HIGH-CARBON BEARING STEEL AND PREPARATION METHOD THEREOF

Abstract

The invention relates to the technical field of microstructure refinement and homogenization of bearing steel, and specifically relates to a high-carbon bearing steel and a method of preparing same. The high-carbon bearing steel of the invention has the following chemical composition: C: 0.80˜1.20 wt %, Cr: 0.40˜2.0 wt %, Mn: 0.15˜0.75 wt %, Si: 0.15˜0.75 wt %, Nb: 0˜0.20 wt %, Mo: 0˜0.20 wt %, V: 0˜0.20 wt %, P≤0.015 wt %, S≤0.01 wt %, the remaining is Fe and unavoidable impurities; the contents of Nb, Mo and V are not 0 at the same time. According to the invention, microalloying elements such as Nb, Mo and V, in combination with other elements, are added into the high-carbon bearing steel to effectively refine the bearing steel matrix and promote the precipitation of a large amount of nano-carbides, thereby enhancing the contact fatigue life of the high-carbon bearing steel.

Claims

1. A high-carbon bearing steel, wherein the chemical composition comprises: C: 0.80˜1.20 wt %, Cr: 0.40˜2.0 wt %, Mn: 0.15˜0.75 wt %, Si: 0.15˜0.75 wt %, Nb: 0˜0.20 wt %, Mo: 0˜0.20 wt %, V: 0˜0.20 wt %, P≤0.015 wt %, S≤0.01 wt %, the remaining is Fe and unavoidable impurities; wherein the composition comprises at least one of Nb, Mo and V.

2. The high-carbon bearing steel according to claim 1, wherein the high-carbon bearing steel comprises at least two of Nb, Mo and V.

3. The high-carbon bearing steel according to claim 1, wherein a total quantity of Nb, Mo and V is 0.10˜0.30 wt %.

4. The high-carbon bearing steel according to claim 2, wherein a total quantity of Nb, Mo and V is 0.10˜0.30 wt %.

5. A method of making the high-carbon bearing steel of claim 1, comprising the steps of: smelting raw materials of the high-carbon bearing steel to obtain steel ingots, wherein the steel ingots have a chemical composition corresponding to the chemical composition of the high-carbon bearing steel of claim 1; homogenizing the steel ingots and then processing them into bars; successively spheroidizing annealing, quenching, and tempering the bars to obtain the high-carbon bearing steel.

6. A method of making the high-carbon bearing steel of claim 2, comprising the steps of: smelting raw materials of the high-carbon bearing steel to obtain steel ingots, wherein the steel ingots have a chemical composition corresponding to the chemical composition of the high-carbon bearing steel of claim 2; homogenizing the steel ingots and then processing them into bars; successively spheroidizing annealing, quenching, and tempering the bars to obtain the high-carbon bearing steel.

7. A method of making the high-carbon bearing steel of claim 3, comprising the steps of: smelting raw materials of the high-carbon bearing steel to obtain steel ingots, wherein the steel ingots have a chemical composition corresponding to the chemical composition of the high-carbon bearing steel of claim 3; homogenizing the steel ingots and then processing them into bars; successively spheroidizing annealing, quenching, and tempering the bars to obtain the high-carbon bearing steel.

8. A method of making the high-carbon bearing steel of claim 4, comprising the steps of: smelting raw materials of the high-carbon bearing steel to obtain steel ingots, wherein the steel ingots have a chemical composition corresponding to the chemical composition of the high-carbon bearing steel of claim 4; homogenizing the steel ingots and then processing them into bars; successively spheroidizing annealing, quenching, and tempering the bars to obtain the high-carbon bearing steel.

9. The method according to claim 5, wherein the smelting is electro-slag remelting (ESR), double vacuum melting (VIM+VAR), out-of-furnace refining or vacuum induction melting.

10. The method according to claim 6, wherein the smelting is electro-slag remelting (ESR), double vacuum melting (VIM+VAR), out-of-furnace refining or vacuum induction melting.

11. The method according to claim 7, wherein the smelting is electro-slag remelting (ESR), double vacuum melting (VIM+VAR), out-of-furnace refining or vacuum induction melting.

12. The method according to claim 8, wherein the smelting is electro-slag remelting (ESR), double vacuum melting (VIM+VAR), out-of-furnace refining or vacuum induction melting.

13. The method according to claim 5, wherein the temperature for homogenization is 1100˜1250° C., and the holding time is 2˜6 hours.

