CN115404390A - Rare earth microalloyed high-temperature carburized bearing steel and preparation method thereof - Google Patents
Rare earth microalloyed high-temperature carburized bearing steel and preparation method thereof Download PDFInfo
- Publication number
- CN115404390A CN115404390A CN202211006073.2A CN202211006073A CN115404390A CN 115404390 A CN115404390 A CN 115404390A CN 202211006073 A CN202211006073 A CN 202211006073A CN 115404390 A CN115404390 A CN 115404390A
- Authority
- CN
- China
- Prior art keywords
- rare earth
- bearing steel
- weight percent
- steel
- carburized bearing
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 151
- 239000010959 steel Substances 0.000 title claims abstract description 151
- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 92
- 150000002910 rare earth metals Chemical class 0.000 title claims abstract description 49
- 238000002360 preparation method Methods 0.000 title claims abstract description 14
- 238000000034 method Methods 0.000 claims abstract description 50
- 230000008569 process Effects 0.000 claims abstract description 33
- 239000002131 composite material Substances 0.000 claims abstract description 24
- 238000010438 heat treatment Methods 0.000 claims abstract description 24
- 238000003723 Smelting Methods 0.000 claims abstract description 17
- 238000005255 carburizing Methods 0.000 claims abstract description 15
- 239000002994 raw material Substances 0.000 claims abstract description 11
- 238000007670 refining Methods 0.000 claims abstract description 10
- 238000005303 weighing Methods 0.000 claims abstract description 9
- 238000005242 forging Methods 0.000 claims abstract description 6
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 40
- 229910052799 carbon Inorganic materials 0.000 claims description 27
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 24
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 20
- 229910052759 nickel Inorganic materials 0.000 claims description 20
- 238000005496 tempering Methods 0.000 claims description 20
- 229910052804 chromium Inorganic materials 0.000 claims description 18
- 239000011651 chromium Substances 0.000 claims description 18
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 16
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 16
- 229910052750 molybdenum Inorganic materials 0.000 claims description 16
- 239000011733 molybdenum Substances 0.000 claims description 16
- 238000010313 vacuum arc remelting Methods 0.000 claims description 14
- 230000006698 induction Effects 0.000 claims description 10
- 229910052742 iron Inorganic materials 0.000 claims description 10
- 229910052720 vanadium Inorganic materials 0.000 claims description 10
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 10
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- 239000010703 silicon Substances 0.000 claims description 9
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 8
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 239000011572 manganese Substances 0.000 claims description 8
- 238000010791 quenching Methods 0.000 claims description 7
- 230000000171 quenching effect Effects 0.000 claims description 7
- PXHPOOHQBBWJBW-UHFFFAOYSA-N cerium rhenium Chemical group [Ce].[Re] PXHPOOHQBBWJBW-UHFFFAOYSA-N 0.000 claims description 6
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 6
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 4
- 238000010079 rubber tapping Methods 0.000 claims description 3
- FFBHFFJDDLITSX-UHFFFAOYSA-N benzyl N-[2-hydroxy-4-(3-oxomorpholin-4-yl)phenyl]carbamate Chemical compound OC1=C(NC(=O)OCC2=CC=CC=C2)C=CC(=C1)N1CCOCC1=O FFBHFFJDDLITSX-UHFFFAOYSA-N 0.000 claims 1
- 238000004519 manufacturing process Methods 0.000 abstract description 5
- 238000005299 abrasion Methods 0.000 abstract description 2
- 238000012545 processing Methods 0.000 abstract description 2
- 238000005096 rolling process Methods 0.000 abstract description 2
- 229910001566 austenite Inorganic materials 0.000 description 14
- 229910000734 martensite Inorganic materials 0.000 description 13
- 229910000859 α-Fe Inorganic materials 0.000 description 8
- 239000006104 solid solution Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000011159 matrix material Substances 0.000 description 6
- 230000003749 cleanliness Effects 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- 238000000265 homogenisation Methods 0.000 description 4
- 239000012535 impurity Substances 0.000 description 4
- 238000009826 distribution Methods 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 239000003921 oil Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910001315 Tool steel Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 230000001276 controlling effect Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910003178 Mo2C Inorganic materials 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- HSFWRNGVRCDJHI-UHFFFAOYSA-N alpha-acetylene Natural products C#C HSFWRNGVRCDJHI-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 150000001721 carbon Chemical group 0.000 description 1
- 125000004432 carbon atom Chemical group C* 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 125000002534 ethynyl group Chemical group [H]C#C* 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910017604 nitric acid Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
- C23C8/22—Carburising of ferrous surfaces
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
The invention discloses rare earth microalloyed high-temperature carburized bearing steel and a preparation method thereof, wherein the preparation method comprises the following steps: weighing raw materials and refining to obtain furnace burden; performing double vacuum smelting on the furnace burden and the composite rare earth element to obtain a steel ingot containing the rare earth element; and forging and forming the steel ingot, and carrying out a surface carburizing treatment process and a heat treatment process to obtain the rare earth microalloyed high-temperature carburized bearing steel. The high-temperature carburized bearing steel which is microalloyed by rare earth and is suitable for high-end key bearings has the advantages of high surface hardness, good core toughness and excellent fatigue resistance, is suitable for environments of high temperature, high rotating speed, abrasion and the like in the high-end equipment manufacturing industry of aerospace and the like, and is convenient for processing and manufacturing rolling bearings, sliding bearings, main shafts and other like parts.
