CN102660671A - Heat treatment method for 55Si2Mn alloy steel - Google Patents
Heat treatment method for 55Si2Mn alloy steel Download PDFInfo
- Publication number
- CN102660671A CN102660671A CN2012101880048A CN201210188004A CN102660671A CN 102660671 A CN102660671 A CN 102660671A CN 2012101880048 A CN2012101880048 A CN 2012101880048A CN 201210188004 A CN201210188004 A CN 201210188004A CN 102660671 A CN102660671 A CN 102660671A
- Authority
- CN
- China
- Prior art keywords
- 55si2mn
- steel
- temperature
- alloy steel
- quenching
- 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
Landscapes
- Heat Treatment Of Articles (AREA)
Abstract
The invention provides a heat treatment method for a 55Si2Mn alloy steel. The method comprises the following steps of: 1) heating a 55Si2Mn alloy steel part to the temperature of 850-860 DEG C for austenitizing treatment, wherein the heat insulation time is 8-9.5 minutes; 2) carrying out isothermal quenching in a martensite transformation temperature interval of the 55Si2Mn alloy steel, wherein the quenching temperature is 210-220 DEG C and the heat insulation time is 1-1.5 minutes; 3) carrying out isothermal partition heat treatment on the 55Si2Mn alloy steel processed in the step 2 at the partition temperature of 400-420 DEG C for 6-7 minutes: and 4) quenching the steel part obtained in the step 3 to the room temperature, and carrying out the isothermal partition heat treatment to obtain a complex phase structure composed of low carbon martensite and retained austenite as well as transformation structures of low carbon martensite and retained austenite, so that the processed 55Si2Mn alloy steel presents well coordination of high strength and high plasticity, the stress corrosion resistance is improved and the hydrogen embrittlement sensitivity is reduced.
Description
Technical field
The present invention relates to a kind of heat treating method of 55Si2Mn steel alloy.
Background technology
The 55Si2Mn alloy spring steel is widely used silicon-manganese spring steel, and intensity, elasticity and hardening capacity are high slightly than 55Si2Mn.It is alloy spring steel that the 55Si2Mn steel belongs to silicomanganese, be on the basis of high-quality medium carbon steel, improve silicon, manganese content forms.The effect of silicon is hardness, intensity, yield tensile ratio and the fatigue property that improves steel, increases the temper resistance of steel simultaneously.The effect of manganese is to improve the hardening capacity and the wear resistance of steel.Owing to have good comprehensive mechanical properties and cheap price, the 55Si2Mn steel has obtained using widely, and the application percentage in China's spring steel is produced is near 60%.The 55Si2Mn alloy spring steel is suitable for making in rail truck, the automobile and tractor industry and bears bigger load.The flat spring of 55Si2Mn spring steel or line footpath the whisker below the 30mm, leaf spring also be suitable for making working temperature in non-corrosive medium below 250 ℃ heat-resisting spring and bear stress alternation and at the heavily stressed large-scale important spring that rolls of work down.Concrete commonly used vibration damping leaf spring and whisker, the cylinder relief valve spring of doing on automobile, tractor and the locomotive also can be used as the heat-resisting spring that uses below 250 ℃.
The Chemical Composition of conventional 55Si2Mn alloy spring steel is: carbon C: 0.52～0.6; Silicon Si:1.50～2.00; Manganese Mn:0.60～0.90; Sulphur S :≤0.035; Phosphorus P :≤0.035; Chromium Cr :≤0.35; Nickel :≤0.35; Copper Cu :≤0.25.Existing heat treatment mode is: quench hot+low-temperaturetempering.Conventional crystalline phase is organized as tempering troostite.55Si2Mn steel alloy silicon and manganese improve elastic strength and yield tensile ratio, improve hardening capacity, anti-temper resistance and anti-relaxation stability, and superheated susceptivity is also less, but decarburizing tendency is bigger, and when especially silicon and carbon content were higher, carbon was easy to greying, and steel is become fragile.And traditional thermal treatment process can not be taken into account the requirement of HS and good plasticity and toughness: if it is lower to reduce tempering temperature, and then relatively poor, the easy generation low stress brittle fracture of plasticity; Can improve plasticity if improve tempering temperature, but intensity declines to a great extent.Therefore; Though traditional heat treating regime can guarantee such alloy and can satisfy the service condition of common environment for use; But shortcomings such as plasticity, toughness is not good enough or obdurability coupling not enough, hydrogen embrittlement and Sensitivity of Stress Corrosion are big have but limited the performance of such steel alloy obdurability potentiality.The fast development of automobile lightweight especially in recent years and high performance, an urgent demand improves the stress of spring steel.
