CN115747645B - Steel for high-strength high-contact fatigue high-power wind power yaw bearing ring, bearing ring and production process - Google Patents
Steel for high-strength high-contact fatigue high-power wind power yaw bearing ring, bearing ring and production process Download PDFInfo
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E10/00—Energy generation through renewable energy sources
- Y02E10/70—Wind energy
- Y02E10/72—Wind turbines with rotation axis in wind direction
Abstract
The invention discloses steel for a high-strength high-contact fatigue high-power wind power yaw bearing ring, a bearing ring and a production process, and belongs to the field of alloy steel. The invention simultaneously adjusts the heat treatment process parameters by controlling the chemical component proportion, wherein the heat treatment process parameters are in accordance with: 1) Normalizing, S-T 1/20≤t1≤S-T1/80; 2) Tempering: quenching, S-T 2/10≤t2≤S-T2/50; tempering, namely 1.5 xS-T 3/10≤t3≤1.5×S-T3/50, wherein the tensile strength of the 1/2 wall thickness (the wall thickness is more than or equal to 300 mm) of the prepared bearing ring is more than or equal to 950MPa, the yield strength is more than or equal to 850MPa, and the KV 2 at minus 40 ℃ is more than or equal to 120J; under the action of 2000MPa contact stress, the contact fatigue life is more than or equal to 110 ten thousand times, and the requirement of 20 years of high-power wind power service is met.
Description
Technical Field
The invention belongs to the field of alloy steel, and particularly relates to steel for a high-strength high-contact fatigue high-power wind power yaw bearing ring, a bearing ring and a production process.
Background
The wind power is enlarged to cause the size of a wind power key component bearing to be increased, and according to investigation, the outer diameter of a 1.5MW wind power yaw bearing ring is about 2.1m, and the outer diameter of a 6MW wind power yaw bearing ring is up to 4.5 m, and the outer diameter is enlarged by 2.1 times. In addition, the size of the bearing is increased, the wall thickness of the bearing ring is increased, and the uniformity of the section performance of the bearing ring is poor, so that the requirements of the high-power wind power bearing ring on the toughness and uniformity are increased. JB/T10705 also indicates that "materials with comparable or better performance can be used to manufacture wind power yaw bearing rings". The development of the ocean wind power in China is rapid, but the current development is generally lower than 6MW, and the key equipment materials cannot be completely self-supplied. Therefore, development of steel for a high-power ocean wind power yaw bearing ring is urgent.
Patent CN 101230441A indicates that wind power yaw and pitch bearing rings are manufactured by 42CrMoVNb steel, V-shaped impact energy of the material at minus 40 ℃ is more than or equal to 91J, and tensile strength is more than or equal to 835MPa. However, the patent does not describe the power of the steel applied to the wind power bearing ring, the performance value is inferred to be applicable to wind power generation sets below 3MW, and the performance of the material is not clear whether the real anatomical value of the bearing ring or the small sample test value is adopted.
Patent CN 104178695A discloses that a wind power bearing ring is manufactured by adopting medium carbon boron microalloyed steel, the tensile strength of the wind power bearing ring is more than or equal to 1090MPa, and V-shaped impact energy at minus 20 ℃ is more than or equal to 29J after heat treatment. The material of the invention has low overall toughness, the heat treatment quenching heat preservation time is 50-130min, the thickness of the produced bearing ring is thinner, and the requirement of the thick-wall performance of the high-power wind power bearing ring can not be met. The fatigue performance and the like of the marine wind power bearing are not tested and evaluated, and the application support of the marine wind power bearing on the material is insufficient.
Disclosure of Invention
1. Problems to be solved
Aiming at the problem that the existing large-size wind power bearing ring is poor in toughness and contact fatigue resistance, the invention provides the steel for the high-strength high-contact fatigue high-power wind power yaw bearing ring, the bearing ring and the production process, and the manufactured bearing ring is high in toughness and contact fatigue resistance.
