MPa, tensile strength 630MPa, extend: 23.5%, thickness of slab 1/4 place ,-40 DEG C of ballistic work AKV(are longitudinally) and 113J, 189J, 142J, yield tensile ratio: 0.74, obtain qualified finished steel plate.The metallographic 500X at Fig. 5, Fig. 6 respectively steel plate thickness of slab 1/4 place and 100X micro-organization chart, by Fig. 5, Fig. 6 it can be seen that be organized as F+P+ tempering B, even tissue, the grain size of thickness of slab 1/4 place tissue is about 9.0 grades.
Embodiment 4
In the present embodiment, the thickness that rolls into of Q460GJC steel plate is: 180mm.
Prepare by following technique:
(1) rolling mill practice: adopting II type controlled rolling process, the II stage adopts zerolling, start rolling temperature 750 DEG C.
(2) Technology for Heating Processing: adopt 2 times normalizing process+tempering process.Wherein tempering process temperature is at 480 DEG C, heat time heating time 300min.
Pick test, its mechanical property: yield strength 485MPa, tensile strength 595MPa, extend: 25.5%, thickness of slab 1/4 place ,-40 DEG C of ballistic work AKV(are longitudinally) 103,129,142J, yield tensile ratio: 0.82, obtain qualified finished steel plate.The metallographic 500X at Fig. 7, Fig. 8 respectively steel plate thickness of slab 1/4 place and 100X micro-organization chart, by Fig. 7, Fig. 8 it can be seen that be organized as F+P+ tempering B, even tissue, the grain size of thickness of slab 1/4 place tissue is about 8.5 grades.
Claims (3)
1. a low yield strength ratio Q460GJ Plate Production method, it is characterised in that:
(1) rolling mill practice: adopting II type controlled rolling process, the II stage adopts zerolling, start rolling temperature≤760 DEG C；
(2) Technology for Heating Processing: adopt 2 times normalizing process+tempering process, tempering process temperature: 500 DEG C ± 20 DEG C, total heat time heating time: 200min～300min.
2. a kind of low yield strength ratio Q460GJ Plate Production method according to claim 1, it is characterised in that the thickness of described steel plate is 150mm～180mm.
3. a kind of low yield strength ratio Q460GJ Plate Production method according to claim 2, it is characterised in that: described steel plate yield tensile ratio≤0.83.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610369051.0A CN105803174A (en) | 2016-05-30 | 2016-05-30 | Production method of low-yield-ratio Q460GJ steel plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610369051.0A CN105803174A (en) | 2016-05-30 | 2016-05-30 | Production method of low-yield-ratio Q460GJ steel plate |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN105803174A true CN105803174A (en) | 2016-07-27 |
Family
ID=56452171
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610369051.0A Pending CN105803174A (en) | 2016-05-30 | 2016-05-30 | Production method of low-yield-ratio Q460GJ steel plate |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105803174A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106929640A (en) * | 2017-04-21 | 2017-07-07 | 舞阳钢铁有限责任公司 | The heat treatment method of big thickness high tenacity 15CrMoR steel plates |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001342520A (en) * | 2000-06-02 | 2001-12-14 | Nippon Steel Corp | Method for manufacturing high tension steel of low yield ratio and superior toughness with little fluctuation of material property |
| CN101613828A (en) * | 2009-07-16 | 2009-12-30 | 首钢总公司 | Super-thick steel plate for low yield ratio buildings with 460 MPa grade yield strength and manufacture method |
| CN101845602A (en) * | 2009-03-26 | 2010-09-29 | 宝山钢铁股份有限公司 | High-performance weather-proof building structural steel and manufacturing method thereof |
| CN102021494A (en) * | 2009-09-23 | 2011-04-20 | 宝山钢铁股份有限公司 | Weather resistant thick steel plate and manufacturing method thereof |
| CN102080182A (en) * | 2010-12-27 | 2011-06-01 | 南阳汉冶特钢有限公司 | High-strength steel plate Q460GJE-Z35 for extra-thick high-rise building structure and production method thereof |
-
2016