Summary of the invention
The present invention is the insufficient problem of plasticity and toughness when satisfying intensity that will solve existing 55Si2Mn, and a kind of heat treating method of 55Si2Mn steel alloy is provided.
The heat treating method of 55Si2Mn steel alloy of the present invention is realized through following steps:
1) the 55Si2Mn steel part is heated to 850-860 ℃, carries out austenitizing and handle, soaking time is 8-9.5 minute;
2) in the martensite transformation temperature interval of 55Si2Mn steel, carry out isothermal quenching then, quenching temperature is 210-220 ℃, and soaking time is 1-1.5 minute;
3) will be under the partition temperature of 55Si2Mn steel after step 2 is handled at 400-420 ℃ isothermal partition thermal treatment 6-7 minute;
4) steel part that step 3 is obtained is quenched to room temperature.
Method of the present invention is through a large amount of experiments; After the 55Si2Mn steel alloy is handled through the heat treating method of concrete steps of the present invention and parameter; Can obtain partial martensite and residual austenite through isothermal quenching; Pass through the thermal treatment of isothermal partition subsequently with the heterogeneous structure of acquisition, thereby make the 55Si2Mn steel alloy after handling present the good combination of HS and high-ductility, and improved stress corrosion resistance, reduction hydrogen embrittlement susceptibility by low carbon martensite and residual austenite and transformation organizational composition thereof; Thereby having the high-intensity higher plasticity that has simultaneously, to satisfy the needs of special occasions.
Embodiment
Technical scheme of the present invention is not limited to following cited embodiment, also comprises the arbitrary combination between each embodiment.
Embodiment 1:
1) the 55Si2Mn steel part is heated to 850 ℃, carries out austenitizing and handle, soaking time is 8 minutes;
2) in the martensite transformation temperature interval of 55Si2Mn steel, carry out isothermal quenching then, quenching temperature is 210 ℃, and soaking time is 1 minute;
3) will be under the partition temperature of 55Si2Mn steel after step 2 is handled at 400 ℃ 6 minutes s of isothermal partition thermal treatment;
4) steel part that step 3 is obtained is quenched to room temperature.
Embodiment 2:
1) the 55Si2Mn steel part is heated to 855 ℃, carries out austenitizing and handle, soaking time is 9 minutes;
2) in the martensite transformation temperature interval of 55Si2Mn steel, carry out isothermal quenching then, quenching temperature is 215 ℃, and soaking time is 1 minute;
3) will be under the partition temperature of 55Si2Mn steel after step 2 is handled at 410 ℃ 6 minutes s of isothermal partition thermal treatment;
4) steel part that step 3 is obtained is quenched to room temperature.
Embodiment 3:
1) the 55Si2Mn steel part is heated to 860 ℃, carries out austenitizing and handle, soaking time is 9.5 minutes;
2) in the martensite transformation temperature interval of 55Si2Mn steel, carry out isothermal quenching then, quenching temperature is 220 ℃, and soaking time is 1.5 minutes;
3) will be under the partition temperature of 55Si2Mn steel after step 2 is handled at 420 ℃ 7 minutes s of isothermal partition thermal treatment;
4) steel part that step 3 is obtained is quenched to room temperature.
After the heat treating method of the 55Si2Mn of this embodiment steel alloy is handled; The tensile strength of 55Si2Mn steel alloy reaches 1750MPa～2100MPa; Ys reaches 1550MPa～1900MPa, and unit elongation is 6%～9%, and reduction of area is 28%～43%; Obtain to meet the comprehensive mechanical property index request that the different superstrengths of actual service condition match with good plasticity and toughness, and significantly improved hydrogen embrittlement and Sensitivity of Stress Corrosion.
