WO2023246799A1 - 一种加工性能良好的电机轴用高强韧无缝钢管及其制造方法 - Google Patents

一种加工性能良好的电机轴用高强韧无缝钢管及其制造方法 Download PDF

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Publication number
WO2023246799A1
WO2023246799A1 PCT/CN2023/101467 CN2023101467W WO2023246799A1 WO 2023246799 A1 WO2023246799 A1 WO 2023246799A1 CN 2023101467 W CN2023101467 W CN 2023101467W WO 2023246799 A1 WO2023246799 A1 WO 2023246799A1
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seamless steel
steel pipe
strength
motor shafts
manufacturing
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English (en)
French (fr)
Inventor
骆素珍
翟国丽
高展
刘文灏
孙文
陈志宏
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to DE112023002709.9T priority Critical patent/DE112023002709T5/de
Publication of WO2023246799A1 publication Critical patent/WO2023246799A1/zh
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, rods, wire, tubes, profiles or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, rods, wire, tubes, profiles or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • 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
    • C21D11/00—Process control or regulation for heat treatments
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/085—Cooling or quenching
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a steel pipe and a manufacturing method thereof, in particular to a seamless steel pipe and a manufacturing method thereof.
  • components such as electric vehicle motor shafts are responsible for transmitting motor torque to the driving wheels and are very important safety components. Due to the high-speed operation of the motor shaft, the motor shaft not only bears a huge torsional moment during actual use, but also bears traction and braking forces from the wheels, such as longitudinal force, lateral force, vertical force and vibration impact force. Therefore, in the face of such harsh usage requirements, when actually preparing motor shafts, the industry usually requires materials with high strength and plasticity to ensure sufficient anti-torsion and anti-fatigue properties.
  • the publication number is CN104962838A
  • the publication date is October 7, 2015
  • the Chinese patent document titled "A high-strength steel, high-strength plastic seamless steel pipe for automobile transmission half shaft and its manufacturing method" discloses a high-strength plastic seamless steel pipe Strength steel, high-strength plastic seamless steel pipe for automobile transmission half shaft and manufacturing method thereof, its chemical composition is: C: 0.07 ⁇ 0.15%, Si: 0.1 ⁇ 1.0%, Mn: 2.0 ⁇ 2.6%, Ni: 0.05 ⁇ 0.6% , Cr: 0.2 ⁇ 1.0%, Mo: 0.1 ⁇ 0.6%, B: 0.001-0.006%, Cu: 0.05 ⁇ 0.50%; Al: 0.015 ⁇ 0.060%; Nb: 0.02-0.1%; V: 0.02-0.15%.
  • the steel pipe adopts a low-C design.
  • the strength of the prepared finished product is low, but it is conducive to welding and is more suitable for automobile axle shafts produced by friction stir welding.
  • the publication number is CN1388834A
  • the publication number is January 1, 2003
  • the Chinese patent document titled "A high carbon steel pipe with excellent cold working performance and high frequency hardening performance and its manufacturing method” discloses a High carbon steel pipe with excellent cold working performance and high frequency hardening performance and its manufacturing method, its public chemical composition mass percentage is: C 0.30 ⁇ 0.80%, Si ⁇ 2%, Mn ⁇ 3%.
  • special rolling technology is used to obtain a structure with cementite less than 1 ⁇ m, thereby improving the cold working performance and high-frequency hardening performance of the steel.
  • the present invention hopes to develop and obtain a new high-strength seamless steel pipe and its manufacturing method for preparing motor shafts.
  • One of the purposes of the present invention is to provide a high-strength seamless steel pipe for motor shafts with good processing performance.
  • the high-strength seamless steel pipe for motor shafts can obtain excellent mechanical properties through reasonable component matching and process design. It has very excellent mechanical properties before and after quenching and tempering heat treatment, and the hardness after quenching and tempering heat treatment can reach more than 58HRC, the strong plastic product (the product of tensile strength and elongation) is more than 15000MPa%, and it can withstand torque of more than 300KN. It is particularly suitable for It is suitable for preparing motor shaft parts that carry high torsional loads, and has good promotion prospects and application value.
  • the present invention provides a high-strength seamless steel pipe for motor shafts with good processing performance, which contains Fe and inevitable impurity elements, and also contains the following chemical elements in the following mass percentages:
  • the mass percentage of each chemical element is:
  • the mass percentage of each chemical element is:
  • the increase in the C element content is beneficial to improving the strength and fatigue resistance of the material, but the C element content in the steel pipe should not be too high.
  • the toughness and plasticity of the material will decrease, which is not conducive to cold processing, and it is prone to quality problems such as processing cracks and serious decarburization. Therefore, in the high-strength seamless steel pipe for motor shafts of the present invention, in order to ensure the quenching hardness and hardenability of the material, the mass percentage content of the C element is controlled between 0.40 and 0.60%, thereby ensuring both the quenching hardness and hardenability of the material. It has good hardenability and reduces the sensitivity of quenching cracking, which can ensure the cold working performance of steel.
  • the mass percentage of the C element can be further preferably controlled between 0.45% and 0.55%.
  • the Si element has a greater influence on the cold working performance.
  • Si is the residual element after deoxidation of steel during smelting. If the steel is required to have a lower content of Si, the deO2 method during the smelting process of molten steel needs to be changed. Therefore, it is necessary to comprehensively control the Al and Ca contents to ensure deoxidation. level, and ensure that the corresponding non-metallic inclusions have no adverse impact on the fatigue resistance of the steel. Based on this, in the high-strength seamless steel pipe for motor shafts of the present invention, the mass percentage content of Si element is controlled to 0 ⁇ Si ⁇ 0.25%.