14. The method according to claim 6, wherein the temperature for homogenization is 1100˜1250° C., and the holding time is 2˜6 hours.

15. The method according to claim 7, wherein the temperature for homogenization is 1100˜1250° C., and the holding time is 2˜6 hours.

16. The method according to claim 8, wherein the temperature for homogenization is 1100˜1250° C., and the holding time is 2˜6 hours.

17. The method according to claim 5, wherein the process of spheroidizing annealing comprises holding the bars at 800˜860° C. for 0.5˜12 hours, then cooling down to 680˜740° C. and holding for 0.5˜12 hours, and finally cooling in air to room temperature.

18. The method according to claim 5, wherein the temperature for quenching is 820˜860° C., the holding time is 0.10˜1.0 hours, and the cooling for quenching is oil quenching.

19. The method according to claim 5, wherein the temperature for tempering is 130˜200° C., the holding time is 0.5˜3.5 hours, and the cooling for tempering is air cooling.

20. The method according to claim 5, wherein the bars are processed by hot forging or hot rolling, and the temperature for hot forging or hot rolling is 1150˜1200° C.

Description

BRIEF DESCRIPTION OF THE DRAWING

[0022] The drawing shows an SEM diagram of steel MA5 smelted in the laboratory after tempering.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT(S)

[0023] The invention provides a high-carbon bearing steel, the chemical composition comprising C: 0.80˜1.20 wt %, Cr: 0.40˜2.0 wt %, Mn: 0.15˜0.75 wt %, Si: 0.15˜0.75 wt %, Nb: 0˜0.20 wt %, Mo: 0˜0.20 wt %, V: 0˜0.20 wt %, P≤0.015 wt %, S≤0.01 wt %, the remaining is Fe and unavoidable impurities, wherein the composition comprises at least one of Nb, Mo and V.

[0024] The high-carbon bearing steel of the invention comprising C: 0.80˜1.20 wt %, preferably 0.9˜1.1 wt %, and more preferably 0.95˜1.05 wt %.

[0025] The high-carbon bearing steel of the invention comprising Cr: 0.40˜2.0 wt %, preferably 0.5˜1.8 wt %, and more preferably 1.0˜1.6 wt %.

[0026] The high-carbon bearing steel of the invention comprising Mn: 0.15˜0.75 wt %, preferably 0.20˜0.60 wt %, and more preferably 0.3˜0.5 wt %.

[0027] The high-carbon bearing steel of the invention comprising Si: 0.15˜0.75 wt %, preferably 0.20˜0.70 wt %, and more preferably 0.30˜0.60 wt %.

[0028] The high-carbon bearing steel of the invention comprising P≤0.015 wt %, preferably 0.001˜0.015 wt %.

[0029] The high-carbon bearing steel of the invention comprising S≤0.01 wt %, preferably 0.001˜0.01 wt %.

[0030] The high-carbon bearing steel of the invention comprising Nb: 0˜0.20 wt %, preferably 0.03˜0.20 wt %, and more preferably 0.05˜0.15 wt %.

[0031] The high-carbon bearing steel of the invention comprising Mo: 0˜0.20 wt %, preferably 0.03˜0.20 wt %, and more preferably 0.05˜0.15 wt %.

[0032] The high-carbon bearing steel of the invention comprising V: 0˜0.20 wt %, preferably 0.03˜0.20 wt %, and more preferably 0.05˜0.10 wt %.

[0033] According to the invention, the contents of Nb, Mo and V are not 0 at the same time, i.e., the high-carbon bearing steel of the invention comprises at least one of Nb, Mo and V; the invention preferably comprises at least two of Nb, Mo and V. According to the invention, the total quantity of Nb, Mo and V is preferably 0.10˜0.30 wt %, more preferably 0.15˜0.30 wt %, and more preferably 0.25˜0.30 wt %.

[0034] According to the invention, microalloying elements such as Nb, Mo and V, in combination with other elements, are added into the high-carbon bearing steel to effectively refine the bearing steel matrix, refine the carbides in the bearing steel, and promote the precipitation of a large amount of nano-carbides, thereby enhancing the mechanical properties and the contact fatigue life of the high-carbon bearing steel.

[0035] The invention provides a method of preparing the high-carbon bearing steel in the above composition, comprising the following steps:

[0036] The preparation comprises smelting the raw materials of the high-carbon bearing steel to obtain steel ingots, wherein the steel ingots have a chemical composition corresponding to the chemical composition of the high-carbon bearing steel in the above composition.

[0037] The steel ingots are homogenized and then processed into bars.