Description
Technical Field
The invention belongs to the field of high-temperature carburized bearing steel, and particularly relates to rare earth microalloyed high-temperature carburized bearing steel and a preparation method thereof.
Background
The bearing is an important and key basic part in the equipment manufacturing industry, and the requirement on the bearing is higher and higher along with the rapid development of high-end industrial fields such as aviation, aerospace, high-speed rail and the like. The steel used to make bearings is called bearing steel, and the level of the bearing steel directly determines the service life of the bearing. The high-carbon chromium bearing steel GCr15 has typical chemical compositions (mass percentage, the same below) of 1% of carbon and 1.5% of chromium, a part of carbon solid solution matrix generates solid solution strengthening to enable the steel to have higher hardness, and the other part of carbon solid solution matrix is combined with iron and chromium to form carbide which is distributed on the matrix, so that the requirement of the bearing on wear resistance is met. Since GCr15 has high hardness and wear resistance and is cheap, GCr has occupied most of the bearing fields since being invented at the beginning of the 20 th century till now. However, since GCr15 has a high carbon content, large-sized carbides are easily formed, the toughness of steel is seriously affected, and it can be used only at room temperature or low temperature (< 150 ℃), thus limiting the range of application. Under certain high-temperature service environments, such as aircraft engines, the bearings need to be guaranteed to have good high-temperature resistance, so that the high-speed tool steel is used for reference, the 8Cr4Mo4V (M50) is designed by secondary hardening, the typical chemical components of the high-speed tool steel are 0.8% of carbon, 4% of chromium, 4% of molybdenum and 1% of vanadium, and the steel is separated out stable Mo2C carbide after high-temperature tempering, so that the use requirement of the high-temperature environment below 350 ℃ is met. Along with the increase of the rotating speed of the bearing of the aeroengine, the DN value is continuously increased, and the bearing steel is required to have the performances of high temperature resistance, high hardness, wear resistance, high fatigue resistance and the like, and also has good impact resistance. Therefore, the high-temperature carburized bearing steel G13Cr4Mo4Ni4V (M50 NiL) was developed by reducing carbon and increasing nickel on the basis of 8Cr4Mo 4V. The carbon content is reduced, and the toughness of the steel can be improved; the nickel content is increased, the carbon atom absorption capacity of the surface can be reduced, the diffusion of carbon atoms in austenite is accelerated, the carburizing heat treatment is facilitated, and meanwhile, the nickel can also improve the toughness of steel.
High temperature carburized bearing steel has not been widely used to date because of its unstable properties. The source influencing the performance fluctuation lies in that the cleanliness of the steel is not high, namely, higher gas elements and impurity elements exist in the steel, and further, the size, distribution, shape and the like of inclusions in the steel are influenced. With the continuous development of smelting process, the contents of gas elements and impurity elements of high-temperature carburized bearing steel can be controlled at a lower level through Vacuum Induction Melting (VIM) and Vacuum Arc Remelting (VAR), but the shape of inclusions is a bottleneck restricting the stability of performance. The method for modifying the inclusions and effectively improving the performance by adding trace rare earth into the bearing steel is an effective method, but at present, the method is mostly used for high-carbon chromium bearing steel, and the high-temperature carburized bearing steel is rarely reported. Aiming at the problems, the patent provides rare earth microalloying high-temperature carburized bearing steel and a preparation method thereof, and the purpose of improving the cleanliness and the mechanical property of the steel is achieved.