  • the mass percentage content of the Si element can be further preferably controlled to 0 ⁇ Si ⁇ 0.20%. In some preferred embodiments, the mass percentage content of Si element is controlled to be 0.01% ⁇ Si ⁇ 0.20%. In some preferred embodiments, the mass percentage content of Si element is controlled to be 0.01% ⁇ Si ⁇ 0.23%.
  • Mn In the high-strength seamless steel pipe for motor shafts of the present invention, increasing the content of Mn element can improve the strength of the material, and Mn can stabilize the P and S elements, avoid the formation of low-melting point sulfide, and improve the material's strength. Thermal processing properties.
  • the Mn element content in the steel should not be too low.
  • the Mn element content in the steel is too low, the P and S elements cannot be well stabilized and the required effects cannot be achieved.
  • the Mn element content in the steel must not be too low. It should not be too high.
  • the mass percentage content of Mn element is controlled between 0.5% and 1.2%.
  • the mass percentage of the Mn element can be further preferably controlled between 0.6 and 1.0%.
  • Ti In the high-strength seamless steel pipe for motor shafts of the present invention, an appropriate amount of Ti element can improve the hardenability of the steel.
  • the Ti element can play a role in refining the grains together with C and N elements, but the steel The content of the Ti element should not be too high. Too high a content of Ti may cause difficulties in smelting and continuous casting. Therefore, in the high-strength seamless steel pipe for motor shafts of the present invention, when added, the mass percentage content of the Ti element is controlled to Ti ⁇ 0.045%.
  • the mass percentage of the Ti element can be further preferably controlled between 0.02% and 0.04%.
  • B In the high-strength seamless steel pipe for motor shafts of the present invention, an appropriate amount of B content can improve the hardenability and plasticity of the steel, but an excessively high content of B element may cause high-temperature brittleness of the steel. Therefore, in the high-strength seamless steel pipe for motor shafts of the present invention, when added, the mass percentage content of the B element is controlled to be B ⁇ 0.0045%.
  • the mass percentage of element B can be further preferably controlled between 0.002% and 0.004%.
  • N In the high-strength seamless steel pipe for motor shafts of the present invention, N is controlled within an appropriate range so that it can refine the grains together with Ti and B elements, thereby improving the performance of the material. Therefore, in the high-strength seamless steel pipe for motor shafts of the present invention, the mass percentage content of the N element is controlled between 0.0040% and 0.009%.
  • the mass percentage of the N element can be further preferably controlled between 0.0045% and 0.0085%.
  • Al is a deoxidizer during the smelting process. It can ensure the deoxidation effect of the steel together with Si and other elements, ensure the purity of the steel, and thus ensure the quality of the material. Anti-fatigue properties.
  • the content of Al element in steel should not be too high. When the content of Al element in steel is too high, it may lead to the production of abnormal alumina inclusions. Therefore, in order to exert the beneficial effects of the Al element, in the high-strength seamless steel pipe for motor shafts of the present invention, the mass percentage content of the Al element is controlled between 0.015% and 0.045%.
  • the mass percentage of the N element can be further preferably controlled between 0.015% and 0.035%.
  • Ca, Mg In the high-strength seamless steel pipe for motor shafts of the present invention, an appropriate amount of Ca and Mg can To improve the shape and performance of non-metallic inclusions, thereby improving the fatigue properties of materials, etc. Therefore, in order to exert the beneficial effects of Ca and Mg elements in the high-strength and easy-to-cut seamless steel pipe for motor shafts of the present invention, the inventor can consider adding Ca and/or Mg elements to the steel, which requires Ca, The sum of the mass percentages of the Mg element "Ca+Mg" is controlled between 0.001 and 0.006%.
  • the sum of the mass percentages of Ca and Mg elements "Ca+Mg" can be further preferably controlled between 0.001 and 0.004%.
  • the P element and the S element are both impurity elements in the steel pipe.
  • all efforts should be made to obtain a pipe with better performance and better quality. It is possible to reduce the content of impurity elements in high-strength seamless steel pipes for motor shafts.
  • P and S are both raw materials and auxiliary materials of steel or impurity elements introduced during the production process.
  • the P element can embrittle the grain boundaries and deteriorate the toughness and processing performance of the material; while the S element can be combined to form low melting point sulfides, resulting in a decrease in the processing performance and mechanical properties of the steel.
  • the contents of P, S, and O elements in the steel must be strictly controlled, and controlled to be P ⁇ 0.020%, S ⁇ 0.008%, and O ⁇ 0.0030%.
  • the contents of P, S, and O elements can be further controlled to satisfy: P ⁇ 0.015%, S ⁇ 0.005%, and O ⁇ 0.0025%.
  • the mass percentage content of each chemical element further satisfies at least one of the following items:
  • the microstructure is ferrite + pearlite; preferably, the seamless steel pipe has been normalized.
  • the microstructure after quenching and tempering heat treatment is martensite + retained austenite with a volume phase ratio of 1-25%.
  • the retained austenite proportion is 3-24%
  • the seamless steel pipe for motor shafts of the present invention its yield strength Rp 0.2 ⁇ 400MPa, tensile strength R m ⁇ 550MPa, and elongation A 50 ⁇ 22%; preferably, the seamless The steel pipe is normalized.
  • the seamless steel pipe for motor shafts of the present invention its yield strength Rp 0.2 ⁇ 420MPa, tensile strength R m ⁇ 570MPa, and elongation A 50 ⁇ 25%; preferably, the seamless The steel pipe is normalized.
  • the seamless steel pipe for motor shafts of the present invention its yield strength Rp 0.2 ⁇ 430MPa, tensile strength R m ⁇ 590MPa, and elongation A 50 ⁇ 25%; preferably, the seamless The steel pipe is normalized.
  • the performance after quenching and tempering heat treatment satisfies: yield strength R p0.2 ⁇ 1000MPa, tensile strength R m ⁇ 1400MPa, and elongation A 50 ⁇ 5%, its hardness is ⁇ 58HRC, its strong plastic area is greater than 15000MPa%, and its torsion resistance is ⁇ 300KN.