2. Technical proposal
In order to solve the problems, the technical scheme adopted by the invention is as follows:
The invention discloses steel for a high-strength high-contact fatigue high-power wind power yaw bearing ring, which comprises the following components in percentage by weight:
C 0.47%～0.57%、Si 0.40%～0.70%、Mn 1.30%～1.50%、Cr 0.50%～0.70%、Mo 0.35%～0.45%、Ni 0.25%～0.35%、Cu 0.030%～0.050%、V 0.035%～0.075%、Ti 0.0040%～0.0060%、Al 0.015%~0.025%、P ≤0.015%、S≤0.010%、N 0.0060%～0.0120%、B 0.0020%～0.0040%、O≤0.0040%, The balance of Fe and other unavoidable impurities, and the proportion of each chemical component accords with:
1） 13.0%≤(0.54×C%)×(1+3.34×Mn%)×(1+0.7×Si%)×(1.2+0.36×Cu%)×(1+0.37×Ni%)
×(1+2.61×Cr%)×(1+3×Mo%)×(1+0.6×V%)×(1+Ti%+N%)≤19.0%；
2） 0.55%≤C%+(Mn%+10×N%+15×B%)/6-(Cr%+Mo%+V%+Ti%)/5+(Ni%+Cu%)/15
≤0.62%。
the heat treatment process parameters should be in accordance with:
1) Normalizing, wherein T 1 (DEG C) is the normalizing heating temperature, 1000-1100 ℃, T 1 (min) is the heat preservation time, and S (mm) is the wall thickness of the bearing ring;
2) Tempering: quenching, wherein T 2 (DEG C) is the quenching heating temperature of 800-900 ℃, T 2 (min) is the quenching heat preservation time, and S (mm) is the bearing ring wall thickness;
Tempering, 1.5 xS-T 3/10≤t3≤1.5×S-T3/50, wherein T 3 (DEG C) is normalizing heating temperature, 600-700 ℃, T 3 (min) is heat preservation time, and S (mm) is bearing ring wall thickness.
The invention provides a heat treatment method of the steel, and the prepared steel has excellent toughness and contact fatigue performance, and is suitable for manufacturing a yaw bearing (the thickness of the shaft collar is more than or equal to 300 mm) for high-power wind power. The invention also discloses a process for producing the bearing ring by using the steel.
C: c is the least expensive strengthening element in the steel, and each 0.1% of solid solution C can improve the strength by about 450MPa, and the C and the alloy element in the steel form a precipitated phase to play a role in precipitation strengthening. And C, the hardenability can be obviously improved, so that the large-wall-thickness periodic ring part can obtain a martensitic structure. However, as the content increases, the plasticity and toughness decrease, so the C content is controlled to be 0.47-0.57%.
Si: si is an effective solid solution strengthening element in steel, improves the strength and the hardness of the steel, can play a deoxidizing role in steelmaking, and is a common deoxidizer. However, si tends to be biased to have austenite grain boundaries, so that the bonding force of the grain boundaries is reduced, and brittleness is induced. In addition, si tends to cause element segregation in steel. Therefore, the Si content is controlled to be 0.40% to 0.70%.
Mn: mn can play a solid solution strengthening role, the solid solution strengthening capability is weaker than that of Si, mn is an austenite stabilizing element, the hardenability of steel can be obviously improved, decarburization of steel can be reduced, and the combination of Mn and S can prevent hot shortness caused by S. However, excessive Mn reduces the plasticity of the steel. Therefore, the Mn content is controlled to be 1.30-1.50%.
Cr: cr is a carbide forming element, and Cr can improve both hardenability and strength of steel, but is liable to cause temper embrittlement. Cr can improve the oxidation resistance and corrosion resistance of steel, but when the Cr content is too high, crack sensitivity is increased. The Cr content should be controlled to be 0.50% -0.70%.
Mo: mo mainly improves the hardenability and heat resistance of steel, mo solid-dissolved in a matrix can keep higher stability of a steel structure in the tempering process, and can effectively reduce the segregation of P, S, as and other impurity elements at a grain boundary, so that the toughness of the steel is improved, and the tempering brittleness is reduced. Mo can decrease the stability of M 7C3, and when the Mo content is higher, needle Mo 2 C will be formed, which will result in a decrease in the Mo content of the matrix. Mo can improve the strength of steel by the combined action of solid solution strengthening and precipitation strengthening, and can also change the toughness of steel by changing the precipitation of carbide. So the Mo is controlled to be 0.35-0.45%.
Ni: ni can form infinite mutual-soluble solid solution with Fe, is an austenite stabilizing element, has the effect of expanding a phase area, increases the stability of supercooled austenite, makes a C curve move right, and improves the hardenability of steel. Ni can refine the width of the martensite lath and improve the strength. Ni can obviously reduce the ductile-brittle transition temperature of steel and improve the low-temperature toughness. However, ni element is a noble metal element, and excessive addition results in excessive cost. The Ni content is controlled to be 0.25-0.35%.