Disclosure of Invention
In order to overcome the defects in the prior art, the invention aims to provide the rare earth microalloyed high-temperature carburized bearing steel which has high cleanliness, high surface hardness, good wear resistance, good toughness of a core matrix, high temperature resistance and excellent fatigue resistance and is suitable for high-end key bearings, and the ultrapure purification preparation method thereof. In order to achieve the purpose, the invention provides the following technical scheme:
a preparation method of rare earth microalloyed high-temperature carburized bearing steel comprises the following steps:
weighing raw materials and refining to obtain furnace burden;
performing double vacuum smelting on the furnace burden and the composite rare earth element to obtain a steel ingot containing the rare earth element;
and (3) subjecting the steel ingot to a forging forming process, a surface carburizing treatment process and a heat treatment process to obtain the rare earth microalloyed high-temperature carburized bearing steel.
Specifically, the furnace burden and the composite rare earth element comprise the following components in percentage by weight:
0.11 to 0.15 weight percent of carbon, 4.00 to 4.25 weight percent of chromium, 4.00 to 4.50 weight percent of molybdenum, 1.13 to 1.33 weight percent of vanadium, 3.20 to 3.60 weight percent of nickel, 0.15 to 0.35 weight percent of manganese, 0.10 to 0.25 weight percent of silicon, 0.05 to 0.2 weight percent of composite rare earth element and the balance of iron;
specifically, the composite rare earth element is a rhenium-cerium composite rare earth element.
Further, the raw materials are weighed and refined, and the furnace burden is obtained by the following specific steps:
weighing carbon, chromium, molybdenum, nickel and iron according to weight percentage to obtain raw materials;
and sequentially adding vanadium, manganese and silicon into the raw materials for refining to obtain the furnace burden.
Further, the double vacuum smelting of the furnace burden and the composite rare earth element to obtain the steel ingot containing the rare earth element comprises the following specific steps:
adding rhenium-cerium composite rare earth elements 5 minutes before the furnace burden tapping to obtain molten steel;
and smelting the molten steel by adopting double vacuum to obtain a steel ingot containing rare earth elements.
Specifically, the double vacuum smelting comprises vacuum induction smelting and vacuum arc remelting.
Further, the heat treatment process comprises the following specific steps:
and (3) cold treatment: quenching and preserving heat of the sample after the surface carburization treatment process, cooling the sample to room temperature with oil, then carrying out low-temperature treatment and heat preservation, and then restoring to room temperature;
and (3) tempering: tempering the sample recovered to the room temperature, preserving heat and then cooling in air;
and repeating the cold treatment step and the tempering step once to obtain the rare earth microalloyed high-temperature carburized bearing steel.
Specifically, in the cold treatment step, the quenching temperature of the sample is 1040-1080 ℃, and the holding time is 1 hour.
Specifically, in the cold treatment step, the low-temperature treatment temperature is-78 ℃, and the heat preservation time is 2 hours.
Specifically, in the tempering step, the tempering temperature is 500-550 ℃, and the heat preservation time is 2 hours.
Furthermore, after the heat treatment process of the rare earth microalloyed high-temperature carburized bearing steel, the surface hardness is more than or equal to 57.3HRC, the tensile strength is more than or equal to 1300MPa, the elongation is more than or equal to 15 percent, the core hardness is more than or equal to 42HRC, and the fracture toughness is more than or equal to 45 MPa.m 1/2 The grain size is more than or equal to 5 grade.
The rare earth microalloyed high-temperature carburized bearing steel comprises the following components in percentage by weight:
0.11 to 0.15 weight percent of carbon, 4.00 to 4.25 weight percent of chromium, 4.00 to 4.50 weight percent of molybdenum, 1.13 to 1.33 weight percent of vanadium, 3.20 to 3.60 weight percent of nickel, 0.15 to 0.35 weight percent of manganese, 0.10 to 0.25 weight percent of silicon, 0.05 to 0.2 weight percent of composite rare earth elements and the balance of iron.