  • the performance after quenching and tempering heat treatment satisfies: yield strength R p0.2 ⁇ 1050MPa, tensile strength R m ⁇ 1500MPa, and elongation A 50 ⁇ 7%, its hardness is ⁇ 58HRC, its strong plastic area is greater than 16000MPa%, and its torsion resistance is ⁇ 350KN.
  • the performance after quenching and tempering heat treatment satisfies: yield strength R p0.2 ⁇ 1100MPa, tensile strength R m ⁇ 1600MPa, and elongation A 50 ⁇ 7%, its hardness is ⁇ 60HRC, its strong plastic area is greater than 18000MPa%, and its torsion resistance is ⁇ 400KN.
  • another object of the present invention is to provide a method for manufacturing the above-mentioned high-strength seamless steel pipe for motor shafts.
  • This manufacturing method optimizes the design of the process.
  • the manufacturing process is simple and easy to implement, and can effectively prepare the above-mentioned high-strength seamless steel pipe of the present invention.
  • High-strength seamless steel pipes are used for motor shafts, which have very good application prospects.
  • the present invention proposes the above-mentioned manufacturing method of high-strength seamless steel pipe for motor shaft, which includes the steps:
  • Heat treatment of cold drawn tube Normalize in the temperature range of 750 ⁇ 820°C, and the holding time is 20 ⁇ 60min to obtain the ferrite + pearlite structure.
  • the method also includes the following steps:
  • Quenching and tempering control the quenching temperature to 820-880°C, hold for 15-30 minutes, and water-cool; control the tempering temperature to 150-300°C, hold for 20-40 minutes, and air-cool.
  • the operator can specifically use an electric furnace or converter to smelt and refining to cast the tube blank, and specifically use continuous casting to cut the tube blank to obtain the required size.
  • the hot-rolled pipe material obtained in step (1) must be further intermediate heat treated and cold drawn to the required specifications and dimensional accuracy, and then further finished (cold drawn) Pipe) heat treatment, and finally obtain finished raw materials with good cold and cold processing properties.
  • the hot-rolled pipe material is controlled to be annealed in the temperature range of 650 to 800°C and kept for 20 to 80 minutes, which can ensure the cold drawing of the subsequent step (4).
  • the process went smoothly.
  • the cold-drawn pipe material prepared in the above-mentioned step (4) needs to be normalized in the temperature range of 750 to 820°C, kept for 20 to 60 minutes, and the atmosphere in the furnace needs to be controlled. , ensuring that there is no complete decarburization (that is, there is no full ferrite tissue area on the surface of the steel pipe), and the depth of semi-decarburization is ⁇ 150 ⁇ m.
  • the normalizing temperature and the cooling method it can ensure that the steel pipe obtains a ferrite + pearlite structure, thereby obtaining a normalized pipe whose strength and toughness meet the cold working requirements.
  • step (2) the tube blank is heated and kept at 1210-1280°C for 30-150 minutes.
  • step (2) the perforation temperature is controlled to be 1150-1250°C.
  • step (2) the hot continuous rolling temperature is controlled to be 1000-1200°C.
  • step (2) the tension and relaxation temperature is controlled to be 950 ⁇ 1000°C.
  • the tube blank is manufactured by circuit or converter smelting, refining and pouring, and is cut to the required size by continuous casting.
  • it also includes the steps of intermediate heat treatment and cold drawing to the required specifications and dimensional accuracy.
  • step (5) the pipe obtained by normalizing treatment is not completely decarburized, and the depth of semi-decarburization is ⁇ 150 ⁇ m.
  • the high-strength seamless steel pipe for motor shafts and its manufacturing method according to the present invention have the following advantages and beneficial effects:
  • the inventor can obtain a brand new high-strength seamless steel pipe for motor shafts through reasonable component matching and process design.
  • the microstructure of the high-strength seamless steel pipe for motor shafts after heat treatment is iron.
  • Prime body + pearlite, while the microstructure after further quenching and tempering heat treatment is martensite + retained austenite with a volume phase ratio of 1-25%.
  • the high-strength seamless steel pipe for motor shafts prepared by the present invention has Rp 0.2 ⁇ 400MPa, tensile strength R m ⁇ 550MPa, and elongation A 50 ⁇ 22% in the finished product state; however, the high-strength seamless steel pipe for motor shafts is After further quenching and tempering heat treatment, the strength of the seam steel pipe can be significantly improved.
  • the strong plastic product (the product of tensile strength and elongation) is greater than 15000MPa% and can withstand a torque of more than 300KN. It is especially suitable for preparing motor shaft parts carrying high torsional loads and has good promotion prospects and application value. .
  • Heating, perforation, hot rolling and tensioning heat and keep the tube blank at 1210 ⁇ 1280°C for 30 ⁇ 150min. Then perform high-temperature piercing between 1150 and 1250°C, and then perform high-temperature hot continuous rolling between 1000 and 1200°C. After completing the hot rolling, further conduct tension and reduction, and control the tension and reduction temperature to 950 to 1000°C to obtain Hot rolled pipe.
  • Cold-drawn pipe heat treatment Control the cold-drawn pipe material to be normalized in the temperature range of 750 to 820°C, and the holding time is 20 to 60 minutes to obtain the ferrite + pearlite structure.
  • Table 1 lists the mass percentage of each chemical element in the high-strength seamless steel pipe for motor shaft of Examples 1-10 and the comparative steel pipe of Comparative Examples 1-2.
  • Table 2 lists the specific process parameters used in the above manufacturing process steps for the high-strength seamless steel pipes for motor shafts in Examples 1-10 and the comparative steel pipes of Comparative Examples 1-2.
