CN116377333A - Microalloyed bearing steel casting blank with fine and homogenized structure - Google Patents
Microalloyed bearing steel casting blank with fine and homogenized structure Download PDFInfo
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- CN116377333A CN116377333A CN202310472542.8A CN202310472542A CN116377333A CN 116377333 A CN116377333 A CN 116377333A CN 202310472542 A CN202310472542 A CN 202310472542A CN 116377333 A CN116377333 A CN 116377333A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 76
- 239000010959 steel Substances 0.000 title claims abstract description 76
- 238000005266 casting Methods 0.000 title claims abstract description 54
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 27
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052684 Cerium Inorganic materials 0.000 claims abstract description 3
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 3
- 150000002910 rare earth metals Chemical class 0.000 claims abstract description 3
- 238000004512 die casting Methods 0.000 claims description 7
- 238000009749 continuous casting Methods 0.000 claims description 6
- 230000006698 induction Effects 0.000 claims description 4
- 238000003723 Smelting Methods 0.000 claims description 3
- 229910045601 alloy Inorganic materials 0.000 claims 1
- 239000000956 alloy Substances 0.000 claims 1
- 230000033228 biological regulation Effects 0.000 abstract description 6
- 239000000463 material Substances 0.000 abstract description 5
- 238000000034 method Methods 0.000 abstract description 5
- 238000000265 homogenisation Methods 0.000 description 15
- 238000007670 refining Methods 0.000 description 11
- 238000005275 alloying Methods 0.000 description 10
- 238000004519 manufacturing process Methods 0.000 description 6
- 239000000203 mixture Substances 0.000 description 5
- 238000001816 cooling Methods 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 230000002787 reinforcement Effects 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000006399 behavior Effects 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000000399 optical microscopy Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
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- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
Abstract
A micro-alloyed bearing steel casting blank with fine and homogenized structure belongs to the technical field of steel material structure property regulation. The components are C0.93% -1.05%, si:0.20-0.50%, mn:0.20% -0.50%, cr:1.30-1.6%, S: less than or equal to 0.01 percent, P: less than or equal to 0.02 percent, cu: less than or equal to 0.25 percent, less than or equal to 0.30 percent of Mo, nb: less than or equal to 0.30 percent, V: less than or equal to 0.30 percent, zr:0 to 0.30 percent and Al less than or equal to 0.05 percent. On this basis, rare earth (Ce, la) may be added: less than or equal to 0.05 percent, ni: less than or equal to 1.0 percent; the balance being Fe. The method has the advantages that the original austenite size of the casting blank is thinned by more than 5 times, so that the wear resistance, the fatigue life and the toughness of the bearing steel can be greatly improved; the method can be applied to bearing steel, gear steel and die steel, and can also be applied to the tissue regulation and control of other steel materials.
Description
Technical Field
The invention belongs to the technical field of regulation and control of the tissue performance of steel materials, and particularly provides a microalloyed bearing steel casting blank with tissue refining and homogenizing; relates to an alloying design for refining and homogenizing the structure of a casting blank of steel materials. The bearing steel casting blank structure refining technology disclosed by the invention refines the original austenite size of the casting blank by more than 5 times, provides a simple and feasible control technology for refining, homogenizing and stabilizing the structure performance of a bearing steel product, and can greatly improve the wear resistance, fatigue life and toughness of the bearing steel. The invention can be applied to bearing steel, gear steel and die steel, and can also be applied to the tissue regulation and control of other steel materials.
Background
High contact fatigue life, high wear resistance and high toughness are the future development direction of high-performance bearing steel, and the refinement, homogenization and high reinforcement of the bearing steel are important ways for realizing the high performance of the bearing steel. In order to achieve the purpose, the conventional bearing steel realizes grain size and carbide refinement in the bearing steel through a large-section casting blank, and the refining and homogenization regulation and control of the structure of the bearing steel casting blank are not concerned, so that the bearing steel casting blank is increasingly developed to be large-scale. However, the large size of the casting blank of the bearing steel further limits the refinement and homogenization of the bearing steel product, resulting in the reduction of the toughness, the fatigue life and the wear resistance of the bearing steel product. How to solve the key scientific and technical problems that the bearing steel is thinned and homogenized. Meanwhile, along with the development demands of large bearings such as wind power, shield and the like, the refinement and homogenization of large casting blanks also become an important development direction of bearing steel. Therefore, the method solves the development direction that the homogenization and the refinement of the bearing steel casting blank become future high-performance bearing steel and large-section bearing steel casting blanks.