Claims (2)
1. the heat treating method of a 55Si2Mn steel alloy is characterized in that: adopt following steps
1) the 55Si2Mn steel part is heated to 850-860 ℃, carries out austenitizing and handle, soaking time is 8-9.5 minute;
2) in the martensite transformation temperature interval of 55Si2Mn steel, carry out isothermal quenching then, quenching temperature is 210-220 ℃, and soaking time is 1-1.5 minute;
3) will be under the partition temperature of 55Si2Mn steel after step 2 is handled at 400-420 ℃ isothermal partition thermal treatment 6-7 minute;
4) steel part that step 3 is obtained is quenched to room temperature.
2. the heat treating method of 55Si2Mn steel alloy according to claim 1 is characterized in that:
1) the 55Si2Mn steel part is heated to 855 ℃, carries out austenitizing and handle, soaking time is 9 minutes;
2) in the martensite transformation temperature interval of 55Si2Mn steel, carry out isothermal quenching then, quenching temperature is 215 ℃, and soaking time is 1 minute;
3) will be under the partition temperature of 55Si2Mn steel after step 2 is handled at 410 ℃ 6 minutes s of isothermal partition thermal treatment;
4) steel part that step 3 is obtained is quenched to room temperature.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2012101880048A CN102660671A (en) | 2012-06-08 | 2012-06-08 | Heat treatment method for 55Si2Mn alloy steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2012101880048A CN102660671A (en) | 2012-06-08 | 2012-06-08 | Heat treatment method for 55Si2Mn alloy steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN102660671A true CN102660671A (en) | 2012-09-12 |
Family
ID=46770246
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2012101880048A Pending CN102660671A (en) | 2012-06-08 | 2012-06-08 | Heat treatment method for 55Si2Mn alloy steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102660671A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103276164A (en) * | 2013-05-15 | 2013-09-04 | 哈尔滨工业大学 | High-strength and high-toughness heat treatment method of medium-carbon silicon-manganese-chromium-nickel series low alloy steel |
| CN110791618A (en) * | 2019-11-11 | 2020-02-14 | 常熟非凡新材股份有限公司 | Method for processing lining plate of ball mill |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03215623A (en) * | 1990-01-19 | 1991-09-20 | Nisshin Steel Co Ltd | Production of tough high strength steel |
| GB2361012A (en) * | 1998-12-19 | 2001-10-10 | Exxonmobil Upstream Res Co | Ultra-high strength ausaged steels with excellent cryogenic temperature toughness |
| CN101121955A (en) * | 2007-09-13 | 2008-02-13 | 上海交通大学 | Heat treatment method for increasing quenched steel component mechanical property by using carbon distribution and tempering |
| CN101134995A (en) * | 2007-10-16 | 2008-03-05 | 长安汽车（集团）有限责任公司 | Alloy spring steel ultra-fine martensite heat treatment quenching strengthening process |
| CN101225499A (en) * | 2008-01-31 | 2008-07-23 | 上海交通大学 | Low-alloy super-strength multiphase steel and heat treatment method thereof |
| CN101597680A (en) * | 2009-07-09 | 2009-12-09 | 贵州大学 | Train 60Si2CrVA steel spring goods quenching-distribution thermal treatment process |
| CN102433514A (en) * | 2011-11-29 | 2012-05-02 | 宁波精磊汽车零部件有限公司 | Low-alloy steel and preparation method thereof |
-
2012
- 2012-06-08 CN CN2012101880048A patent/CN102660671A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03215623A (en) * | 1990-01-19 | 1991-09-20 | Nisshin Steel Co Ltd | Production of tough high strength steel |
| GB2361012A (en) * | 1998-12-19 | 2001-10-10 | Exxonmobil Upstream Res Co | Ultra-high strength ausaged steels with excellent cryogenic temperature toughness |
| CN101121955A (en) * | 2007-09-13 | 2008-02-13 | 上海交通大学 | Heat treatment method for increasing quenched steel component mechanical property by using carbon distribution and tempering |