The invention has the technical effects and advantages that:
the high-temperature carburized bearing steel which is microalloyed by rare earth and is suitable for the high-end key bearing has excellent toughness matching performance and fatigue resistance, and because the addition of the rare earth element reduces segregation, refines grains, purifies grain boundaries and causes impurities to deteriorate. The addition of trace rare earth improves the purity and homogeneity of the high-temperature carburized bearing steel, not only spheroidizes, refines and uniformly distributes carbides, but also changes harmful inclusions into small-size nearly-spherical inclusions, thereby improving the mechanical property of the steel and the fatigue resistance of the steel. The added trace rare earth is also beneficial to improving the oxidation resistance of the steel, adjusting the thermal expansion coefficient of the steel and improving the dimensional stability and the wear resistance of the machined high-end key bearing part. The high-temperature carburized bearing steel has high surface hardness, good core toughness and excellent fatigue resistance, is suitable for environments of high temperature, high rotating speed, abrasion and the like in the aerospace high-end equipment manufacturing industry and is convenient for processing and manufacturing rolling bearings, sliding bearings, main shafts and other like parts.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and claims hereof as well as the appended drawings.
Drawings
FIG. 1 is a flow chart of a preparation method of rare earth microalloyed high temperature carburized bearing steel of the present invention;
FIG. 2 shows the as-cast structure of a double vacuum smelted ingot of a rare earth microalloyed high temperature carburized bearing steel of the present invention;
FIG. 3 shows the microstructure of the rare earth microalloyed high temperature carburized bearing steel after homogenization heat treatment.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
In order to solve the defects of the prior art, the invention discloses rare earth microalloyed high-temperature carburized bearing steel and a preparation method thereof, and the preparation method specifically comprises the following steps:
the high-temperature carburized bearing steel of the high-end key bearing adopting rare earth microalloying has the main characteristic of combining high hardness and high toughness, thereby meeting the performance requirement of the bearing service in a high-temperature and high-speed environment. The key technology of the characteristic lies in the cooperation of the effect of designing rare earth element purified steel and a heat treatment process. The high-temperature carburized bearing steel which is microalloyed by rare earth and is suitable for a high-end key bearing is martensitic steel, and the basic condition for forming a martensitic structure is that austenite must be formed at a quenching temperature, so that the steel contains a certain amount of austenite forming elements. The steel of the invention is formed by controlling elements such as carbon, nickel, manganese and the like to promote austenite.
Carbon: carbon is one of the strongest effective elements for forming austenite and is also an effective element for improving the hardness, but if the content is controlled to be proper, excessive carbide is easily generated due to too high carbon content, and the toughness and the fatigue performance of steel are adversely affected; the carbon content is too low and the core hardness of the steel does not meet the requirements. The carbon content of the bearing steel is preferably controlled to be 0.11-1.15 wt%.
Nickel: nickel is the best element for forming and stabilizing austenite and is also the main additive element for improving the toughness of steel. The nickel reduces dislocation resistance in the steel and improves the toughness of the steel; the carbon curve is shifted to the right, and the hardenability of the steel is improved; the Ms point (martensitefinish, which means the martensite finish temperature) of the steel is lowered, and the residual austenite in the steel is increased. However, too much nickel will promote the segregation of harmful elements in the steel and increase the temper brittleness of the steel. In addition, the nickel resource is in short supply and the price is high, so that the nickel is saved as much as possible. The content of nickel in the bearing steel is preferably controlled to be 3.20-3.60 wt%.
Manganese: manganese has a large effect of expanding an austenite region and is infinitely solid-dissolved in austenite, so that the steel can more easily obtain austenite when a certain amount of manganese is added to the steel. The content of manganese in the bearing steel is preferably controlled to be 0.15-0.35 wt%.
The bearing steel of the present invention also contains elements such as chromium, molybdenum, etc., which are ferrite-forming elements. It combines with ferrite forming elements to facilitate the creation of a balanced structure. The structure and the performance of the bearing steel are controlled by adjusting the contents of ferrite forming elements and austenite forming elements.
Chromium: chromium increases the hardenability of the steel and has a secondary hardening effect, which increases the hardness and wear resistance of carbon steel without making the steel brittle, and also reduces the martensitic transformation point, making the steel difficult to harden, since ferrite is more likely to appear in martensitic steels. The chromium content in the bearing steel of the invention is preferably controlled to be 4.00-4.25 wt%.
Molybdenum: molybdenum can effectively improve the hardenability of steel and the tempering resistance or tempering stability of steel, molybdenum is a stronger carbide forming element and is combined with carbon to form stable small-size carbide, the hardness of steel is improved, and a certain wear resistance is maintained. However, excessive molybdenum tends to cause ferrite and lower the martensite transformation point, making the steel difficult to harden. The content of molybdenum in the bearing steel is preferably controlled to be 4.00-4.50 wt%.
The addition of trace rare earth elements can change the quality of impurities and improve and optimize the structure and the grain size of steel, and the content of the rare earth elements in the bearing steel is preferably controlled to be 0.05 to 0.2 weight percent.