V: v is a strong C, N compound forming element, and V (C, N) forms fine dispersion and maintains a coherent relation with the matrix, so that the effects of strengthening and refining tissues can be achieved. The V content is controlled to be 0.035-0.075%.
Ti: ti has wide effect in steel, ti can be used as deoxidizer for deoxidization, ti, C and N can form carbon nitrogen compound, and is separated out in steel to play a role in precipitation strengthening, and grain boundary can be pinned to prevent grain growth. The Ti content is controlled to be 0.0040-0.0060%.
Cu: cu can enlarge an austenite phase region, and a Cu simple substance serving as a second phase can remarkably improve strength and improve the tempering stability and strength of a structure. However, too high Cu will result in Cu embrittlement. Therefore, the Cu content is controlled to be 0.030-0.050%.
Al: al is a main deoxidizer for steelmaking, al and N are combined to form tiny dispersion-distributed AlN, and the tiny dispersion-distributed AlN and a matrix are kept in a coherent relation, so that the effects of strengthening and refining tissues can be achieved, fatigue crack initiation and expansion resistance can be increased, and the durability of the steel is improved. The Al content is controlled to be 0.015% -0.035%.
B: b is an element with smaller atomic size, and is easy to interact with crystal lattices of carbon element in steel, so that the crystal lattices of the steel are distorted, the martensite acquisition capacity of the steel is improved, and the toughness and fatigue performance of the large-size wind power bearing core can be improved by adding B. However, too much B content can cause B to be concentrated at interfaces (grain boundaries, phase boundaries and the like), and the interfacial binding force is reduced to cause brittle fracture. Therefore, the content of B is limited to 0.0020 to 0.0040%.
O and N: T.O forms oxide inclusion in steel, and the T.O is controlled to be less than or equal to 0.0040 percent; n can form nitride in steel to form fine precipitated phase refined structure, fe 4 N can be precipitated, the diffusion speed is low, the timeliness of the steel is caused, and the processing performance is reduced, so that the N is controlled to be 0.0060% -0.0120%.
The high-power wind power yaw bearing has large size and needs to ensure enough strength and toughness. The hardenability can be effectively improved by adding the alloy elements, so that the toughness is improved.
The invention improves the strength and toughness of the steel by adding the microalloy V and Ti and combining B and N together. The Ti element is a stronger carbon nitrogen compound element, can pin grain boundary refinement grains, improves the toughness, and the carbon nitrogen compound formed by Ti has a more standard cube structure, forms a semi-coherent or coherent structure with a steel matrix, has good binding force and high fusion degree, is favorable for improving the toughness of the steel, but has high hardness, is favorable for improving the wear resistance of the material, but has the risk of falling hard substances, and reduces the contact fatigue performance. In order to exert the beneficial effects of Ti and eliminate the harmful effects of Ti, the content of Ti is limited on one hand, and the size of Ti compounds is regulated and controlled through a heat treatment process on the other hand, so that the sizes of Ti compounds are fine, thereby avoiding large-particle hard phases and reducing the adverse effects on contact fatigue performance. The main action mechanism is that V and Ti can form carbon nitrogen compound with C and N, the formed carbon nitrogen compound is finely dispersed and distributed in steel, dislocation passing resistance can be increased, toughness is improved, and meanwhile, the carbon nitrogen compound can be pinned to grain boundaries to block grain boundary migration, refine grains and improve toughness and fatigue performance. Secondly, the atomic size of the B element is small and is similar to the mass fraction and the electronic structure of the carbon element in the steel, the interaction with C is extremely easy to form in the steel to cause lattice change, and the capacity of the steel to obtain a martensitic structure is improved, so that the toughness of the large-size bearing core part is improved, and the total content of N+B is between 0.0080 and 0.016 percent by limiting the content of N and B, so that the combination of the N+B and V and Ti is ensured, the synergistic exertion of the beneficial effects of the elements is promoted, and the toughness and the fatigue performance of the steel are comprehensively improved.
