CN106636590B - A kind of medium carbon steel thermo-mechanical processi method of alternative modifier treatment - Google Patents
A kind of medium carbon steel thermo-mechanical processi method of alternative modifier treatment Download PDFInfo
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- CN106636590B CN106636590B CN201611094718.7A CN201611094718A CN106636590B CN 106636590 B CN106636590 B CN 106636590B CN 201611094718 A CN201611094718 A CN 201611094718A CN 106636590 B CN106636590 B CN 106636590B
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- carbon steel
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- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
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- Crystallography & Structural Chemistry (AREA)
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- Heat Treatment Of Steel (AREA)
Abstract
A kind of medium carbon steel thermo-mechanical processi method of alternative modifier treatment, it is mainly：Medium carbon steel pole is heated to α+γ two-phase sections insulation a period of time, comes out of the stove and carries out the groove rolling of 9 passages, cumulative deformation 70%.5min is carried out after the completion of every 3 passes and melts down heating process, room temperature is air-cooled to after the 9th passes.Rolling rod iron microscopic structure is formed and formd stronger by the ferrite matrix and particle globular cementite of threadiness<101>Fiber texture degree.The comprehensive mechanical property of medium carbon steel bar prepared by the present invention can not only reach the performance level of traditional hardening and tempering process processing medium carbon steel, and present invention process is simple, production efficiency is high, quenching and tempering cooling medium are avoided to pollution caused by environment, it is not related to workpiece deformation caused by quenching stress, internal tiny crack germinating and cracking, Product Process performance and mechanical property are not influenceed by quenching degree and temper brittleness etc., for great section workpiece, without from steel alloy, substantially reducing material cost.
Description
Technical field
The present invention relates to a kind of processing method of ferrous materials.
Background technology
The prior heat treatment of medium carbon steel is modifier treatment, that is, high tempering after quenching, obtains tempered sorbite tissue, the group
Knit and be made up of ferrite matrix and equally distributed spheroidite particle, so as to ensure to obtain good intensity, plasticity and tough
The cooperation of property, that is, obtain good comprehensive mechanical property.This traditional handicraft is mainly used in manufacture axle, pin, gear and connecting rod
Deng component of machine.Modifier treatment technique is related to quenching and high tempering, following deficiency be present：(1) quenching and high tempering need
Want long-time heating and insulation, consume the substantial amounts of energy, low production efficiency, and quench and tempering used in cooling medium have to environment
Certain pollution.(2) in order to ensure that larger cross-section dimension workpiece obtains uniform tempered sorbite tissue, it is necessary to using having height
The addition price of quenching degree compared with high alloy element steel alloy, come meet the through hardening layer depth of great section workpiece requirement, material into
This height；For some steel alloys, temper brittleness sensitiveness also be present, it has to add Alloy Elements Mo costly.(3)
Quenching process causes larger quenching stress with Volumetric expansion caused by quick martensite transfor mation, exist workpiece deformation,
Internal tiny crack germinates and tearing tendency.
The content of the invention
Metallographic but also energy-conservation, the alternative tune of efficiency high inside medium carbon steel had not only been can guarantee that it is an object of the invention to provide a kind of
The medium carbon steel thermo-mechanical processi method of matter processing.The technology path of the method for the invention is：By middle carbon quenched and tempered steel be heated to α+
γ two-phase section, multi- pass rolling deformation is carried out after insulation, is then air-cooled to room temperature, obtain the ferrite with fibrous feature+
Spheroidite tissue.
The technical solution adopted by the present invention is specific as follows：
(1) medium carbon steel bar is heated to α+γ two-phase section temperature, 720~820 DEG C of temperature range, insulation in heating furnace
40min, it is set to obtain ferrite+austenitic duplex tissue；
(2) take out rod iron and carry out 9 passage groove rollings immediately, total accumulative deformation amount controlling is rolled not less than 70%
Heating furnace is put back to during system after every 3 passage and reheats 5min, then carries out next 3 passes, it is empty after the 9th passes
It is as cold as room temperature.Because dynamic recrystallization occurs for ferrite at the initial stage of rolling, austenite, which is elongated, becomes threadiness, and makes crystal boundary and position
Mistake increases.The operation of rolling with bar cooling, when temperature is reduced to Ar1When, dynamic perlitic transformation occurs for austenite, simultaneously
The carbide of sheet can crush under rolling stress and effects of strain.In order to prevent operation of rolling temperature drop from excessively causing rolling
Drag quickly increases, and takes to roll rod after every 3 passage and put back in open rolling heating furnace being incubated 5min, now due to crystal boundary and dislocation pair
The facilitation of carbon atom diffusion, makes cementite that fast spheroidizing annealing occur, while partial austenitic transition process can also occur, so
Ensure to complete the follow-up operation of rolling under conditions of rolling drag does not significantly increase.Air cooling obtains to room temperature after 9th passes
The bacillar structure formed to ferrite and granular carbide, and have stronger<101>Fiber texture degree, make substantial amounts of ferrite
{ 001 } cleavage surface parallel to rolling direction, this is not only improved carries perpendicular to the cracked deviation of rolling direction impact fracture
High impact toughness, it is also beneficial to improve intensity and plasticity.