On one hand, the preparation method of the rare earth microalloyed bearing steel is shown in the attached drawing 1 and comprises the following steps:
weighing raw materials and refining to obtain furnace burden;
performing double vacuum smelting on the furnace burden and the composite rare earth element to obtain a steel ingot containing the rare earth element;
and (3) subjecting the steel ingot to a forging forming process, a surface carburizing treatment process and a heat treatment process to obtain the rare earth microalloyed high-temperature carburized bearing steel.
Further, the furnace burden and the composite rare earth element comprise the following components in percentage by weight:
0.11 to 0.15 weight percent of carbon, 4.00 to 4.25 weight percent of chromium, 4.00 to 4.50 weight percent of molybdenum, 1.13 to 1.33 weight percent of vanadium, 3.20 to 3.60 weight percent of nickel, 0.15 to 0.35 weight percent of manganese, 0.10 to 0.25 weight percent of silicon, 0.05 to 0.2 weight percent of composite rare earth element and the balance of iron.
Further, weighing raw materials for refining to obtain furnace burden, and performing Vacuum Induction Melting (VIM) and Vacuum Arc Remelting (VAR) on the furnace burden and rare earth elements to obtain a steel ingot containing rare earth elements, wherein the method comprises the following specific steps:
weighing the furnace charge containing the carbon, chromium, molybdenum, nickel and iron components according to certain weight percentage, putting the furnace charge into a vacuum induction furnace, and then vacuumizing to 5Pa to obtain the final productAnd preheating for 15 minutes, then heating the vacuum induction furnace to melt the furnace charge, adding vanadium after the furnace charge is molten down, continuing refining for 20 minutes, then introducing argon to 13000Pa, adding manganese and silicon for refining for 10 minutes, finally adding rhenium-cerium composite rare earth elements, and tapping after 5 minutes to obtain the vacuum induction cast ingot. Removing the head, tail and polished surface of the vacuum induction cast ingot, and then performing Vacuum Arc Remelting (VAR) smelting, wherein the melting speed is controlled to be 1.2-2 kg.min -1 The steel ingot containing the rare earth elements can be obtained, the double vacuum casting state structure diagram of the steel ingot is shown as the attached figure 2, the steel ingot obtained by the invention steel adopts double vacuum smelting, the structure of the steel ingot is compact, and high-temperature ferrite exists on part of the grain boundary.
Further, the steel ingot containing the rare earth element is subjected to homogenization treatment, a microstructure diagram of the homogenized steel ingot is shown in fig. 3, after the high-temperature homogenization treatment, high-temperature ferrite on a grain boundary of the steel ingot is eliminated, and the steel ingot has an important effect on improvement of comprehensive mechanical properties of the steel ingot.
Further, the steel ingot containing the rare earth elements is subjected to homogenization treatment and then subjected to a forging forming process, a surface carburizing treatment process and a heat treatment process, and the method specifically comprises the following steps:
forging and forming a rare earth element-containing steel ingot obtained by Vacuum Arc Remelting (VAR), performing vacuum low-pressure pulse carburization on the forged and formed bar by using a vacuum carburizing furnace, and then performing a conventional heat treatment process.
Specifically, the whole carburizing process flow is as follows:
cleaning the surface of the part, putting the part into a vacuum carburizing furnace, vacuumizing, heating, and then introducing carburizing atmosphere for pulse carburizing. The air pressure in the vacuum furnace is 400Pa, and the carburizing agent is acetylene (C) 2 H 2 ) While adding appropriate nitrogen (N) 2 ) And intermittently introducing a carburizing agent, performing carburizing and diffusion at the temperature of 880-930 ℃ for 11-13h, performing oil cooling, and repeating high-temperature tempering twice after carburizing.
Specifically, the whole heat treatment process flow is as follows:
quenching the semi-finished steel after the surface carburization treatment process, carrying out oil cooling to room temperature at the quenching temperature of 1040-1080 ℃ for 1 hour, carrying out low-temperature treatment at-78 ℃ for 2 hours, carrying out tempering treatment after returning to room temperature, selecting the tempering temperature of 500-550 ℃ and carrying out tempering for 2 hours, and carrying out air cooling. And repeating the cold treatment step and the tempering step once to obtain the rare earth microalloyed high-temperature carburized bearing steel.