Through researches, mn in alloy elements is most effective in improving hardenability and strength, and the coefficient is 3.34; mo contributes significantly to hardenability and strength by improving tempering stability and interaction with Mn, and has a coefficient of 3.0; cr is a main substitutional solid solution element, and the contribution coefficient of carbide forming elements to strength is 2.16; ni and Cu do not form carbide in steel, and the hardenability and strength of the steel are improved by changing the crystal lattice morphology through solid solution strengthening, and the coefficients are 0.37 and 0.36 respectively; c is a nonmetallic element, is the most main interstitial solid solution strengthening element in steel, has influence on strength and toughness, and has a coefficient of 0.54; si is a nonmetallic element and is also a main solid solution strengthening element in steel, and contributes 0.70 to the performance of steel. Because the strength and the plasticity and the toughness of the steel have inverse proportion relation, namely the plasticity and the toughness can be reduced when the strength is high, the strength can not be improved at the same time in order to ensure the comprehensive performance of the steel. The strengthening factors in the steel are expressed by A, the A is more than or equal to 13.0% and less than or equal to 19.0%,
A=(0.54×C%)×(1+3.34×Mn%)×(1+0.7×Si%)×(1.2+0.36×Cu%)×(1+0.37×Ni%)
×(1+2.61×Cr%)×(1+3×Mo%)×(1+0.6×V%)×(1+Ti%+N%)。
The bearing needs better contact fatigue performance in the service process, so that the proportion of C, mn, cr, mo, ni, cu, V is limited. The C, mn, N, B can remarkably improve the hardness of the steel shallow layer and the wear resistance so as to improve the contact fatigue performance; cr, mo and V can form a second phase with C, N in steel, and the second phase can increase strength in steel, but is still different from a steel matrix, and if the size is large, a contact fatigue crack source can be formed, so that the contact fatigue is unfavorable; the combination of Ni and Cu with the matrix through solid solution strengthening is beneficial to the contact fatigue performance, so that the contact fatigue factor in the steel is expressed by Y, Y is more than or equal to 0.55% and less than or equal to 0.62%,
Y=C%+(Mn%+10×N%+15×B%)/6-(Cr%+Mo%+V%+Ti%)/5+(Ni%+Cu%)/15。
The invention also discloses a production process of the steel for the yaw bearing ring and the yaw bearing ring: smelting in an electric arc furnace or a converter, refining in an LF furnace, vacuum degassing in RH or VD, continuous casting of round billets with the diameter of 380mm to 700mm, heating of round billets, forging, punching, ring rolling (semi-finished product), heat treatment, machining, flaw detection, packaging and warehousing.
The yaw bearing ring adopts normalizing and tempering heat treatment, and the heat treatment process is as follows:
Normalizing: the temperature of the yaw bearing ring semi-finished product after ring rolling is less than or equal to 600 ℃, the normalizing heating temperature (T 1, DEG C) is 1000-1100 ℃, the normalizing heat preservation time (T 1, min) is determined by the wall thickness (S, mm) of the bearing ring and the normalizing heating temperature (T 1, DEG C), and the requirements of S-T 1/20≤t1≤S-T1/80 are met, and water cooling is realized.
Tempering: the quenching heating temperature (T 2, DEG C) is 800-900 ℃, the quenching heat preservation time (T 2, min) is determined by the wall thickness (S, mm) of the bearing ring and the quenching heating temperature (T 2, DEG C), the S-T 2/10≤t2≤S-T2/50 is satisfied, and the water cooling is carried out; the tempering temperature (T 3, DEG C) is 600-700 ℃, the tempering heat preservation time (T 3, min) is determined by the wall thickness (S, mm) of the bearing ring and the tempering temperature (T 3, DEG C), and the water cooling is realized, wherein the tempering temperature (T 3, DEG C) is 1.5 XS-T 3/10≤t3≤1.5×S-T3/50.
The austenite transformation point is affected by the components, the normalizing temperature and the tempering temperature are determined by the austenite transformation point, and the tempering temperature is selected by the type, the content and the size of the required precipitated phase.
The normalizing heating temperature is controlled to 900-1000 ℃, so that the bearing ring is ensured to be completely austenitized at the temperature, the heating temperature is controlled to be not higher than 1000 ℃, and the size of a second phase precipitated in the forging process of steel is ensured not to be too large, thereby being beneficial to improving the toughness of subsequent products, and being capable of preparing tissues for subsequent tempering after normalizing.
The tempering treatment is carried out at a heating temperature of 800-900 ℃, on one hand, the temperature is ensured to be higher than the austenitizing temperature, the steel is recrystallized on the basis of normalizing, and the grains are further refined; on the other hand, the size of the MX type precipitated phase generated in normalizing is ensured not to be coarse in the hardening and tempering process, thereby being beneficial to improving the toughness and the fatigue performance. The tempering temperature of 600-700 ℃ is adopted, the size of the precipitated phase is controlled while the type of the precipitated phase is ensured, so that the main precipitated phases in the steel are M 23C6 and MX type, and the toughness and fatigue performance are improved.