- 2016-05-30 CN CN201610369051.0A patent/CN105803174A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001342520A (en) * | 2000-06-02 | 2001-12-14 | Nippon Steel Corp | Method for manufacturing high tension steel of low yield ratio and superior toughness with little fluctuation of material property |
| CN101845602A (en) * | 2009-03-26 | 2010-09-29 | 宝山钢铁股份有限公司 | High-performance weather-proof building structural steel and manufacturing method thereof |
| CN101613828A (en) * | 2009-07-16 | 2009-12-30 | 首钢总公司 | Super-thick steel plate for low yield ratio buildings with 460 MPa grade yield strength and manufacture method |
| CN102021494A (en) * | 2009-09-23 | 2011-04-20 | 宝山钢铁股份有限公司 | Weather resistant thick steel plate and manufacturing method thereof |
| CN102080182A (en) * | 2010-12-27 | 2011-06-01 | 南阳汉冶特钢有限公司 | High-strength steel plate Q460GJE-Z35 for extra-thick high-rise building structure and production method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 王有铭 等: "《钢材的控制轧制和控制冷却(第2版)》", 31 March 2009, 《冶金工业出版社》 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106929640A (en) * | 2017-04-21 | 2017-07-07 | 舞阳钢铁有限责任公司 | The heat treatment method of big thickness high tenacity 15CrMoR steel plates |
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 | |
| CN110184525B (en) | High-strength Q500GJE quenched and tempered steel plate for building structure and manufacturing method thereof | |
| CN102952996A (en) | High-elongation cold-rolled TRIP (Transformation-Induced Plasticity) steel plate and preparation method thereof | |
| CN105420605A (en) | Ultralow-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof | |
| CN103882292B (en) | A kind of cold rolling structural carbon steel production method | |
| CN109266815B (en) | Shape control method for online quenching high-strength steel plate | |
| CN106636911B (en) | With the 900MPa grade hot rolled steel sheets and its manufacturing method of sheet billet Direct Rolling | |
| CN104862597A (en) | Method for improving elongation of cold-rolled dual-phase steel by utilizing retained austenite | |
| CN102400038A (en) | Hot-rolled dual-phase steel and production method thereof | |
| CN102304665A (en) | Steel plate for automobile and production method thereof | |
| CN103290202B (en) | Production method for improving yield ratio and bore expansion of 1000MPa-level high-strength steel | |
| CN103276314A (en) | X80 pipeline steel plate with low yield ratio and high toughness and manufacturing method thereof | |
| CN103882314A (en) | 42 CrMo steel cold-rolled sheet and its production method | |
| CN105483545A (en) | 800MPa level hot-rolling high broaching steel plate and manufacturing method thereof | |
| CN112831731A (en) | Online quenching complex phase structure hot-rolled wear-resistant steel and preparation method thereof | |
| CN107447167A (en) | A kind of production method of low yield strength ratio high-strength medium plate | |
| CN101338400A (en) | High strength low-temperature-used low carbon bainite steel and production process thereof | |
| CN103695618B (en) | A kind of thermo-mechanical processi method preparing submicron Multiphase Steel | |
| CN104141099A (en) | Manufacturing method of super-thick X70 hot-rolled plate coil | |
| CN101633976A (en) | Direct quenching technology suitable for steel plates with different thicknesses and high durability | |
| CN102162073A (en) | Preparation method of low-carbon low-silicon cold-rolled hot-galvanized dual-phase steel for extra-deep drawing | |
| CN101942600A (en) | Preparation method of transformation-induced plasticity (TRIP) medium-manganese hot-rolled steel sheet | |
| CN104073744B (en) | The high tenacity X80 pipe line steel coiled sheet of thickness >=18.5mm and production method | |
| CN104018092B (en) | A kind of 750MPa grade high-strength steel plate, purposes and its manufacture method | |
| CN105256231A (en) | Cold-rolled steel plate for condenser pipe and preparation method for cold-rolled steel plate |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20160727 |
|
| RJ01 | Rejection of invention patent application after publication |