The bearing steel after the heat treatment process has the surface hardness of more than or equal to 57.3HRC, the core hardness of more than or equal to 42HRC, the tensile strength of more than or equal to 1300MPa, the elongation of more than or equal to 15 percent and the fracture toughness of more than or equal to 45 MPa.m 1/2 The grain size is more than or equal to 5 grade.
The high-temperature carburized bearing steel suitable for the high-end bearing, which is microalloyed by rare earth, is tested according to different heat treatment processes, and the obtained results are listed in table 1.
TABLE 1 Heat treatment Process and hardness test results thereof
As shown in Table 1, the core hardness of the high-temperature carburized bearing steel which is microalloyed by rare earth and is suitable for a high-end key bearing is higher than 42HRC after the high-temperature carburized bearing steel is subjected to a heat treatment process.
After the heat treatment process, the core matrix structure of the bearing steel consists of martensite, fine carbides dispersed in the martensite and a small amount of residual austenite.
On the other hand, the rare earth microalloyed high temperature carburized bearing steel of the embodiment comprises the following components in percentage by weight:
0.11 to 0.15 weight percent of carbon, 4.00 to 4.25 weight percent of chromium, 4.00 to 4.50 weight percent of molybdenum, 1.13 to 1.33 weight percent of vanadium, 3.20 to 3.60 weight percent of nickel, 0.15 to 0.35 weight percent of manganese, 0.10 to 0.25 weight percent of silicon, 0.05 to 0.2 weight percent of composite rare earth element and the balance of iron.
Specifically, the composite rare earth element is a rhenium-cerium composite rare earth element.
Further, the high-temperature carburized bearing steel is corroded by 4wt% nitric acid alcohol solution, and the annealed structure of the high-temperature carburized bearing steel is spherical pearlite, ferrite and carbide. The annealed average hardness was 234HV. The globular pearlite, ferrite and carbide structure and the 234HV hardness give the steel grade excellent machinability.
The high-temperature carburized bearing steel adopting rare earth microalloying and being suitable for the high-end key bearing adopts the alloying principle of secondary hardening, and realizes solid solution strengthening and precipitation strengthening by adding alloy elements and adopting a proper heat treatment process. In order to meet the requirements of strength, hardness and other properties, the steel is heated to austenitizing temperature by a heat treatment process, then is completely transformed into a martensite structure by adopting an oil-cooling mode, austenite in the steel is further transformed into martensite by adopting cold treatment, and then carbide distribution and residual austenite form in the steel are regulated and controlled by proper tempering. The core of the invention lies in that the Vacuum Induction Melting (VIM) and Vacuum Arc Remelting (VAR) smelting methods are creatively adopted, the metallurgical quality of the high-temperature carburized bearing steel is improved by adding trace rare earth elements, and then the tissue balance of the steel is regulated and controlled by a general heat treatment process, so that the application requirements of the steel suitable for the high-end key bearing are finally met. Vacuum Induction Melting (VIM) and Vacuum Arc Remelting (VAR) smelting greatly improve the purity of the molten steel, and the addition of high-purity rare earth enables the molten steel to have better hydrogen and oxygen removal effects, thereby being beneficial to improving the cleanliness of steel. The addition of trace rare earth can also control the distribution form of carbide in the steel so as to ensure that the steel achieves the best performance. The rare earth is distributed in martensite to form supersaturated solid solution, and the martensite bearing steel matrix obtains higher hardness by controlling the lattice distortion degree of the supersaturated solid solution and the dispersity of martensite structure. The invention improves the cleanliness of steel by creatively adding rare earth, realizes the purposes of solid solution strengthening and precipitation strengthening, and does not optimize the structure and improve the grain size in the common sense.
Finally, it should be noted that: although the present invention has been described in detail with reference to the foregoing embodiments, it will be apparent to those skilled in the art that modifications may be made to the embodiments or portions thereof without departing from the spirit and scope of the invention.
Claims (11)
1. A preparation method of rare earth microalloyed high-temperature carburized bearing steel is characterized by comprising the following steps:
weighing raw materials and refining to obtain furnace burden;
performing double vacuum smelting on the furnace burden and the composite rare earth element to obtain a steel ingot containing the rare earth element;
and (3) subjecting the steel ingot to a forging forming process, a surface carburizing treatment process and a heat treatment process to obtain the rare earth microalloyed high-temperature carburized bearing steel.