The tensile strength of the 1/2 wall thickness (the wall thickness is more than or equal to 300 mm) of the prepared bearing ring is more than or equal to 950MPa, the yield strength is more than or equal to 850MPa, and the KV 2 at minus 40 ℃ is more than or equal to 120J; under the action of 2000MPa contact stress, the contact fatigue life is more than or equal to 110 ten thousand times, and the requirement of 20 years of high-power wind power service is met.
3. Advantageous effects
Compared with the prior art, the invention has the beneficial effects that:
The steel for the high-strength high-contact fatigue high-power wind power yaw bearing ring has good toughness and contact fatigue resistance, and the tensile strength of the 1/2 wall thickness (the wall thickness is more than or equal to 300 mm) of the prepared bearing ring is more than or equal to 950MPa, the yield strength is more than or equal to 850MPa and the KV 2 at minus 40 ℃ is more than or equal to 120J; under the action of 2000MPa contact stress, the contact fatigue life is more than or equal to 110 ten thousand times, and the requirement of 20 years of high-power wind power service is met.
Drawings
The technical solution of the present invention will be described in further detail below with reference to the accompanying drawings and examples, but it should be understood that these drawings are designed for the purpose of illustration only and thus are not limiting the scope of the present invention. Moreover, unless specifically indicated otherwise, the drawings are intended to conceptually illustrate the structural configurations described herein and are not necessarily drawn to scale.
FIG. 1 is a diagram showing the structure of a bearing ring surface layer at 12.5mm after quenching in example 2 of the present invention;
FIG. 2 is a diagram showing the structure of the 12.5mm surface layer of the bearing ring after quenching in comparative example 2 of the present invention;
FIG. 3 is a microstructure of 1/2 wall thickness of a bearing ring according to example 2 of the present invention;
FIG. 4 is a microstructure of the invention at 1/2 wall thickness of the bearing ring of comparative example 2;
FIG. 5 is a graph showing transmission analysis at 1/2 thickness of the bearing ring according to example 2 of the present invention;
FIG. 6 is a graph of transmission analysis of a comparative example 2 bearing ring of the present invention at 1/2 thickness.
Detailed Description
The following detailed description of exemplary embodiments of the invention refers to the accompanying drawings, which form a part hereof, and in which are shown by way of illustration exemplary embodiments in which the invention may be practiced. While these exemplary embodiments are described in sufficient detail to enable those skilled in the art to practice the invention, it is to be understood that other embodiments may be realized and that various changes to the invention may be made without departing from the spirit and scope of the invention. The following more detailed description of the embodiments of the invention is not intended to limit the scope of the invention, as claimed, but is merely illustrative and not limiting of the invention's features and characteristics in order to set forth the best mode of carrying out the invention and to sufficiently enable those skilled in the art to practice the invention. Accordingly, the scope of the invention is limited only by the attached claims.
The invention discloses steel for a high-strength high-contact fatigue high-power wind power yaw bearing ring, which comprises the following components in percentage by weight:
C 0.47%～0.57%、Si 0.40%～0.70%、Mn 1.30%～1.50%、Cr 0.50%～0.70%、Mo 0.35%～0.45%、Ni 0.25%～0.35%、Cu 0.030%～0.050%、V 0.035%～0.075%、Ti 0.0040%～0.0060%、Al 0.015%~0.025%、P ≤0.015%、S≤0.010%、N 0.0060%～0.0120%、B 0.0020%～0.0040%、O≤0.0040%, The balance of Fe and other unavoidable impurities, and the proportion of each chemical component accords with:
1） 13.0%≤(0.54×C%)×(1+3.34×Mn%)×(1+0.7×Si%)×(1.2+0.36×Cu%)×(1+0.37×Ni%)
×(1+2.61×Cr%)×(1+3×Mo%)×(1+0.6×V%)×(1+Ti%+N%)≤19.0%；
2） 0.55%≤C%+(Mn%+10×N%+15×B%)/6-(Cr%+Mo%+V%+Ti%)/5+(Ni%+Cu%)/15
≤0.62%。
the heat treatment process parameters should be in accordance with:
1) Normalizing, wherein T 1 (DEG C) is the normalizing heating temperature, 1000-1100 ℃, T 1 (min) is the heat preservation time, and S (mm) is the wall thickness of the bearing ring;
2) Tempering: quenching, wherein T 2 (DEG C) is the quenching heating temperature of 800-900 ℃, T 2 (min) is the quenching heat preservation time, and S (mm) is the bearing ring wall thickness;
Tempering, 1.5 xS-T 3/10≤t3≤1.5×S-T3/50, wherein T 3 (DEG C) is normalizing heating temperature, 600-700 ℃, T 3 (min) is heat preservation time, and S (mm) is bearing ring wall thickness.