The physical metallurgy principle of the method for the invention is：Medium carbon steel deforms in the initial passes of two-phase section, makes iron
Dynamic recrystallization refinement occurs for ferritic, and austenite deformation makes crystal grain elongate generation fibrosis along rolling direction, causes austenite crystal
Boundary's quantity and dislocation density increase.In the operation of rolling, reduced with blank temperature, austenite can be transformed into the group of pearlite type
Knit, because number of grain boundaries and dislocation density are higher in deformed austenite, refine the cemetite lamellae in pearlite, and spacing subtracts
It is small.During through melting down heating in short-term, then carry out rolling deformation, cause cemetite lamellae fragmentation, promote cementite nodularization, while these ooze
Carbon body also suppresses ferritic crystal grain and grown up.So, when being cooled to room temperature, the fining ferrite of fibrosis can be obtained and spherical oozed
Carbon body tissue.
It is of the invention to be had the following advantages that compared with traditional modifier treatment：
1st, can be obtained using this method in medium carbon steel and its modifier treatment identical tissue, i.e. ferrite and spherical carburizing
Body tissue, and its tensile strength, yield strength, elongation percentage and impact flexibility are above the quenched place of GB/T 699-1999 medium carbon steel
Manage set quota.
2nd, preparation technology is simple, and production efficiency is high.
3rd, it is not related to quenching and tempering heat treatment process, avoids cooling medium to pollution caused by environment, be not related to and quench
Workpiece deformation, internal tiny crack germinating and cracking caused by fiery stress, Product Process performance and mechanical property not by quenching degree and
Temper brittleness etc. influences.
4th, for great section workpiece, without from steel alloy, the medium carbon steel handled using the present invention is entirely capable of meeting to require,
Substantially reduce material cost.
Table 1 lists to be contrasted with the method for the invention and the medium carbon steel mechanical property of GB/T 699-1999 modifier treatment：
Table 1
Brief description of the drawings
Fig. 1 is the stereoscan photograph figure of the bar microscopic structure prepared by the embodiment of the present invention 1.
Fig. 2 is the stereoscan photograph figure of the bar microscopic structure prepared by the embodiment of the present invention 2.
Fig. 3 is the stereoscan photograph figure of the bar microscopic structure prepared by the embodiment of the present invention 3.
Fig. 4 is the stereoscan photograph figure of the bar microscopic structure prepared by the embodiment of the present invention 4.
Fig. 5 is the stereoscan photograph figure of the bar microscopic structure prepared by the embodiment of the present invention 5.
Fig. 6 is the stereoscan photograph figure of the bar microscopic structure prepared by the embodiment of the present invention 6.
Fig. 7 is the stereoscan photograph figure of the bar microscopic structure prepared by the embodiment of the present invention 7.
Embodiment
Technique of the present invention will be further illustrated according to specific embodiment and Figure of description below.
Embodiment 1
The a diameter of 30mm steel pole of commercialization 45 is heated to 720 DEG C, is incubated 40min, coming out of the stove carries out accumulative deflection and be
70% 9 passage groove rollings (side-water chestnut-side), obtain the bar of square-section.Wherein the 9th passage is trimming, the 8th
Rod iron is turned 90 ° after secondary rolling and enters the 8th hole rolling again.3rd, after the 6th passes, rod iron is put back in 720 DEG C of stove respectively
Insulation 5 minutes.9th passes terminate rear Direct Air-Cooled.
Embodiment 2~6
Carried out according to the scheme of embodiment 1, the difference with embodiment 1 is heating-up temperature being changed into 740,760 from 720 DEG C
DEG C, 780 DEG C, 800 DEG C and 820 DEG C, and the 3rd, the 6th passes terminate rear rod iron and melt down the temperature of heating correspondingly also by 720
DEG C it is changed into 740 DEG C, 760 DEG C, 780 DEG C, 800 DEG C and 820 DEG C.