2. The preparation method of the rare earth microalloyed high temperature carburized bearing steel as claimed in claim 1, wherein the furnace burden and the composite rare earth elements comprise the following components in percentage by weight:
0.11 to 0.15 weight percent of carbon, 4.00 to 4.25 weight percent of chromium, 4.00 to 4.50 weight percent of molybdenum, 1.13 to 1.33 weight percent of vanadium, 3.20 to 3.60 weight percent of nickel, 0.15 to 0.35 weight percent of manganese, 0.10 to 0.25 weight percent of silicon, 0.05 to 0.2 weight percent of composite rare earth element and the balance of iron;
the composite rare earth element is a rhenium-cerium composite rare earth element.
3. The method for preparing rare earth microalloyed high temperature carburized bearing steel according to claim 1,
the method comprises the following steps of weighing raw materials, refining and obtaining furnace burden:
weighing carbon, chromium, molybdenum, nickel and iron according to weight percentage to obtain raw materials;
and sequentially adding vanadium, manganese and silicon into the raw materials for refining to obtain the furnace burden.
4. The method for preparing rare earth microalloyed high temperature carburized bearing steel according to claim 1, characterized in that,
the method comprises the following specific steps of performing double vacuum smelting on the furnace burden and the composite rare earth element to obtain the steel ingot containing the rare earth element:
adding rhenium-cerium composite rare earth elements 5 minutes before the furnace burden tapping to obtain molten steel;
and smelting the molten steel in double vacuum to obtain a steel ingot containing the rare earth element.
5. The method for preparing rare earth microalloyed high temperature carburized bearing steel according to claim 1 or 4, characterized in that the double vacuum smelting comprises vacuum induction smelting and vacuum arc remelting.
6. The method for preparing rare earth microalloyed high temperature carburized bearing steel according to claim 1, characterized in that the heat treatment process comprises the following specific steps:
and (3) cold treatment: quenching and preserving heat of the sample after the surface carburization treatment process, cooling the sample to room temperature, then carrying out low-temperature treatment and heat preservation, and then restoring to the room temperature;
tempering: tempering the sample recovered to the room temperature, preserving heat and then cooling in air;
and repeating the cold treatment step and the tempering step once to obtain the rare earth microalloyed high-temperature carburized bearing steel.
7. The method for preparing rare earth microalloyed high temperature carburized bearing steel according to claim 6, characterized in that in the cold treatment step, the quenching temperature of the sample is 1040-1080 ℃ and the holding time is 1 hour.
8. The method for preparing rare earth microalloyed high temperature carburized bearing steel according to claim 6, characterized in that, in the cold treatment step, the low temperature treatment temperature is-78 ℃ and the holding time is 2 hours.
9. The method for preparing rare earth microalloyed high temperature carburized bearing steel according to claim 6, characterized in that in the tempering step, the tempering temperature is 500-550 ℃ and the tempering time is 2 hours.
10. The method for preparing rare earth microalloyed high-temperature carburized bearing steel according to claim 1 or 6, characterized in that the rare earth microalloyed high-temperature carburized bearing steel has a surface hardness of 57.3HRC or more, a tensile strength of 1300MPa or more, an elongation of 15% or more, a core hardness of 42HRC or more, and a fracture toughness of 45 MPa-mMm or more after a heat treatment process 1/2 The grain size is more than or equal to 5 grade.
11. A rare earth microalloyed high temperature carburized bearing steel prepared by the method of any one of claims 1 to 10, characterized in that the rare earth microalloyed high temperature carburized bearing steel comprises the following components in percentage by weight:
0.11 to 0.15 weight percent of carbon, 4.00 to 4.25 weight percent of chromium, 4.00 to 4.50 weight percent of molybdenum, 1.13 to 1.33 weight percent of vanadium, 3.20 to 3.60 weight percent of nickel, 0.15 to 0.35 weight percent of manganese, 0.10 to 0.25 weight percent of silicon, 0.05 to 0.2 weight percent of composite rare earth element and the balance of iron.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211006073.2A CN115404390A (en) | 2022-08-22 | 2022-08-22 | Rare earth microalloyed high-temperature carburized bearing steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211006073.2A CN115404390A (en) | 2022-08-22 | 2022-08-22 | Rare earth microalloyed high-temperature carburized bearing steel and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN115404390A true CN115404390A (en) | 2022-11-29 |