The invention provides a heat treatment method of the steel, and the prepared steel has excellent toughness and contact fatigue performance, and is suitable for manufacturing a yaw bearing (the thickness of the shaft collar is more than or equal to 300 mm) for high-power wind power. The invention also discloses a process for producing the bearing ring by using the steel.
The invention adopts steel types with specific components, and the components of the steel types of the examples and the comparative examples are shown in table 1.
TABLE 1 chemical composition (wt%) of the examples of the invention
| Steel grade | Example 1 | Example 2 | Example 3 | Comparative example 1 | Comparative example 2 | Comparative example 3 |
| C | 0.49 | 0.51 | 0.55 | 0.54 | 0.52 | 0.48 |
| Si | 0.53 | 0.48 | 0.55 | 0.65 | 0.59 | 0.49 |
| Mn | 1.35 | 1.41 | 1.46 | 1.48 | 1.43 | 1.32 |
| Cr | 0.55 | 0.51 | 0.63 | 0.65 | 0.53 | 0.59 |
| Ni | 0.28 | 0.33 | 0.31 | 0.32 | 0.26 | 0.31 |
| Mo | 0.38 | 0.39 | 0.42 | 0.44 | 0.38 | 0.41 |
| V | 0.042 | 0.054 | 0.071 | 0.065 | 0.039 | 0.072 |
| Ti | 0.0043 | 0.0057 | 0.0056 | 0.0055 | 0.0044 | 0.0054 |
| Cu | 0.035 | 0.042 | 0.038 | 0.045 | 0.038 | 0.049 |
| Al | 0.019 | 0.02 | 0.023 | 0.023 | 0.018 | 0.021 |
| P | 0.009 | 0.013 | 0.01 | 0.012 | 0.008 | 0.007 |
| S | 0.009 | 0.007 | 0.009 | 0.002 | 0.004 | 0.005 |
| N | 0.0062 | 0.0076 | 0.0105 | 0.0084 | 0.0097 | 0.0114 |
| B | 0.0025 | 0.0035 | 0.0022 | 0.0025 | 0.0028 | 0.0032 |
| O | 0.0036 | 0.0031 | 0.0029 | 0.0032 | 0.0026 | 0.0032 |
| A value | 13.14 | 13.9 | 18.69 | 20.4 | 14.73 | 13.97 |
| Y value | 0.56 | 0.6 | 0.61 | 0.6 | 0.61 | 0.54 |
The production process of the steel of the invention is as follows:
smelting in an electric furnace: oxygen is fixed before tapping, and steel retaining operation is adopted in the tapping process, so that slag discharging is avoided;
LF furnace: adjusting C, si, mn, cr, ni, mo, V, ti, cu and other elements to target values;
Vacuum degassing: the pure degassing time is more than or equal to 15 minutes, the H content after vacuum treatment is less than or equal to 1.5ppm, and the phenomenon of hydrogen embrittlement caused by white spots in steel is avoided;
continuous casting: controlling the target temperature of the ladle molten steel to be 10-40 ℃ above the liquidus temperature, and continuously casting 380mm~/>700Mm round billet.
The manufacturing route of the bearing ring comprises the following steps: heating round blank (diameter 600 and 700 mm), forging, punching and ring rolling (semi-finished product).
Heat treatment of the bearing rings: heating the trolley furnace, preserving heat, normalizing, quenching, tempering, preserving heat and water cooling.
The bearing ring processing route is as follows: rough turning of a bearing ring, flaw detection, finish turning of a valve body, grinding, flaw detection, packaging and warehousing.
The performance detection method comprises the following steps:
tissue: samples were taken from the bearing ring extension at 12.5mm and 1/2 thickness (300 mm thickness) of the surface layer of the extension for metallographic and grain size analysis.