  • Tensile test According to GB/T 228.1-2010 Metal Materials
  • Tensile Test Part 1 Room Temperature Tensile Test Method, to test the steel pipes obtained in each example and comparative example before quenching and tempering heat treatment at room temperature. Yield strength, tensile strength and elongation values.
  • Table 3 lists the performance test results of the high-strength seamless steel pipes for motor shafts in Examples 1-10 that have not undergone quenching and tempering heat treatment and the comparative steel pipes in Comparative Examples 1-2.
  • the high-strength seamless steel pipes for motor shafts in Examples 1-10 already have very excellent mechanical properties, and their yield strength R p0.2 is at 417 -506MPa, its tensile strength R m is between 564-672MPa, and its elongation A 50 is between 23-30%.
  • the microstructure of the high-strength seamless steel pipes for motor shafts in Examples 1 to 10 was all ferrite + pearlite.
  • the inventor further tested the high-strength and toughness seamless steel pipes for motor shafts in the prepared finished product examples 1-10.
  • Seamless steel pipes and comparative steel pipes of Comparative Examples 1-2 were sampled separately, and the steel pipes of each Example and Comparative Example were subjected to quenching and tempering heat treatment.
  • the process of controlling the quenching and tempering heat treatment was as follows: the quenching temperature is 860°C, and the holding time is 20 minutes. Water cooling; tempering temperature is 250°C, holding time is 30min, air cooling.
  • the inventor After completing the quenching and tempering heat treatment of the steel pipes of the examples and comparative examples, the inventor further conducted a mechanical property test on the quenched and tempered heat treated steel pipes to measure the performance of the steel pipes after quenching and tempering heat treatment.
  • the relevant mechanical property test results are listed below in Table 4.
  • the tensile test process is the same as the test process in Table 3 above, which can also be measured corresponding to the quenching and tempering heat treatment. Yield strength, tensile strength and elongation of the steel pipes of Examples 1-10 and Comparative Examples 1-2.
  • Hardness test Use a Rockwell hardness tester to measure the hardness (HRC) of the steel pipes of Examples 1-10 and Comparative Examples 1-2 after quenching and tempering heat treatment.
  • Anti-torsion performance test Use a static torsion test device to measure the anti-torsion performance of the steel pipes of Examples 1-10 and Comparative Examples 1-2 after quenching and tempering heat treatment.
  • Table 4 lists the performance test results of the high-strength seamless steel pipes for motor shafts of Examples 1-10 and the comparative steel pipes of Comparative Examples 1-2 after quenching and tempering heat treatment.
  • Rm ⁇ A50 is the strong plastic product, which is the product of tensile strength and elongation.
  • the high-strength seamless steel pipes for motor shafts obtained in Examples 1-10 of the present invention all have excellent mechanical properties.