[0038] The bars are successively subject to spheroidizing annealing, quenching, and tempering to obtain the high-carbon bearing steel.

[0039] According to the invention, preparation comprises smelting the raw materials of the high-carbon bearing steel to obtain steel ingots. According to the invention, the smelting preferably comprises electro-slag remelting (ESR), double vacuum melting (VIM+VAR), out-of-furnace refining or vacuum induction melting. The invention has no special requirement for the smelting process, any process that is well known in the art such as electro-slag remelting (ESR), double vacuum melting (VIM+VAR), out-of-furnace refining or vacuum induction melting, may be used. The smelting of the invention is suitable for a converter, an electric furnace, or an induction furnace. According to the invention, the chemical composition of the steel ingots corresponds to the chemical composition of the high-carbon bearing steel in the above composition. The invention has no special requirements on the types and sources of the various raw materials, as long as they meet the required ingredients of the steel ingots. According to the invention, smelting is carried out so that the oxygen content in the bearing steel is not higher than 20 ppm and the size of large granular inclusions (DS) is ≤40 microns.

[0040] According to the invention, after the steel ingots are obtained, they are homogenized and then processed into bars.

[0041] According to the invention, the temperature for homogenization is preferably about 1100˜1250° C., and more preferably about 1150˜1200° C.; the holding time is preferably about 2˜6 hours, and more preferably about 3˜5 hours. Upon the completion of homogenization, the resulting billet is processed into bars. According to the invention, the processing is preferably hot forging or hot rolling, and the temperature for hot forging or hot rolling is preferably about 1150˜1200° C. The invention has no special requirement on the size of the bars, as long as it is set according to the requirements on the bearing steel. In the examples of the invention, the size of the bars is 160 mm. According to the invention, the processed bars are preferably cooled in air to room temperature, and then subject to the subsequent steps.

[0042] According to the invention, after the bars are obtained, they are spheroidizing annealed to obtain the annealed bars.

[0043] According to the invention, the process of spheroidizing annealing preferably comprises the steps of holding the bars are at about 800˜860° C. for 0.5˜12 hours, then cooling down to about 680˜740° C. and holding for 0.5˜12 hours, and finally cooling in the air to room temperature. According to the invention, spheroidizing annealing is carried out to get uniform fine carbides.

[0044] According to the invention, after the annealed bars are obtained, they are quenched to obtain quenched bars. According to the invention, the temperature for quenching is preferably about 820˜860° C., and more preferably 840° C., the holding time is preferably 0.1˜1.0 hours, and more preferably 0.5 hours; the cooling for quenching is preferably oil quenching. The invention has no special requirement on the process of oil quenching, and any oil quenching well known in the art may be used.

[0045] According to the invention, after the quenched bars are obtained, they are tempered to get the high-carbon bearing steel. According to the invention, the temperature for tempering is preferably about 130˜200° C., and more preferably 170° C., the holding time is preferably 0.5˜3.5 hours, and more preferably 3 hours; the cooling for tempering is preferably air cooling. Quenching and tempering are employed in the invention so as to get ultrafine original austenite and carbide particles, wherein the grain size of the original austenite is not less than grade 10.

[0046] The high-carbon bearing steel of the invention and the preparation method thereof will be illustrated in detail below in combination with the following examples, which are not construed as a limitation on the protection scope of the invention.

Example 1

[0047] The steel of the invention is smelted in a laboratory vacuum induction melting furnace, and casted into round ingots of 50 kg. 10 furnaces of steel are totally smelted for forging into rod-like samples, with the chemical ingredients shown in Table 1. MA1-MA10 steel are the microalloying bearing steel of the invention; and C1-C3 are the bearing steel used as the control (wherein the preparation method of round ingots is: C1 is GCr15 smelted in a laboratory vacuum induction melting furnace, C2 is GCr15 refined out of the furnace, and C3 is double vacuum GCr15).

[0048] GCr15 round ingots smelted in a laboratory vacuum induction melting furnace are homogenized at a high temperature of 1200° C. for 5 hours for the subsequent forging-cogging. The initial forging temperature is 1150° C., the initial section size is 120 mm casting blank, which is radially forged into round bars with a section size of 60 mm, and then cooled in air. The round bars with a diameter of 60 mm are spheroidizing annealed (held at 820° C. for 6 hours, then cooled down to 720° C. and held for 6 hours, and finally cooled in air to room temperature), and then quenched (held at 840° C. for 0.5 hours, followed by oil quenching) and tempered at low temperature (held at 170° C. for 3 hours, followed by air cooling) to get the high-carbon bearing steel.