Research shows that the original austenite and carbide double refinement of the bearing steel can greatly improve the toughness, fatigue life and wear resistance of the bearing steel. The grain size of the bearing steel is thinned from 15-20 micrometers to 5-10 micrometers by carrying out double-thinning heat treatment on the GCr15 bearing steel product, so that the strength of the bearing steel GCr15 can be improved from 2000MPa to 2500MPa, and the fatigue life of the bearing steel can be prolonged from L 10 ≥1.0x10 7 Secondary increase to L 10 ≥5.0x10 7 And twice. Meanwhile, the abrasion resistance of the bearing steel is greatly improved due to tissue refinement. Therefore, the refinement and homogenization of the bearing steel structure not only improves the toughness of the bearing steel, but also greatly improves the fatigue life and wear resistance of the bearing steel. However, since the bearing steel structure is inherited, the coarse as-cast structure cannot achieve sufficient structure refinement and homogenization through subsequent limited deformation. In addition, the traditional bearing steel production needs to realize component bearing steel component uniformity by long-time high-temperature homogenization to reduce casting blank segregation, which leads to serious coarsening of a bearing steel casting blank structure and coarse and uneven final bearing steel product structure. In order to realize the refinement and homogenization of the structure of the bearing steel, a manufacturing technical route for producing high-performance bearing steel products by ultra-large-specification casting blanks is proposed at home and abroad, the domestic bearing steel production is developed from the original continuous casting of small square billets of 180mmx and 220mm to the current large square billets of 480mmx and 520mm, and great challenges are brought to the casting and rolling and cooling control equipment capability of the bearing steel, and the refinement, homogenization and high reinforcement of matrix structures and carbides of the bearing steel products cannot be effectively solved. In the future, improvement is needed from the aspects of component design and technological process of bearing steel, so that double refinement of a substrate structure and carbide of a bearing steel product is realized, and on one hand, the reduction of the production of bearing steel by the large-scale casting blank section and the large deformation in the rolling process is realizedProduction equipment is too high in requirement. On the other hand, the requirement of a bearing steel casting blank with the diameter of 1000mm is provided for large-scale equipment such as high-power and long-service-life wind power, the requirement is far greater than the diameter specification of a traditional bearing steel bar product, and the problems of refinement and homogenization of large-size bearing steel are solved through the alloying design and technological process improvement of the bearing steel.
Disclosure of Invention
The invention aims to provide a micro-alloyed bearing steel casting blank with finer and homogenized structure, which solves the problems of finer and homogenized large-size bearing steel. Through the alloying and gold design of the bearing steel casting blank structure refining homogenization, the refining of the bearing steel casting blank matrix structure (the prior austenite grain size) from millimeter level to hundred micrometers level (refining by more than 5 times) is realized, and the high-quality casting is provided for the manufacture of the bearing steel with high strength, high fatigue performance and wear resistance.
The invention can realize the novel alloying design of refining the prior austenite grains and carbide in the bearing steel casting blank. By alloying Nb, mo and V, the structure of the casting blank is greatly thinned, and a high-quality casting blank is provided for subsequent thermal deformation and heat treatment, so that the toughness, high contact fatigue performance and high wear resistance of the bearing steel are ensured.
1. Chemical composition design
The microalloyed bearing steel casting blank with fine and homogenized structure comprises the following components of 0.93% -1.05% of C, si:0.20-0.50%, mn:0.20% -0.50%, cr:1.30-1.6%, S: less than or equal to 0.01 percent, P: less than or equal to 0.02 percent, cu: less than or equal to 0.25 percent, less than or equal to 0.30 percent of Mo, nb: less than or equal to 0.30 percent, V: less than or equal to 0.30 percent, zr:0 to 0.30 percent and Al less than or equal to 0.05 percent. On this basis, rare earth (Ce, la) may be added: less than or equal to 0.05 percent, ni: less than or equal to 1.0 percent; the balance being Fe.
The function and basis of each element of the invention have two main points. The main alloying elements of the bearing steel are C, si, mn, cr and Fe, so that the basic performance of the bearing steel GCr15 is ensured, and the structure refinement regulation and control are realized through Mo, nb, V and Zr alloying, so that the toughness, fatigue performance and wear resistance are improved.