Embodiment 7
Carried out according to the scheme of embodiment 3, the difference with embodiment 3 is steel used being changed to 35 steel.
Table 2 lists the mechanical property of the bar prepared by embodiment 1~7.
Table 2
Claims (2)
1. a kind of medium carbon steel thermo-mechanical processi method of alternative modifier treatment, it is characterised in that：
(1) medium carbon steel bar is heated to α+γ two-phase section temperature, 720~820 DEG C of temperature range, insulation in heating furnace
40min, it is set to obtain ferrite+austenitic duplex tissue；
(2) take out rod iron and carry out 9 passage groove rollings immediately, total accumulative deformation amount controlling was rolled not less than 70%
Heating furnace is put back in journey after every 3 passage and reheats 5min, then carries out next 3 passes, air cooling arrives after the 9th passes
Room temperature.
2. the medium carbon steel thermo-mechanical processi method of alternative modifier treatment according to claim 1, it is characterised in that：Gained
To the bacillar structure that is made up of ferrite and granular carbide of medium carbon steel, and with stronger<101>Fiber texture degree.
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| CN109355549B (en) * | 2018-12-11 | 2020-10-02 | 东北大学 | Steel plate with high strength and excellent low-temperature toughness and manufacturing method thereof |
| CN111485083B (en) * | 2019-01-25 | 2021-09-10 | 南京理工大学 | Preparation method of ultrahigh-strength nano heterogeneous low-carbon steel |
| CN110055379A (en) * | 2019-06-03 | 2019-07-26 | 郑州航空工业管理学院 | A kind of preparation method of micro- multi-layer sheet structure steel plate |
| CN113430359B (en) * | 2021-05-19 | 2022-09-20 | 西北工业大学 | High-strength and high-toughness rolling method for large-size gun steel bar |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1265711A (en) * | 1997-07-28 | 2000-09-06 | 埃克森美孚上游研究公司 | Ultra-high strength, weldable, essentially boron-free steels with superior toughness |
| CN101041881A (en) * | 2007-04-24 | 2007-09-26 | 西安交通大学 | Granule carbonide reinforced ferritic steel and preparation method thereof |
| 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 |
| CN102417959A (en) * | 2011-12-12 | 2012-04-18 | 河北联合大学 | Method for producing annealing-free hot rolling S50C plate and strip |
| CN102712980A (en) * | 2010-01-26 | 2012-10-03 | 新日本制铁株式会社 | High-strength cold-rolled steel sheet, and process for production thereof |
| CN103173598A (en) * | 2013-03-11 | 2013-06-26 | 河北钢铁股份有限公司唐山分公司 | Annealing-free medium-high carbon steel plate making technology |
| CN106077085A (en) * | 2016-07-29 | 2016-11-09 | 中冶赛迪工程技术股份有限公司 | The production system of a kind of low yield strength ratio hot-rolled high-strength anti-seismic steel bar and method |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2006068399A1 (en) * | 2004-12-21 | 2006-06-29 | Posco Co., Ltd. | Non-oriented electrical steel sheets with excellent magnetic properties and method for manufacturing the same |
-
2016
- 2016-12-02 CN CN201611094718.7A patent/CN106636590B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1265711A (en) * | 1997-07-28 | 2000-09-06 | 埃克森美孚上游研究公司 | Ultra-high strength, weldable, essentially boron-free steels with superior toughness |
| CN101041881A (en) * | 2007-04-24 | 2007-09-26 | 西安交通大学 | Granule carbonide reinforced ferritic steel and preparation method thereof |
| 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 |
| CN102712980A (en) * | 2010-01-26 | 2012-10-03 | 新日本制铁株式会社 | High-strength cold-rolled steel sheet, and process for production thereof |
| CN102417959A (en) * | 2011-12-12 | 2012-04-18 | 河北联合大学 | Method for producing annealing-free hot rolling S50C plate and strip |
| CN103173598A (en) * | 2013-03-11 | 2013-06-26 | 河北钢铁股份有限公司唐山分公司 | Annealing-free medium-high carbon steel plate making technology |
| CN106077085A (en) * | 2016-07-29 | 2016-11-09 | 中冶赛迪工程技术股份有限公司 | The production system of a kind of low yield strength ratio hot-rolled high-strength anti-seismic steel bar and method |
Non-Patent Citations (1)
| Title |
|---|
| Q235碳素钢应变强化相变的基本特点及影响因素;杨平 等;《金属学报》;20010630;第592-600页 * |
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