Family
ID=84161294
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211006073.2A Pending CN115404390A (en) | 2022-08-22 | 2022-08-22 | Rare earth microalloyed high-temperature carburized bearing steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115404390A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116497262A (en) * | 2023-06-20 | 2023-07-28 | 成都先进金属材料产业技术研究院股份有限公司 | Method for improving surface hardness of low-carbon high-alloy martensitic bearing steel |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110527911A (en) * | 2019-09-16 | 2019-12-03 | 北京航空航天大学 | Anti-corrosion gear-bearing steel of a kind of low-density high-strength height and preparation method thereof |
| CN113564320A (en) * | 2021-08-05 | 2021-10-29 | 沈阳工业大学 | Heat treatment method of G13Cr4Mo4Ni4V steel for aeroengine bearing |
| CN113755671A (en) * | 2021-09-17 | 2021-12-07 | 沈阳工业大学 | Heat treatment method for improving fatigue performance of carburized G13Cr4Mo4Ni4V steel |
-
2022
- 2022-08-22 CN CN202211006073.2A patent/CN115404390A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110527911A (en) * | 2019-09-16 | 2019-12-03 | 北京航空航天大学 | Anti-corrosion gear-bearing steel of a kind of low-density high-strength height and preparation method thereof |
| CN113564320A (en) * | 2021-08-05 | 2021-10-29 | 沈阳工业大学 | Heat treatment method of G13Cr4Mo4Ni4V steel for aeroengine bearing |
| CN113755671A (en) * | 2021-09-17 | 2021-12-07 | 沈阳工业大学 | Heat treatment method for improving fatigue performance of carburized G13Cr4Mo4Ni4V steel |
Non-Patent Citations (2)
| Title |
|---|
| 吴志伟等: "钢铁材料的冷处理", 《金属热处理》 * |
| 王黎钦: "《滚动轴承的极限设计》", 31 December 2013, 哈尔滨工业大学出版社 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116497262A (en) * | 2023-06-20 | 2023-07-28 | 成都先进金属材料产业技术研究院股份有限公司 | Method for improving surface hardness of low-carbon high-alloy martensitic bearing steel |
| CN116497262B (en) * | 2023-06-20 | 2023-10-31 | 成都先进金属材料产业技术研究院股份有限公司 | Method for improving surface hardness of low-carbon high-alloy martensitic bearing steel |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111394639B (en) | Manufacturing method of high-wear-resistance gear steel | |
| CN107587079B (en) | Nitrogenous microalloying spring steel and preparation method thereof | |
| JPH07238350A (en) | Surface-carburized stainless steel alloy for high-temperature use, article produced from it, and its production | |
| JP7096382B2 (en) | High carbon bearing steel and its manufacturing method | |
| CN112981239B (en) | Quenched and tempered low-carbon alloy steel and manufacturing method thereof | |
| CN112746217B (en) | High-strength low-expansion invar alloy wire and manufacturing method thereof | |
| CN111748739B (en) | Heat-resistant spring steel with tensile strength of more than 2100MPa and production method thereof | |
| CN111850393B (en) | Bainite die steel and preparation method thereof | |
| CN113322415A (en) | Martensitic stainless steel for aviation bearing and preparation method thereof | |
| CN111850399A (en) | Corrosion-resistant plastic die steel with good wear resistance and preparation method thereof | |
| CN113564490B (en) | 8Cr4Mo4V aviation bearing steel added with trace elements | |
| CN115404390A (en) | Rare earth microalloyed high-temperature carburized bearing steel and preparation method thereof | |
| JP3385722B2 (en) | Carburizing and quenching method | |
| JPH083720A (en) | Parts made of steel excellent in rolling fatigue life and its production | |
| CN114134397A (en) | Steel suitable for cold extrusion ball screw and production method thereof | |
| CN108300941A (en) | A kind of high pressure slurry pump pump housing steel and its manufacturing method | |
| CN115558870B (en) | Economical high-service-life high-power steel for wind power yaw bearing ring, bearing ring and production process | |
| CN113718174B (en) | Double-refining high-strength high-toughness long-life medium-high carbon bearing steel and preparation method thereof | |
| CN113462951A (en) | Preparation method of ultrahigh-strength and high-toughness alloy steel | |
| CN108342658B (en) | Steel for shafts and gears and heat treatment method thereof | |
| CN112795722A (en) | Austempering technology for austempered ductile iron | |
| JPH0559527A (en) | Production of steel excellent in wear resistance and rolling fatigue characteristic | |
| CN114892071B (en) | High-temperature carburized gear steel for new energy vehicle and manufacturing method | |
| CN115747645B (en) | Steel for high-strength high-contact fatigue high-power wind power yaw bearing ring, bearing ring and production process | |
| JPH04198417A (en) | Method for producing bearing steel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20221129 |