Performance: samples were taken from the bearing ring extension body, and tensile, impact and contact fatigue samples were taken from the extension body at the position of 12.5mm and 1/2 thickness (300 mm thickness) of the surface layer, and mechanical property tests were performed with reference to GB/T228, GB/T229 and JB/T10510. The heat treatment process is shown in Table 2, and the mechanical properties are shown in Table 3. Wherein, R m is tensile strength, R p0.2 is yield strength, and the contact fatigue life is measured under the action of 2000MPa contact stress.
Table 2 list of forging process conditions for examples and comparative examples of the present invention
TABLE 3 fatigue Property test case List for examples and comparative examples of the present invention
The chemical composition and production method of the steel in examples 1-3 are properly controlled, and the chemical composition ensures that the strength, the plasticity, the toughness and the contact fatigue performance of the steel with the A content of 13.0 percent or more and the Y content of 0.55 percent or less and 0.62 percent or less are all better. The chemical components in the comparative examples 1 and 3 are unsuitable, the chemical components in the comparative example 3 are controlled improperly, the strength of the material is too low, the toughness is insufficient, and the overall performance is not ideal due to improper heat treatment process; comparative example 2 has reasonable design of components, but the heat treatment process is improper, so that the strength and toughness of the material are insufficient, and the contact fatigue resistance is insufficient.
In reasonable component proportion and heat treatment process, the steel structure for the high-power wind power yaw bearing ring is uniform and tiny, ferrite is not generated, as shown in fig. 1 and 2, fig. 1 is a structure diagram of a 12.5mm position of a surface layer of the bearing ring after quenching in embodiment 2 of the invention, and is full martensite, and is full sorbite after tempering, fig. 2 is a structure diagram of a 12.5mm position of a surface layer of the bearing ring after quenching in comparative example 2, 9% ferrite exists, on one hand, the strength of the material is reduced, on the other hand, the bonding force between the ferrite and the tempered sorbite is poor, and when the steel structure is subjected to external force, the steel structure is easy to break at a bonding interface and the toughness is reduced. Ferrite is used as soft particles, and is easy to deform during contact fatigue test, so that soft points are generated, fatigue is generated at the soft points, and fatigue performance is reduced.
Fig. 3 and 4 are microstructure diagrams of the 1/2 wall thickness of the bearing rings of example 2 and comparative example 2, respectively, and it is understood that the crystal grains of example 2 at the 1/2 wall thickness are fine and uniform, while the crystal grains of comparative example 2 at the 1/2 wall thickness have larger individual crystal grains and uneven crystal grain sizes. The uneven grain size can cause that the material is deformed incongruously by external force, and is easy to break at the large grain, so that the toughness of the material is reduced. And the grain size of the large grains is too large, so that the interface force combination degree is reduced, the effect is generated at the interface in the contact fatigue test process, and the fatigue performance is reduced.
Fig. 5 and 6 are transmission analysis diagrams of the thickness of the 1/2 bearing ring of example 2 and the thickness of the 1/2 bearing ring of comparative example 2 respectively, and by comparison, the precipitated phases of the 1/2 bearing ring of example 2 are finely distributed in the battens, the precipitated phases of comparative example 2 are distributed in the battens and among the battens in a large-scale manner, the precipitated phases in the steel can be influenced by controlling the composition and the process, the precipitated phases of the steel types are fine by controlling the process, the precipitated phases with large size are avoided, and the fatigue performance of the material is improved.
Claims (3)
1. The high-strength high-contact fatigue high-power steel for the wind power yaw bearing ring is characterized by comprising ：C 0.47%～0.57%、Si 0.40%～0.70%、Mn 1.30%～1.50%、Cr 0.50%～0.70%、Mo 0.35%～0.45%、Ni 0.25%～0.35%、Cu 0.030%～0.050%、V 0.035%～0.075%、Ti 0.0040%～0.0060%、Al 0.015%~0.025%、P ≤0.015%、S≤0.010%、N 0.0060%～0.0120%、B 0.0020%～0.0040%、O≤0.0040%, of Fe and other unavoidable impurities in percentage by weight, wherein the proportion of each chemical component is as follows:
1）13.0%≤(0.54×C%)×(1+3.34×Mn%)×(1+0.7×Si%)×(1.2+0.36×Cu%)×(1+0.37×Ni%)
×(1+2.61×Cr%)×(1+3×Mo%)×(1+0.6×V%)×(1+Ti%+N%)≤19.0%；
2）0.55%≤C%+(Mn%+10×N%+15×B%)/6-(Cr%+Mo%+V%+Ti%)/5+(Ni%+Cu%)/15
≤0.62%；
The wall thickness of the bearing ring is more than or equal to 300mm, the tensile strength of the 1/2 wall thickness part of the bearing ring is more than or equal to 950MPa, the yield strength is more than or equal to 850MPa, and the KV2 at minus 40 ℃ is more than or equal to 120J; under the action of 2000MPa contact stress, the contact fatigue life is more than or equal to 110 ten thousand times.