2. Manufacturing process and conditions
The bearing steel casting blank designed by the invention can be smelted by vacuum induction, an electric furnace or a converter, and then the casting blank is formed by die casting or continuous casting, wherein the grain size of the prior austenite on the surface is less than or equal to 150 mu m, and the grain size of the prior austenite at the positions of the core and the radius 1/2 is less than or equal to 250 mu m.
Drawings
FIG. 1 is a diagram of a casting structure of a cast billet at a radius of 1/2 without Mo/Nb/V/Zr alloying, showing the prior austenite grain size of about 1000 μm.
FIG. 2 is a diagram of the casting structure of a Mo/Nb/V/Zr cast slab added in a total amount of 0.05 at a radius of 1/2, showing the prior austenite grain size of about 700 μm.
FIG. 3 is a diagram of a casting structure of a Mo/Nb/V/Zr cast slab added in a total amount of 0.10 at a radius of 1/2, showing a prior austenite grain size of about 500 μm.
FIG. 4 is a diagram of the casting structure of a Mo/Nb/V/Zr cast slab at a radius of 1/2 with a total addition of 0.30%, showing the prior austenite grain size of about 130. Mu.m.
FIG. 5 is a graph showing the trend analysis of the prior austenite grain size in the casting slab along with the Mo/Nb/V/Zr total amount, and shows the different change behaviors of the surface, the radius 1/2 and the core of the casting slab and the refining effect of the alloyed casting slab structure.
Detailed Description
Bearing steels with different chemical compositions of 1 # to 4# are prepared in a laboratory by adopting vacuum induction smelting through composition design, and the specific compositions are shown in table 1. Smelting and die casting are carried out by a laboratory 50 kg holding induction furnace, and the industrial die casting or continuous casting of bearing steel is simulated to obtain an ingot with the diameter of 120 mm.
Table 1 steel example composition design (wt.%) of the balance Fe
| C | Si | Mn | Cr | Mo+Nb+V+Zr | Other elements | |
| GCr15-0.00 | 1.01 | 0.28 | 0.50 | 1.30 | 0.00 | Ni：1.0％ |
| GCr15-0.05 | 1.01 | 0.28 | 0.50 | 1.40 | 0.05 | Ni：1.0％ |
| GCr15-0.10 | 0.93 | 0.23 | 0.50 | 1.45 | 0.10 | Ni：1.0％ |
| GCr15-0.30 | 1.05 | 0.30 | 0.35 | 1.60 | 0.30 | La+Ce:0.05％ |
The microstructure of the four casting blanks was analyzed by optical microscopy. In the future, the influence of alloying on the structure of the casting blank is studied, and the surface of the casting blank, the 1/2 position of the radius of the casting blank and the structure characterization of the core structure of the casting blank are developed.
FIG. 1 shows the structure of a cast slab at a radius of 1/2 without Mo/Nb/V/Zr, and it can be seen that the average size of the prior austenite grains is 850 μm;
FIG. 2 shows the structure of a cast slab at a radius of 1/2 of the cast slab with a total Mo/Nb/V/Zr of 0.05%, and it can be seen that the average size of the prior austenite grains is 700 μm;
FIG. 3 shows the structure of a cast slab at a radius of 1/2 of the cast slab with a total Mo/Nb/V/Zr of 0.10%, and it can be seen that the average size of the prior austenite grains is 500 μm;
FIG. 4 shows the structure of a cast slab at a radius of 1/2 of the cast slab with a total Mo/Nb/V/Zr of 0.30%, and it can be seen that the average size of the prior austenite grains is 130 μm;
FIG. 5 shows the variation of the prior austenite size with Mo/Nb/V/Zr addition at the surface of the slab, at 1/2 of the slab radius and at the core of the slab. As can be seen, as the addition amount of Mo/Nb/V/Zr increases, the original austenite grains in the casting blank are gradually refined, and the refining effect of Mo/Nb/V/Zr addition on the casting blank structure is shown. Specifically, under the condition that Mo/Nb/V/Zr is not added, the original austenite grain size of the surface, the radius 1/2 and the core of the casting blank is 800-1000 microns; after 0.05% of the total Mo/Nb/V/Zr is added, the original austenite size on the surface is rapidly thinned to 350 microns, but the original austenite grain size at the center and the radius 1/2 is 600-700 microns, which shows that the 0.05% of Mo/Nb/V/Zr is not added enough to realize the thinning and homogenization of casting blank tissues under the die casting condition; after 0.10% of the total Mo/Nb/V/Zr is added, the original austenite size on the surface is rapidly thinned to 190 microns, but the original austenite grain size at the center and the radius 1/2 is about 500 microns, which indicates that 0.10% of Mo/Nb/V/Zr is added under the die casting condition, and the thinning and homogenization of the casting blank structure are not enough; after 0.30% of the total Mo/Nb/V/Zr is added, the original austenite size at the surface and radius 1/2 is rapidly thinned to 130 microns, and the original austenite grain size of the core is 200 microns, which shows that the 0.30% of Mo/Nb/V/Zr addition under the die casting condition realizes the thinning and homogenization of the casting blank structure.