  • Their yield strength R p0.2 is between 1059-1169 MPa
  • their tensile strength R m is between 1400-1766MPa
  • elongation is between 9-15%
  • its strong plasticity R m ⁇ A 50 is between 15499-24724MPa%
  • hardness is between 59-64HRC
  • torsion resistance is between 346-597KN between.
  • Comparative Examples 1-2 Compared with Examples 1-10, in Comparative Examples 1-2, there are chemical components and/or processes that do not meet the design requirements of the present invention. This design makes at least one of the comparative steel pipes prepared in Comparative Examples 1-2 The mechanical properties failed to meet the requirements of the present invention. As shown in Table 4, the torsional properties of Comparative Examples 1 and 2 are lower than those of Examples 1-10.
  • Table 5 lists the microstructure observation and analysis results of the high-strength seamless steel pipes for motor shafts of Examples 1-10 and the comparative steel pipes of Comparative Examples 1-2 after quenching and tempering heat treatment.

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Abstract

本发明公开了一种加工性能良好的电机轴用高强韧无缝钢管及其制造方法，该无缝钢管含有Fe和不可避免的杂质元素，其还含有质量百分含量如下的下述各化学元素：C：0.40～0.60％，0＜Si≤0.25％，Mn：0.5～1.2％，Ti≤0.045％，B≤0.0045％，N：0.0040～0.009％，Al：0.015～0.045％，Ca+Mg：0.001～0.006％。该无缝钢管在调质热处理前后均具有十分优异的力学性能，且调制热处理后的硬度可达到58HRC以上，强塑积大于15000MPa％，能抵抗300KN以上的扭矩。

Description

一种加工性能良好的电机轴用高强韧无缝钢管及其制造方法 技术领域
本发明涉及一种钢管及其制造方法，尤其涉及一种无缝钢管及其制造方法。
背景技术
近年来，在减碳减污的大背景下，电动车的产销量开始突飞猛进，市场和用于对于电动车自身轻量化的要求也变的越来越苛刻。为了达到最大程度的轻量化，除主车身采用高强度钢、轻质材料外，在整车重量中占比较小的零部件如电机轴等车辆结构件也开始逐渐纳入减重行列，行业内利用空心管材来替代实心棒材和锻材已是大势所趋。
在现有技术中，电动车电机轴等零部件承担着向驱动轮传递电机转矩的功能，是非常重要的安全部件。由于电机轴高速运转，电机轴在实际使用时不仅承受着极大的扭转力矩，其还承受着来自车轮的牵引力、制动力等，例如：纵向力、侧向力、垂直力和震动冲击力。因此，面对如此苛刻的使用要求，在实际制备电机轴时，行业内通常要求材料具有较高的强度、塑性，以确保获得充分的抗扭转、抗疲劳的性能。
此外，因为各类车型所存在的不同，不同电机轴需要通过整体冷挤压、切削加工等加工过程才能获得所需的高速旋转条件下的抗扭、抗疲劳性能。因此，在设计这类电机轴用钢时，在考虑高强韧性、高疲劳性能的同时，还必须兼具良好的冷加工性能。
例如：公开号为CN104962838A，公开日为2015年10月07日，名称为“一种高强度钢、汽车传动半轴用高强塑无缝钢管及其制造方法”的中国专利文献公开了一种高强度钢、汽车传动半轴用高强塑无缝钢管及其制造方法，其化学成分为：C：0.07～0.15％，Si：0.1～1.0％，Mn：2.0～2.6％，Ni：0.05～0.6％，Cr：0.2～1.0％，Mo：0.1～0.6％，B：0.001-0.006％，Cu：0.05～0.50％；Al：0.015～0.060％；Nb：0.02-0.1％；V：0.02-0.15％。在该技术方案中，钢管采用的是低C设计，其所 制备的成品强度偏低，但有利于焊接，比较适合搅拌摩擦焊生产的汽车半轴。
又例如：公开号为CN1388834A，公开号为2003年1月1日，名称为“一种冷加工性能和高频淬硬性能出色的高碳钢管及其制造方法”的中国专利文献，公开了一种冷加工性能和高频淬硬性能出色的高碳钢管及其制造方法，其其公的化学成分质量百分比为：C 0.30～0.80％，Si≤2％，Mn≤3％。在该技术方案中，其是利用特殊的轧制技术，获得渗碳体小于1μm的组织，从而改善钢材的冷加工性能和高频淬硬性能。
不同于上述现有的技术方案，为了解决现有技术中所存在的问题，本发明期望开发并获得一种新的高强韧无缝钢管及其制造方法，以用于制备电机轴。
发明内容
本发明的目的之一在于提供一种加工性能良好的电机轴用高强韧无缝钢管，该电机轴用高强韧无缝钢管通过合理的成分匹配及工艺设计，可以获得优异的力学性能，其在调质热处理前后均具有十分优异的力学性能，且调制热处理后的硬度可达到58HRC以上，强塑积(抗拉强度和延伸率的乘积)大于15000MPa％，能抵抗300KN以上的扭矩，其特别适用于制备承载高扭转载荷的电机轴类零部件，具有良好的推广前景和应用价值。
为了实现上述目的，本发明提供了一种加工性能良好的电机轴用高强韧无缝钢管，其含有Fe和不可避免的杂质元素，其还含有质量百分含量如下的下述各化学元素：
C：0.40～0.60％，0＜Si≤0.25％，Mn：0.5～1.2％，Ti≤0.045％，B≤0.0045％，N：0.0040～0.009％，Al：0.015～0.045％，Ca+Mg：0.001～0.006％。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其各化学元素质量百分比为：
C：0.40～0.60％，0＜Si≤0.25％，Mn：0.5～1.2％，Ti≤0.045％，B≤0.0045％，N：0.0040～0.009％，Al：0.015～0.045％，Ca+Mg：0.001～0.006％；余量为Fe和不可避免的杂质。
优选地，各化学元素质量百分比为：
