CN113957209A - High-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process - Google Patents
High-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process Download PDFInfo
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- CN113957209A CN113957209A CN202111042763.9A CN202111042763A CN113957209A CN 113957209 A CN113957209 A CN 113957209A CN 202111042763 A CN202111042763 A CN 202111042763A CN 113957209 A CN113957209 A CN 113957209A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 51
- 239000010959 steel Substances 0.000 title claims abstract description 51
- 238000000137 annealing Methods 0.000 title claims abstract description 38
- 238000000034 method Methods 0.000 title claims abstract description 37
- 230000008569 process Effects 0.000 title claims abstract description 28
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 26
- 229910052804 chromium Inorganic materials 0.000 title claims abstract description 26
- 239000011651 chromium Substances 0.000 title claims abstract description 26
- 238000010438 heat treatment Methods 0.000 claims abstract description 35
- 238000001816 cooling Methods 0.000 claims abstract description 29
- 238000007599 discharging Methods 0.000 claims abstract description 6
- 229910001566 austenite Inorganic materials 0.000 claims description 6
- 229910001562 pearlite Inorganic materials 0.000 claims description 5
- 239000007788 liquid Substances 0.000 claims 1
- 230000001131 transforming effect Effects 0.000 claims 1
- 229910001567 cementite Inorganic materials 0.000 abstract description 8
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 abstract description 8
- 230000015572 biosynthetic process Effects 0.000 abstract description 2
- 239000013078 crystal Substances 0.000 abstract description 2
- 239000000463 material Substances 0.000 abstract description 2
- 238000005096 rolling process Methods 0.000 description 12
- 238000004519 manufacturing process Methods 0.000 description 8
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 239000002245 particle Substances 0.000 description 5
- 230000009467 reduction Effects 0.000 description 5
- 230000008859 change Effects 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000007123 defense Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 230000007847 structural defect Effects 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
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Classifications
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
-
- 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
- C21D1/04—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering with simultaneous application of supersonic waves, magnetic or electric fields
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
-
- 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
- C21D2201/00—Treatment for obtaining particular effects
Abstract
The invention provides a high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process, which comprises the steps of placing the high-carbon chromium bearing steel in a high-intensity magnetic field heat treatment device, starting to apply a stable high-intensity magnetic field with the intensity of 8-12T, and heating the high-carbon chromium bearing steel to Ac under the magnetic field1Austenitizing at 20-50 deg.C; then cooling to Ar1Carrying out isothermal spheroidization at the temperature of minus 10-30 ℃; and reducing the temperature of the magnetic field after isothermal treatment, and discharging from the furnace and air cooling when the magnetic field is zero. The time consumed by the high-intensity magnetic field rapid spheroidizing annealing process is 5-8 h, only the time of the traditional spheroidizing annealing process is below 50%, the spheroidizing annealing time is greatly shortened, the treated tissue basically eliminates reticular cementite, the content of the pro-eutectoid cementite can be reduced, the formation of coarse carbide of a crystal boundary is avoided, and the spheroidized tissue is carbonizedThe uniformity of the material is better, the spheroidized structure is more excellent, and the structure and the mechanical property are both suitable for subsequent processing and forming of bearing parts.
Description
Technical Field
The invention relates to the technical field of bearing steel heat treatment, in particular to a high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process.
Background
The bearing is an important mechanical basic part, determines the precision, performance and reliability of equipment to a great extent, and plays an extremely important role in the fields of national economy and national defense. The bearing steel is one of the steel types with the strictest quality requirement, the most inspection projects and the largest production difficulty in all alloy steels, and the world recognizes that the production level of the bearing steel is a national metallurgical level mark.
The bearing steel is divided into the following parts according to characteristics and application environments: high-carbon chromium bearing steel (namely full-quenched bearing steel), carburized bearing steel (namely surface-hardened bearing steel), high-temperature bearing steel and stainless bearing steel. The high-carbon chromium bearing steel has high fatigue resistance, high extensibility, good wear resistance, proper elasticity and toughness, certain antirust capacity and good cold and hot processability. The heat treatment method is simple, the content of alloy elements is not high, the price is low, and the like, and the high-carbon chromium bearing steel is widely applied internationally, and accounts for more than 90 percent of the yield of all bearing steel.
The carbides are important composition phases of the bearing steel, and the finer, more uniform and more rounded carbides contribute more to the improvement of the bearing life. The heat treatment of the bearing steel comprises two links, wherein the pretreatment is spheroidizing annealing, and the final treatment is quenching. The steel spheroidizing annealing of the bearing aims to obtain a structure with fine, small, uniform and round carbide particles uniformly distributed on a ferrite matrix, reduce the hardness to facilitate cutting processing and prepare the structure for final heat treatment. The size and distribution of the carbide particles in the final quenched and tempered structure of the bearing depends to a large extent on the size and distribution of the carbide particles after spheroidizing annealing. Therefore, designing a proper spheroidizing heat treatment process to obtain an ideal spheroidized structure is one of the key technologies for improving the fatigue life of the bearing.