| CN101134995A (en) * | 2007-10-16 | 2008-03-05 | 长安汽车（集团）有限责任公司 | Alloy spring steel ultra-fine martensite heat treatment quenching strengthening process |
| CN101225499A (en) * | 2008-01-31 | 2008-07-23 | 上海交通大学 | Low-alloy super-strength multiphase steel and heat treatment method thereof |
| CN101597680A (en) * | 2009-07-09 | 2009-12-09 | 贵州大学 | Train 60Si2CrVA steel spring goods quenching-distribution thermal treatment process |
| CN102433514A (en) * | 2011-11-29 | 2012-05-02 | 宁波精磊汽车零部件有限公司 | Low-alloy steel and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| S.S.NAYAK,ET AL,: "Microstructure-hardness relationship in quenched and partitioned medium-carbon and high-carbon steels containing silicon", 《MATERIALS SCIENCE AND ENGINEERING A》 * |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103276164A (en) * | 2013-05-15 | 2013-09-04 | 哈尔滨工业大学 | High-strength and high-toughness heat treatment method of medium-carbon silicon-manganese-chromium-nickel series low alloy steel |
| CN103276164B (en) * | 2013-05-15 | 2014-12-31 | 哈尔滨工业大学 | High-strength and high-toughness heat treatment method of medium-carbon silicon-manganese-chromium-nickel series low alloy steel |
| CN110791618A (en) * | 2019-11-11 | 2020-02-14 | 常熟非凡新材股份有限公司 | Method for processing lining plate of ball mill |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103031498B (en) | Manufacture method of extremely thick ocean engineering steel plate with low compression ratio and super high-strength strain age | |
| CN102534132A (en) | Quenching-partitioning thermal treatment method for high strength and toughness of medium carbon silicon-manganese low alloy steel | |
| CN102758140B (en) | High-carbon microalloying steel ball and production process thereof | |
| CN103243275A (en) | Preparation method of bainite/martensite/austenite composite high-strength steel | |
| CN101660036B (en) | Heat treating method of high strength and high ductility steel tube | |
| CN102605378A (en) | Carburizing and quenching method | |
| CN104805258A (en) | 42CrMo steel fast spheroidizing annealing method | |
| CN102433514A (en) | Low-alloy steel and preparation method thereof | |
| CN102286690A (en) | Pipeline steel plate capable of resisting hydrogen-induced cracking and production method thereof | |
| CN101597682A (en) | Process for ultrafining heat-treatment on crystal grains of axle steel | |
| CN102719752A (en) | Seamless steel pipe with excellent hydrogen sulfide stress corrosion resistance and manufacturing method thereof | |
| CN108774681A (en) | The supper-fast heat treatment method of high-strength steel | |
| CN104745952A (en) | Pressure vessel steel, manufacturing method thereof and manufacturing method of deep drawing article | |
| CN103740912A (en) | Processing method for improving temper embrittlement resistance of steel plate for pressure vessels | |
| CN103014546A (en) | Alloy steel | |
| CN102953013A (en) | Preparation technology of die steel for hot-forging die and die-casting die | |
| CN102660671A (en) | Heat treatment method for 55Si2Mn alloy steel | |
| CN102703670B (en) | Method for processing 55Si2Mn alloy spring | |
| CN102534419A (en) | Super-martensitic stainless steel and preparation method thereof | |
| CN102115806A (en) | Heat treatment process for improving low temperature toughness of super-thick plates | |
| CN102212751A (en) | Steel for high-strength petroleum casing pipe used in heavy oil thermal recovery well and manufacturing method thereof | |
| CN102676934A (en) | Preparation method of 55Si2Mn alloy steel | |
| CN111471838A (en) | High-strength and high-toughness spring steel and heat treatment process thereof | |
| CN101624684B (en) | Carburizing bainite steel and manufacturing method thereof | |
| CN105132815A (en) | Cold forging steel for high-strength large-dimension bolt and production 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 | ||
| C12 | Rejection of a patent application after its publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20120912 |