C：0.4～0.57％，Si：0.01～0.23％，Mn：0.5～1.2％，Ti：0～0.043％，B：0～0.0042％，N：0.004～0.009％，Al：0.016～0.045％，Ca+Mg：0.001～0.006％。
在本发明所述的电机轴用高强韧无缝钢管中，各化学元素的设计原理如下所述：
C：在本发明所述的电机轴用高强韧无缝钢管中，C元素含量的提高有利于提高材料的强度和抗疲劳性能，但钢管中的C元素含量也不宜过高，当C元素含量过高时，会导致材料的韧塑性下降，不利于冷加工，且容易出现加工裂纹、脱碳严重等质量问题。因此，在本发明所述的电机轴用高强韧无缝钢管中，为保证材料的淬火硬度和淬硬性，将C元素的质量百分含量控制在0.40～0.60％之间，从而既保证材料的淬透性、又降低了淬裂敏感性，其可以确保钢材的冷加工性能。
当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步优选地将C元素的质量百分含量控制在0.45～0.55％之间。
Si：在本发明所述的电机轴用高强韧无缝钢管中，Si元素对冷加工性能影响较大，钢管中的Si元素含量越低，则钢管的冷加工性能越好。一般情况下，Si是钢在冶炼脱氧后的残余元素，如果要求钢中具备较低含量的Si，则需要改变钢水冶炼过程中的脱O方式，因此需要通过综合控制Al和Ca含量来确保脱氧水平，并确保对应的非金属夹杂物对钢材的抗疲劳性能无不利影响。基于此，在本发明所述的电机轴用高强韧无缝钢管中，将Si元素的质量百分含量控制为0＜Si≤0.25％。
当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步优选地将Si元素的质量百分含量控制为0＜Si≤0.20％。在一些优选的实施方式中，将Si元素的质量百分含量控制为0.01％≤Si≤0.20％。在一些优选的实施方式中，将Si元素的质量百分含量控制为0.01％≤Si≤0.23％。
Mn：在本发明所述的电机轴用高强韧无缝钢管中，提高Mn元素的含量，可以提高材料的强度，且Mn能够稳定P、S元素，避免低熔点硫化物的形成，提高材料的热加工性能。为了实现上述效果，钢中Mn元素含量不宜过低，当钢中Mn元素含量过低时，则不能很好的稳定P、S元素，达不到所需的效果；同时，钢中Mn元素含量也不宜过高，钢中Mn元素含量过高时，会导致冷加工形变硬化严重，并加剧模具磨损。因此，考虑到Mn元素含量对于钢材性能的影响，在本发明所述的电机轴用高强韧无缝钢管中，将Mn元素的质量百分含量控制在0.5～1.2％之间。
当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步优选地将Mn元素的质量百分含量控制在0.6～1.0％之间。
Ti：在本发明所述的电机轴用高强韧无缝钢管中，适量的Ti元素可以改善钢的淬硬性，Ti元素能够与C和N元素一起可以起到细化晶粒的作用，但钢中Ti元素的含量不宜过高，过高含量的Ti可能导致冶炼连铸困难。因此，在本发明所述的电机轴用高强韧无缝钢管中，当添加时，将Ti元素的质量百分含量控制为Ti≤0.045％。
当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步优选地将Ti元素的质量百分含量控制在0.02～0.04％之间。
B：在本发明所述的电机轴用高强韧无缝钢管中，适量的B含量可以改善钢的淬透性和塑性，但过高含量的B元素可能会导致钢材的高温脆性。因此，在本发明所述的电机轴用高强韧无缝钢管中，当添加时，将B元素的质量百分含量控制为B≤0.0045％。
当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步优选地将B元素的质量百分含量控制在0.002～0.004％之间。
N：在本发明所述的电机轴用高强韧无缝钢管中，将N控制在适量范围，使得其可以与Ti、B元素一起细化晶粒，从而改善材料的性能。因此，在本发明所述的电机轴用高强韧无缝钢管中，将N元素的质量百分含量控制在0.0040～0.009％之间。
当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步优选地将N元素的质量百分含量控制在0.0045～0.0085％之间。
Al：在本发明所述的电机轴用高强韧无缝钢管中，Al是冶炼过程中脱氧剂，其能够与Si等元素一起确保钢种的脱氧效果，保证钢质纯净度，从而保证材料的抗疲劳性能。但需要注意的是，钢中Al元素含量也不宜过高，当钢中Al元素含量过高时，可能导致异常氧化铝夹杂物的产生。因此，为发挥Al元素的有益效果，在本发明所述的电机轴用高强韧无缝钢管中，将Al元素的质量百分含量控制在0.015～0.045％之间。
当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步优选地将N元素的质量百分含量控制在0.015～0.035％之间。
Ca、Mg：在本发明所述的电机轴用高强韧无缝钢管中，适量的Ca、Mg可 以改善非金属夹杂物形状和性能，从而改善材料的疲劳性能等。因此，在本发明所述的高强韧易切削电机轴用无缝钢管中，为发挥Ca、Mg元素的有益效果，发明人可以考虑向钢中添加Ca和/或Mg元素，其需要将Ca、Mg元素的质量百分含量之和“Ca+Mg”控制在0.001～0.006％之间。
当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步优选地将Ca、Mg元素的质量百分含量之和“Ca+Mg”控制在0.001～0.004％之间。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，在不可避免的杂质中，P≤0.020％，S≤0.008％，O≤0.0030％。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，在不可避免的杂质中，P≤0.015％，S≤0.005％，O≤0.0025％。
在本发明所述的电机轴用高强韧无缝钢管中，P元素和S元素均为钢管中的杂质元素，在技术条件允许情况下，为了获得性能更好且质量更优的管材，应尽可能降低电机轴用高强韧无缝钢管中杂质元素的含量。
在本发明中，P、S均是钢铁原辅料或生产过程中引入的杂质元素，P元素可使晶界脆化，使材料的韧性和加工性能劣化；而S元素则可以配合形成低熔点的硫化物，从而导致钢材的加工性能以及本身的力学性能下降。
因此，在本发明中，必须严格地控制钢中P、S、O元素的含量，并控制为P≤0.020％，S≤0.008％，O≤0.0030％。当然，在一些优选的实施方式中，为了获得更优的实施效果，可以进一步控制P、S、O元素的含量满足：P≤0.015％，S≤0.005％，O≤0.0025％。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其各化学元素质量百分含量进一步满足下述各项的至少其中之一：
C：0.45～0.55％，
0＜Si≤0.20％，
Mn：0.6～1.0％，
Ti：0.02～0.04％，
B：0.002～0.004％，
N：0.0045～0.0085％，
Al：0.015～0.035％，