2. A process for producing a bearing ring from the steel for a high strength and toughness high contact fatigue high power wind power yaw bearing ring of claim 1, comprising: smelting in an arc furnace or a converter, refining in an LF furnace, vacuum degassing in RH or VD, continuous casting of round billets, heating of round billets, forging, punching, ring rolling, heat treatment, machining, flaw detection, packaging and warehousing;
the steel for the yaw bearing ring adopts normalizing and tempering heat treatment processes, and the tempering process comprises quenching and tempering;
In the normalizing process, the furnace charging temperature is less than or equal to 600 ℃, the normalizing heating temperature is 1000-1100 ℃, the normalizing heat preservation time is determined by the wall thickness of the bearing ring and the normalizing heating temperature, S-T 1/20≤t1≤S-T1/80 is satisfied, water cooling is carried out, wherein T 1 is the normalizing heating temperature, T 1 is the normalizing heat preservation time, the unit is min, S is the wall thickness of the bearing ring, and the unit is mm;
in the quenching and tempering process, the quenching heating temperature is 800-900 ℃, the quenching heat preservation time is determined by the wall thickness of the bearing ring and the quenching heating temperature, and the water cooling is carried out to satisfy S-T 2/10≤t2≤S-T2/50, wherein T 2 is the quenching heating temperature, T 2 is the quenching heat preservation time, the unit is min, the S is the wall thickness of the bearing ring, and the unit is mm;
in the tempering process, the tempering temperature is 600-700 ℃, the tempering heat preservation time is determined by the wall thickness of the bearing ring and the tempering temperature, and the water cooling of 1.5 xS-T 3/10≤t3≤1.5×S-T3/50 is satisfied, wherein T 3 is the tempering temperature, T 3 is the tempering heat preservation time, the unit is min, S is the wall thickness of the bearing ring, and the unit is mm.
3. The bearing ring manufactured by the production process of the high-strength and high-toughness high-contact fatigue high-power wind power yaw bearing ring, which is characterized in that the sorbite content at the position of 12.5mm of the surface layer of the bearing ring after tempering is 100%, and the sorbite content at the position of 1/2 wall thickness is more than or equal to 92%.
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| JPH10168547A (en) * | 1996-12-12 | 1998-06-23 | Kawasaki Steel Corp | Steel for bearing |
| CN105821304A (en) * | 2016-06-07 | 2016-08-03 | 马鞍山钢铁股份有限公司 | Niobium and titanium containing steel for motor train unit axle and heat processing technology thereof |
| CN105886904A (en) * | 2016-06-07 | 2016-08-24 | 马鞍山钢铁股份有限公司 | Vanadium-containing steel for motor train unit axle and production method and heat treatment process thereof |
| CN105951000A (en) * | 2016-07-13 | 2016-09-21 | 马鞍山钢铁股份有限公司 | Steel for vanadium/niobium-contained motor train unit axle and heat treatment process thereof |
| CN113930681A (en) * | 2021-09-29 | 2022-01-14 | 武汉钢铁有限公司 | High-hardenability high-fatigue-life low-temperature-resistant spring flat steel and production method thereof |
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- 2022-11-04 CN CN202211375363.4A patent/CN115747645B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10168547A (en) * | 1996-12-12 | 1998-06-23 | Kawasaki Steel Corp | Steel for bearing |
| CN105821304A (en) * | 2016-06-07 | 2016-08-03 | 马鞍山钢铁股份有限公司 | Niobium and titanium containing steel for motor train unit axle and heat processing technology thereof |
| CN105886904A (en) * | 2016-06-07 | 2016-08-24 | 马鞍山钢铁股份有限公司 | Vanadium-containing steel for motor train unit axle and production method and heat treatment process thereof |
| CN105951000A (en) * | 2016-07-13 | 2016-09-21 | 马鞍山钢铁股份有限公司 | Steel for vanadium/niobium-contained motor train unit axle and heat treatment process thereof |
| CN113930681A (en) * | 2021-09-29 | 2022-01-14 | 武汉钢铁有限公司 | High-hardenability high-fatigue-life low-temperature-resistant spring flat steel and production method thereof |
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