The traditional spheroidizing annealing process needs a long annealing time (10-16 h), and the annealed carbide particles are not uniform, so that the subsequent cold processing and the final quenching and tempering structure and performance are influenced.
The existing patented technology in the aspect of bearing spheroidizing annealing is basically multi-process, the production process is complex, the production period is long, and the energy consumption is high.
For example, patent CN2012100753172 discloses a heat treatment process method for shortening the spheroidizing annealing heat treatment time of GCr15 bearing steel and improving the spheroidization rate and distribution uniformity of carbide, the process comprises the steps of firstly, rapidly induction heating rolled GCr15 bearing steel to 700-720 ℃ at the speed of 5-15 ℃/s, preserving heat for 5-10 min, and then air cooling to room temperature; heating the cooled GCr15 bearing steel to 780 ℃, and preserving heat for 40 min; then slowly cooling to 700 ℃ at the speed of 20 ℃/h, discharging and air cooling. The patent comprises the process of heating twice and then cooling to room temperature, and the production process is complex, the energy consumption is high, and the time consumption is more than 10 hours.
The patent CN201410538252X discloses an on-line rapid spheroidizing annealing process of a GCr15 high-carbon chromium bearing steel hot-rolled rod wire, which heats a sample to be rolled to 1150-1250 ℃, and keeps the temperature constant for 60-120 min; rolling at 920-960 ℃, wherein the rolling reduction is 40% -60%; then cooling to 740-780 ℃ for further rolling, wherein the rolling reduction is 30% -50%; slowly cooling the rolled steel plate to 500-600 ℃ at the speed of 0.3-0.5 ℃/s; and finally, quickly cooling to room temperature. The rolling process of the patent is complex, and the requirement on a rolling mill is high; the carbide is mainly formed in the slow cooling process, and the particles are not uniform.
The patent CN201710411463 discloses an online rapid spheroidizing annealing method for GCr15 bearing steel after hot rolling, and the process heats a sample to be rolled to 1000-1200 ℃, and isothermally heats the sample for 30-60 min; rolling at 950-1000 ℃ with the reduction of 20-30%; the finishing temperature is 760-800 ℃, and the reduction is 10-25%; carrying out isothermal treatment on the rolled steel plate at 720-750 ℃ for 3-5 h; after isothermal treatment, the furnace is cooled to 600 +/-20 ℃ and air cooled. The rolling temperature of the patent is low, the deformation resistance is high, the requirement on the strength of a rolling mill is high, and the service life of the rolling mill is influenced; and the spheroidizing annealing time is longer, the total time is 6-10 h, and the production efficiency is low.
The patent CN2018103183017 discloses a rapid spheroidizing annealing process method of GCr15 bearing steel, which comprises the steps of heating a hot-rolled GCr15 sample to 1000-1200 ℃, carrying out isothermal treatment for 60-100 min, and then cooling to room temperature along with a furnace; then heating the initially annealed sample to 800-850 ℃, and carrying out isothermal treatment for 30-60 min; rolling at 800-850 ℃ with the rolling reduction of 10-30%; then carrying out isothermal treatment at 800-850 ℃ for 30-60 min; cooling the isothermal sample to 720-750 ℃ in a furnace, and further carrying out isothermal treatment for 30-120 min; cooling to 550-650 ℃ along with the furnace; and finally, air cooling to room temperature. The patent comprises the process of heating twice and then cooling to room temperature, the production process is complex, and the total time of spheroidizing annealing exceeds 10 hours.
The patent CN201810665068X discloses an on-line critical spheroidizing annealing method of GCr15 bearing steel, which comprises the steps of immediately cooling a steel bar subjected to hot rolling to 550-650 ℃ at the speed of 10-25 ℃/s, then heating to 790-800 ℃ at the speed of 5-20 ℃/min, carrying out heat preservation for 1-3 h, then carrying out furnace cooling to 710-730 ℃ at the speed of 1-3 ℃/min, carrying out isothermal treatment, carrying out furnace cooling to 650-680 ℃ at the speed of 0.5-2.5 ℃/min after carrying out isothermal treatment for 120min, and finally carrying out air cooling to room temperature. The patent water-cools to 550-650 ℃, and the formed pearlite lamellar spacing is larger, and meanwhile, coarse grain boundary cementite is easily formed in the subsequent heating process, so that the temperature needs to be kept for a longer time at 790-800 ℃ to dissolve the large-size cementite phase.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides a high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process, which ensures that proper content of undissolved spherical carbide is reserved on an austenite matrix by reasonably selecting austenitizing temperature and dissimilarity eutectoid phase transformation temperature, and provides more nucleation positions for the precipitation and growth of cementite in the dissimilarity eutectoid phase transformation process. Meanwhile, the content of the proeutectoid cementite is reduced through a strong magnetic field, and the heterotactic eutectoid phase change is accelerated, so that the time required by spheroidizing annealing is effectively shortened, the energy efficiency is improved, and the spheroidizing annealing structure is optimized.