[0049] MA1-MA10 and C1-C3 were tested for their mechanical properties, impact toughness and contact fatigue life (Tensile test: the tensile rate is 10.sup.−4/s, and the elongation adopts A5; Impact test: the size for impacting samples is U-shaped impact of 10 mm×10 mm×55 mm; Contact fatigue test: a thrust plate test with a maximum Hertz stress of 4.5 GPa), with the results shown in Table 2.

TABLE-US-00001 TABLE 1 Chemical compositions of steel of the invention and traditional steel ( wt %) C Cr Si Mn S P Mo Nb V Steel of the MA1 0.80 0.4 0.75 0.75 0.010 0.010 — — 0.05 invention MA2 0.91 0.8 0.58 0.64 0.010 0.015 — 0.05 — MA3 0.95 1.42 0.55 0.60 0.010 0.015 0.05 — 0.15 MA4 0.95 1.41 0.30 0.35 0.010 0.015 0.02 0.08 — MA5 1.00 1.52 0.30 0.30 0.005 0.010 0.10 0.10 — MA6 1.01 1.52 0.30 0.35 0.005 0.010 0.20 MA7 1.02 1.48 0.25 0.25 0.005 0.005 0.05 0.20 — MA8 1.12 1.80 0.30 0.35 0.004 0.010 0.10 0.15 0.05 MA9 1.20 2.00 0.15 0.15 0.010 0.015 0.20 0.05 0.10 MA10 1.20 1.51 0.36 0.29 0.005 0.010 0.09 Comparative C1 1.02 1.48 0.35 0.38 0.005 0.005 — — — steel C2 1.00 1.41 0.30 0.35 0.005 0.010 — — — C3 0.80 1.48 0.36 0.41 0.010 0.015 — — —

TABLE-US-00002 TABLE 2 Results of mechanical properties and fatigue performances of the steel of the invention and the comparative steel Rm A5 Aku L.sub.10 (MPa) (%) (J) (10.sup.7 times) Steel of the MA1 2450 4.5 16.0 ≥2.8 invention MA2 2520 4.3 13.0 ≥2.1 MA3 2490 3.0 12.0 ≥4.5 MA4 2510 3.9 11.0 ≥6.5 MA5 2570 4.2 11.0 ≥10 MA6 2590 5.0 12 ≥4.7 MA7 2530 3.8 10.5 ≥8.2 MA8 2510 3.3 10.0 ≥10 MA9 2493 3.0 8.9 ≥4.3 MA10 2430 2.0 8.5 ≥2.7 Comparative C1 2230 1.5 7.0 ≥0.7 steel C2 2380 1.5 4.8 ≥1.0 C3 2460 2.0 5.6 ≥>4.5

[0050] As seen in Table 2, microalloying of Nb, V and Mo greatly enhances the tensile strength (Rm), the elongation (A5) and the impact toughness (Aku) of bearing steel. This is mainly attributable to the ultrafine matrix and the ultrafine size of carbides. As shown in FIG. 1, a large amount of carbides are finely and uniformly distributed in the high-carbon bearing steel, and the average size of carbides is 0.28 microns, which is finer than the carbides of traditional GCr15 by about 1 time. At the same time, due to the microstructure refinement and enhanced mechanical properties for the steel of the invention, the contact fatigue life L.sub.10 of microalloying bearing steel is enhanced by 3˜14 times compared to L.sub.10 of laboratory smelted bearing steel without microalloying (C1). Meanwhile, compared to the contact fatigue life of industrialized out-of-furnace refined steel GCr15 (C2) and double vacuum GCr15 (C3), it is also enhanced significantly. For example, compared to out-of-furnace refined GCr15, the fatigue life is enhanced by 2˜10 times; and compared to double vacuum GCr15, the fatigue life also reaches 0.5˜2.2 times. At the same time, it can be found from the comparison between Table 1 and Table 2 that when the total quantity of the compound microalloying is in a range of 0.10˜0.30%, the contact fatigue performance can be enhanced better. The characteristics of low cost and long life for the steel of the invention will greatly improve the service life and reliability of high-end equipment, thus having huge market application potentials in aerospace, mining machinery, transportation, marine ships, and other fields.

[0051] The foregoing is only preferable implementation of the invention. It should be noted to persons with ordinary skills in the art that several improvements and modifications can be made without deviating from the principle of the invention, which are also considered within the scope of the invention.