Ca+Mg：0.001～0.004％。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其微观组织为铁素体+珠光体；优选地，所述无缝钢管经过正火处理。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其经过调质热处理的微观组织为马氏体+体积相比例为1-25％残余奥氏体。优选地，残余奥氏体比例为3-24％
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其屈服强度Rp0.2≥400MPa，抗拉强度Rm≥550MPa，延伸率A50≥22％；优选地，所述无缝钢管经过正火处理。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其屈服强度Rp0.2≥420MPa，抗拉强度Rm≥570MPa，延伸率A50≥25％；优选地，所述无缝钢管经过正火处理。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其屈服强度Rp0.2≥430MPa，抗拉强度Rm≥590MPa，延伸率A50≥25％；优选地，所述无缝钢管经过正火处理。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其经过调质热处理的性能满足：屈服强度Rp0.2≥1000MPa，抗拉强度Rm≥1400MPa，延伸率A50≥5％，其硬度≥58HRC，强塑积大于15000MPa％，抗扭转性能≥300KN。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其经过调质热处理的性能满足：屈服强度Rp0.2≥1050MPa，抗拉强度Rm≥1500MPa，延伸率A50≥7％，其硬度≥58HRC，强塑积大于16000MPa％，抗扭转性能≥350KN。
进一步地，在本发明所述的电机轴用高强韧无缝钢管中，其经过调质热处理的性能满足：屈服强度Rp0.2≥1100MPa，抗拉强度Rm≥1600MPa，延伸率A50≥7％，其硬度≥60HRC，强塑积大于18000MPa％，抗扭转性能≥400KN。
相应地，本发明的另一目的在于提供上述的电机轴用高强韧无缝钢管的制造方法，该制造方法对工艺进行了优化设计，其制造过程简便且易于实施，可以有效制备本发明上述的电机轴用高强韧无缝钢管，具有十分良好的应用前景。
为了实现上述目的，本发明提出了上述的电机轴用高强韧无缝钢管的制造方法，其包括步骤：
(1)制得管坯；
(2)加热、穿孔、热轧和张减；
(3)中间热处理：将热轧管料在650～800℃温度区间进行退火，保温时间为20～80min；
(4)冷拔；
(5)冷拔管热处理：在750～820℃温度区间进行正火，保温时间为20～60min，以获得铁素体+珠光体组织。
优选地，该方法还包括以下步骤：
(6)调质：控制淬火温度820～880℃，保温15～30min，水冷；控制回火温度150～300℃，保温20～40min，空冷。
在本发明上述技术方案中，在步骤(1)的管坯制造过程中，操作人员可以具体利用电炉或转炉冶炼+精炼浇注成管坯，并具体利用连铸切割到得到所需尺寸的管坯。为了满足汽车电机轴对钢管尺寸精度以及冷加工过程对表面状态的要求，须对步骤(1)所得热轧管料进一步中间热处理，并冷拔至所需规格和尺寸精度，再进一步成品(冷拔管)热处理，最终获得冷冷加工性能良好的成品原料。
需要说明的是，在上述步骤(3)中，在中间热处理工艺时，控制热轧管料在650～800℃温度区间进行退火，并保温20～80min，可以确保后续步骤(4)的冷拔过程的顺利进行。
另外，在本发明上述步骤(5)的成品热处理中，需要将上述步骤(4)所制备的冷拔管料在750～820℃温度区间进行正火，保温20～60min，并控制炉内气氛，保证无全脱碳(即钢管表面无全铁素体组织区)，半脱碳深度≤150μm。在该技术方案中，其通过控制正火温度和冷却方式的配合，可以确保钢管获得铁素体+珠光体组织，从而获得强度和韧性均满足冷加工要求的正火管。
进一步地，在本发明所述的制造方法中，在步骤(2)中，将管坯在1210～1280℃加热保温30～150min。
进一步地，在本发明所述的制造方法中，在步骤(2)中，控制穿孔温度为1150～1250℃。
进一步地，在本发明所述的制造方法中，在步骤(2)中，控制热连轧温度为1000～1200℃。
进一步地，在本发明所述的制造方法中，在步骤(2)中，控制张减温度为 950～1000℃。
进一步地，在本发明所述的制造方法中，包含下列步骤至少其中之一：
在步骤(1)中，所述管坯由电路或转炉冶炼、精炼浇筑制造，采用连铸切割得到所需尺寸，优选地，还包括进行中间热处理并冷拔至所需规格和尺寸精度的步骤；
在步骤(5)中，正火处理得到的管材无全脱碳，半脱碳深度≤150μm。
相较于现有技术，本发明所述的电机轴用高强韧无缝钢管及其制造方法具有如下所述的优点以及有益效果：
在本发明中，发明人通过合理的成分匹配及工艺设计，可以获得一种全新的电机轴用高强韧无缝钢管，该电机轴用高强韧无缝钢管在经过热处理后获得的微观组织为铁素体+珠光体，而在进一步进行调质热处理后的微观组织为马氏体+体积相比例为1-25％残余奥氏体。
本发明所制备的这种电机轴用高强韧无缝钢管在成品状态下的Rp0.2≥400MPa，抗拉强度Rm≥550MPa，延伸率A50≥22％；但这种电机轴用高强韧无缝钢管在进一步进行调质热处理后，其强度可以获得明显提升，其屈服强度Rp0.2≥1000MPa，抗拉强度Rm≥1400MPa，延伸率A50≥5％，且调制热处理后的硬度可达到58HRC以上，强塑积(抗拉强度和延伸率的乘积)大于15000MPa％，能抵抗300KN以上的扭矩，其特别适用于制备承载高扭转载荷的电机轴类零部件，具有良好的推广前景和应用价值。
具体实施方式
下面将结合具体的实施例对本发明所述的电机轴用高强韧无缝钢管及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-10和对比例1-2
本发明所述实施例1-10的电机轴用高强韧无缝钢管和对比例1-2的对比钢管均采用以下步骤制得：
(1)按照表1所示的化学元素的质量百分配比利用电炉或转炉冶炼+精炼浇注成管坯，并连铸切割到得到所需尺寸管坯。
(2)加热、穿孔、热轧和张减：将管坯在1210～1280℃加热保温30～150min， 再在1150～1250℃之间进行高温穿孔，然后在1000～1200℃之间进行高温热连轧，完成热轧后进一步进行张减，并控制张减温度为950～1000℃，以加工制得热轧管料。
(3)中间热处理：将热轧管料在650～800℃温度区间进行退火，保温时间为20～80min。
(4)冷拔。
(5)冷拔管热处理：控制冷拔管料在750～820℃温度区间进行正火，保温时间为20～60min，以获得铁素体+珠光体组织。
需要说明的是，本发明所述实施例1-10的电机轴用高强韧无缝钢管的化学元素成分和相关工艺设计均满足本发明设计规范要求。而对比例1-2的对比钢管虽然也采用上述工艺步骤制得，但其化学元素成分和/或相关工艺参数存在不符合本发明设计的参数。
表1列出了实施例1-10的电机轴用高强韧无缝钢管和对比例1-2的对比钢管中各化学元素质量百分比。
表1.(余量为Fe和除P、S、O外其他的不可避免的杂质)
表2列出了实施例1-10的电机轴用高强韧无缝钢管和对比例1-2的对比钢管在上述制造工艺步骤中所采用的具体工艺参数。
表2.