The technical scheme of the invention is as follows: a high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process comprises the following steps:
placing the high-carbon chromium bearing steel in a high-intensity magnetic field heat treatment device, starting to apply a stable high-intensity magnetic field with the strength of 8-12T, and firstly heating the high-carbon chromium bearing steel to Ac under the magnetic field1Austenitizing at 20-50 deg.C, wherein Ac1The temperature at which pearlite transforms to austenite when heated;
then cooling to Ar1Carrying out isothermal treatment at 10-30 ℃, cooling the magnetic field simultaneously after isothermal treatment, discharging the furnace and air cooling when the magnetic field is zero, wherein Ar1The temperature at which pearlite transforms to austenite on cooling.
Preferably, the austenitizing time is 10 to 30 min.
Preferably, the isothermal time is 30-60 min.
Preferably, the strong magnetic field applied during the heat treatment is generated by a liquid-helium-free annular superconducting magnet.
Preferably, the heat treatment apparatus is a heat treatment furnace, and the heat treatment furnace is located at the center of the high-intensity magnetic field.
The invention has the beneficial effects that:
1. the spherical carbide is obtained through the segregation eutectoid phase change, compared with the traditional process of breaking and spheroidizing the lamellar carbide through long-time isothermal, the high-intensity magnetic field rapid spheroidizing annealing process has the advantages that the time consumed by the high-intensity magnetic field rapid spheroidizing annealing process is 5-8 hours, only the time is below 50% of the time of the traditional spheroidizing annealing process, the spheroidizing annealing time is obviously shortened, the energy is saved, and the production efficiency is improved; the treated structure basically eliminates the reticular cementite, and the structure and the mechanical property are both suitable for the subsequent processing and forming of bearing parts.
2. According to the invention, through applying the strong magnetic field, the heterotactic eutectoid phase change can be accelerated, the spheroidizing annealing time is shortened, the content of the proeutectoid cementite can be reduced, the formation of coarse carbides of a crystal boundary is avoided, the uniformity of the carbides in a spheroidized structure is better, and the spheroidized structure is more excellent;
3. the internal structure of the material treated by the method is uniform, the structural defects of banded structures and the like after the hot-rolled raw material is completely annealed are avoided, and the hardness of the treated high-carbon chromium bearing steel is between 179 and 207 percent of HBW.
Drawings
FIG. 1 is a spheroidized annealed metallographic (OM) structure diagram according to the present invention;
FIG. 2 is a Scanning Electron Microscope (SEM) texture map of spheroidizing annealing according to the present invention;
FIG. 3 is a Transmission Electron Microscope (TEM) texture map of spheroidizing annealing according to the present invention.
Detailed Description
The following further illustrates embodiments of the invention:
example 1
In the embodiment, a GCr15 high-carbon chromium bearing steel sample is placed in a high-intensity magnetic field heat treatment device, a steady-state high-intensity magnetic field with the strength of 10T is applied, GCr15 steel is firstly heated to 810 ℃ under the magnetic field for austenitizing, and the austenitizing time is 30 min; then cooling to 720 ℃ for isothermal treatment, wherein the isothermal time is 60 min; and reducing the temperature of the magnetic field after isothermal treatment, and discharging from the furnace and air cooling when the magnetic field is zero.
The GCr15 high-carbon chromium bearing steel structure after heat treatment by the heat treatment method of the embodiment is a spheroidized annealed structure in which fine, uniform and spheroidized carbides are embedded on a ferrite matrix, the grade of the spheroidized annealed structure is grade 2, the hardness is 190HBW, and the spheroidized annealed structure meets the national standard GB/T18254-2016.
Example 2
In the embodiment, a GCr15SiMo high-carbon chromium bearing steel sample is placed in a high-intensity magnetic field heat treatment device, a steady-state high-intensity magnetic field with the strength of 10T is applied, the GCr15SiMo steel is firstly heated to 800 ℃ under the magnetic field for austenitizing, and the austenitizing time is 30 min; then cooling to 700 ℃ for isothermal treatment, wherein the isothermal time is 60 min; and reducing the temperature of the magnetic field after isothermal treatment, and discharging from the furnace and air cooling when the magnetic field is zero.