Considering that the cooling speed of a laboratory simulated casting blank is relatively low, the industrialized continuous casting can be predicted to realize faster cooling, so that the full refinement of the casting blank tissue is realized under the condition that a large amount of Mo/Nb/V/Zr is not added. 0.10% Mo/Nb/V/Zr is recommended for alloying large-section casting blanks at higher cooling speeds of industrial continuous casting.
Claims (1)
1. A micro-alloyed bearing steel casting blank with fine and homogenized structure: the alloy is characterized in that C is 0.93-1.05%, si:0.20-0.50%, mn:0.20% -0.50%, cr:1.30-1.6%, S: less than or equal to 0.01 percent, P: less than or equal to 0.02 percent, cu: less than or equal to 0.25 percent, less than or equal to 0.30 percent of Mo, nb: less than or equal to 0.30 percent, V: less than or equal to 0.30 percent, zr:0 to 0.30 percent and Al less than or equal to 0.05 percent. On this basis, rare earth (Ce, la) may be added: less than or equal to 0.05 percent, ni: less than or equal to 1.0 percent; the balance being Fe;
smelting by a vacuum induction furnace or a converter, and then forming a casting blank by die casting or continuous casting, wherein the grain size of the prior austenite on the surface is less than or equal to 150 mu m, and the grain size of the prior austenite at the positions of the core and the radius 1/2 is less than or equal to 250 mu m.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20140099228A1 (en) * | 2011-05-25 | 2014-04-10 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Steel with excellent rolling-contact fatigue properties |
| CN105925909A (en) * | 2016-06-24 | 2016-09-07 | 邢台钢铁有限责任公司 | Bearing steel wire rod and production method thereof |
| CN112111696A (en) * | 2020-09-29 | 2020-12-22 | 钢铁研究总院 | High-carbon bearing steel with high isotropy and long contact fatigue life and manufacturing method thereof |
| CN113718174A (en) * | 2021-08-21 | 2021-11-30 | 钢铁研究总院 | Double-refined high-strength-toughness long-life medium-high carbon bearing steel and preparation method thereof |
| CN113862561A (en) * | 2021-09-08 | 2021-12-31 | 钢铁研究总院 | Long-life high-carbon bearing steel pipe and preparation method and application thereof |
| CN115612920A (en) * | 2022-08-29 | 2023-01-17 | 江阴兴澄特种钢铁有限公司 | Steel for flexible bearing of harmonic speed reducer of robot and production method thereof |
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2023
- 2023-04-27 CN CN202310472542.8A patent/CN116377333A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20140099228A1 (en) * | 2011-05-25 | 2014-04-10 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Steel with excellent rolling-contact fatigue properties |
| CN105925909A (en) * | 2016-06-24 | 2016-09-07 | 邢台钢铁有限责任公司 | Bearing steel wire rod and production method thereof |
| CN112111696A (en) * | 2020-09-29 | 2020-12-22 | 钢铁研究总院 | High-carbon bearing steel with high isotropy and long contact fatigue life and manufacturing method thereof |
| WO2022068856A1 (en) * | 2020-09-29 | 2022-04-07 | 钢铁研究总院 | High-carbon bearing steel having high isotropy and long contact fatigue life and manufacturing method |
| CN113718174A (en) * | 2021-08-21 | 2021-11-30 | 钢铁研究总院 | Double-refined high-strength-toughness long-life medium-high carbon bearing steel and preparation method thereof |
| CN113862561A (en) * | 2021-09-08 | 2021-12-31 | 钢铁研究总院 | Long-life high-carbon bearing steel pipe and preparation method and application thereof |
| CN115612920A (en) * | 2022-08-29 | 2023-01-17 | 江阴兴澄特种钢铁有限公司 | Steel for flexible bearing of harmonic speed reducer of robot and production method thereof |
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