The carbide in the GCr15SiMo high-carbon chromium bearing steel structure after heat treatment by the heat treatment method in the embodiment is fine, uniform and spheroidized, the grade of spheroidized annealing structure is 2, the hardness is 185HBW, and the spheroidized annealing structure meets the national standard GB/T18254-2016.
The foregoing embodiments and description have been presented only to illustrate the principles and preferred embodiments of the invention, and various changes and modifications may be made therein without departing from the spirit and scope of the invention as hereinafter claimed.
Claims (5)
1. A high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process is characterized by comprising the following steps:
placing the high-carbon chromium bearing steel in a high-intensity magnetic field heat treatment device, starting to apply a stable high-intensity magnetic field with the strength of 8-12T, and firstly heating the high-carbon chromium bearing steel to the austenite temperature Ac under the magnetic field1Austenitizing at 20-50 ℃, wherein Ac1 is the temperature at which pearlite transforms to austenite when heated;
and cooling to Ar1- (10-30) DEG C for isothermal treatment, reducing the temperature of the magnetic field simultaneously after the isothermal treatment, and discharging from the furnace for air cooling when the magnetic field is zero, wherein Ar1 is the temperature for transforming pearlite into austenite during cooling.
2. The high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process according to claim 1, characterized in that: the austenitizing time is 10-30 min.
3. The high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process according to claim 1, characterized in that: the isothermal time is 30-60 min.
4. The high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process according to claim 1, characterized in that: the strong magnetic field applied during the heat treatment is generated by a liquid helium-free annular superconducting magnet.
5. The high-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process according to claim 1, characterized in that: the heat treatment device is a heat treatment furnace, and the heat treatment furnace is positioned at the central position of the high-intensity magnetic field.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114480797A (en) * | 2022-01-27 | 2022-05-13 | 石狮市汇星机械有限公司 | Heat treatment process method for producing knitting machine cam by using GCr15 steel |
| CN114686654A (en) * | 2022-04-07 | 2022-07-01 | 内蒙古科技大学 | Bearing steel spheroidizing annealing method and system based on pulsed magnetic field |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10298641A (en) * | 1997-04-24 | 1998-11-10 | Kawasaki Steel Corp | Production of steel excellent in spheroidize-annealing treatability |
| CN1492059A (en) * | 2002-10-25 | 2004-04-28 | 东北大学 | Strong magnetic field quick complete annealing process for medium carbon low alloy structure steel |
| CN104328259A (en) * | 2014-10-13 | 2015-02-04 | 北京科技大学 | GCr15 high carbon chromium bearing steel on-line rapid spheroidizing annealing technology |
| CN109055707A (en) * | 2018-10-26 | 2018-12-21 | 苏州轴承厂股份有限公司 | The heat treatment process of high-carbon-chromium bearing steel part |
| WO2019001262A1 (en) * | 2017-06-28 | 2019-01-03 | 武汉理工大学 | Process for forming, by means of warm ring rolling, high-carbon chromium bearing steel capable of structure spheroidization |
| CN111763806A (en) * | 2020-06-23 | 2020-10-13 | 江苏龙城精锻有限公司 | Low-temperature annealing magnetic heat treatment process for low-carbon steel |
-
2021
- 2021-09-07 CN CN202111042763.9A patent/CN113957209A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10298641A (en) * | 1997-04-24 | 1998-11-10 | Kawasaki Steel Corp | Production of steel excellent in spheroidize-annealing treatability |
| CN1492059A (en) * | 2002-10-25 | 2004-04-28 | 东北大学 | Strong magnetic field quick complete annealing process for medium carbon low alloy structure steel |
| CN104328259A (en) * | 2014-10-13 | 2015-02-04 | 北京科技大学 | GCr15 high carbon chromium bearing steel on-line rapid spheroidizing annealing technology |
| WO2019001262A1 (en) * | 2017-06-28 | 2019-01-03 | 武汉理工大学 | Process for forming, by means of warm ring rolling, high-carbon chromium bearing steel capable of structure spheroidization |
| CN109055707A (en) * | 2018-10-26 | 2018-12-21 | 苏州轴承厂股份有限公司 | The heat treatment process of high-carbon-chromium bearing steel part |
| CN111763806A (en) * | 2020-06-23 | 2020-10-13 | 江苏龙城精锻有限公司 | Low-temperature annealing magnetic heat treatment process for low-carbon steel |
Non-Patent Citations (1)
| Title |
|---|
| 强文江等: "《金属材料学》", 30 September 2016, 冶金工业出版社 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114480797A (en) * | 2022-01-27 | 2022-05-13 | 石狮市汇星机械有限公司 | Heat treatment process method for producing knitting machine cam by using GCr15 steel |
| CN114686654A (en) * | 2022-04-07 | 2022-07-01 | 内蒙古科技大学 | Bearing steel spheroidizing annealing method and system based on pulsed magnetic field |
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Application publication date: 20220121 |