将制备的成品实施例1-10的电机轴用高强韧无缝钢管和对比例1-2的对比钢管分别取样，并对各实施例和对比例的钢管在未经过调质热处理前的微观组织进行观察，并对各实施例和对比例的各项性能进行测试，以获得调质前的常温力学性能，相关力学性能的测试结果列于表3中。
相关性能检测手段如下所述：
拉伸试验：按照根据GB/T 228.1-2010金属材料拉伸试验第1部分：室温拉伸试验方法，以测试获得在未经过调质热处理前的各实施例和对比例的钢管在室温下的屈服强度、抗拉强度和延伸率数值。
表3列出了未经过调质热处理的实施例1-10的电机轴用高强韧无缝钢管和对比例1-2的对比钢管的性能测试结果。
表3.

从上述表3之中可以看出，在未经过调质热处理前，实施例1-10的电机轴用高强韧无缝钢管已经具备了十分优异的力学性能，其屈服强度Rp0.2在417-506MPa之间，其抗拉强度Rm在564-672MPa之间，其延伸率A50在23-30％之间。此外，观察发现，在未经过调质热处理前，实施例1-10的电机轴用高强韧无缝钢管的微观组织均为铁素体+珠光体。
相应地，为了进一步说明本发明所述的电机轴用高强韧无缝钢管在经过调质热处理后仍然具有十分优异的性能，发明人进一步对制备的成品实施例1-10的电机轴用高强韧无缝钢管和对比例1-2的对比钢管分别取样，并对各实施例和对比例的钢管进行调质热处理，控制调质热处理的工艺为：其中淬火温度为860℃，保温时间为20min，水冷；回火温度为250℃，保温时间为30min，空冷。
在完成对于实施例和对比例样品钢管的调质热处理后，发明人进一步对调质热处理后的钢管进行力学性能测试，以测得钢管在调质热处理后的性能，相关力学性能测试结果列于下述表4之中。
在对调质热处理后的实施例1-10和对比例1-2的钢管进行力学性能测试时，其所进行的拉伸试验过程同上述表3的测试过程，其同样可以对应测得调质热处理后的实施例1-10和对比例1-2的钢管的屈服强度、抗拉强度和延伸率。
此外，除上述性能外，还进一步地对调质热处理后的各实施例和对比例钢管的其他性能进行了测试，相关测试手段如下所述：
硬度测试试验：采用洛氏硬度测定仪，以测得调质热处理后的实施例1-10和对比例1-2的钢管的硬度(HRC)。
抗扭转性能测试：采用静扭试验装置，以测得调质热处理后的实施例1-10和对比例1-2的钢管的抗扭转性能。
表4列出了经过调质热处理后的实施例1-10的电机轴用高强韧无缝钢管和对比例1-2的对比钢管的性能测试结果。
表4.
注：在上述表4之中，Rm×A50为强塑积，其是抗拉强度和延伸率的乘积。
由表4可以看出，在调质热处理后，相较于对比例1-2的对比钢管，本发明所述实施例1-10的电机轴用高强韧无缝钢管的综合性能明显更优。同时，相较于调质热处理前，调质热处理后的实施例1-10的电机轴用高强韧无缝钢管的屈服强度和抗拉强度均得到了明显的提升，且延伸率A50相应地下降了。
参阅表4可知，本发明所获得的实施例1-10的电机轴用高强韧无缝钢管均具有优异的力学性能，其屈服强度Rp0.2在1059-1169MPa之间，其抗拉强度Rm在1400-1766MPa之间，延伸率在9-15％之间，其强塑性Rm×A50在15499-24724MPa％之间，硬度在59-64HRC之间，且抗扭转性能在346-597KN之间。
相较于实施例1-10，在对比例1-2中，均存在不满足本发明设计要求的化学成分和/或工艺，这种设计使得对比例1-2所制备的对比钢管的至少一项力学性能并未能达到本发明的要求。如表4所示，对比例1和对比例2的抗扭性能低于实施例1-10。
此外，完成上述力学性能性能的检测后，发明人还对经过调质热处理后的实施例1-10和对比例1-2的钢管进行了取样，并对其微观组织进行观察和分析，相关观察和分析结果如下述表5所示。本发明中，采用蔡司(ZEISS)光学显微镜观察微观组织，采用X射线衍射(XRD)分析残余奥氏体的比例。
表5列出了经过调质热处理后的实施例1-10的电机轴用高强韧无缝钢管和对比例1-2的对比钢管的微观组织观察分析结果。
表5.
由上述表5可以看出，在经过调质热处理后，实施例1-10的电机轴用高强韧无缝钢管均获得了马氏体+残余奥氏体的微观组织，且其残余奥氏体的体积相比例具体在3-24％之间。
需要说明的是，本案中各技术特征的组合方式并不限本案权利要求中所记载的组合方式或是具体实施例所记载的组合方式，本案记载的所有技术特征可以以任何方式进行自由组合或结合，除非相互之间产生矛盾。
还需要注意的是，以上所列举的实施例仅为本发明的具体实施例。显然本发明不局限于以上实施例，随之做出的类似变化或变形是本领域技术人员能从本发明公开的内容直接得出或者很容易便联想到的，均应属于本发明的保护范围。

Claims (15)

  1. 一种加工性能良好的电机轴用高强韧无缝钢管，其含有Fe和不可避免的杂质元素，其特征在于，其还含有质量百分含量如下的下述各化学元素：
    C：0.40～0.60％，0＜Si≤0.25％，Mn：0.5～1.2％，Ti≤0.045％，B≤0.0045％，N：0.0040～0.009％，Al：0.015～0.045％，Ca+Mg：0.001～0.006％。
  2. 如权利要求1所述的电机轴用高强韧无缝钢管，其特征在于，其各化学元素质量百分比为：
    C：0.40～0.60％，0＜Si≤0.25％，Mn：0.5～1.2％，Ti≤0.045％，B≤0.0045％，N：0.0040～0.009％，Al：0.015～0.045％，Ca+Mg：0.001～0.006％；余量为Fe和不可避免的杂质；
    优选地，各化学元素质量百分比为：
    C：0.4～0.57％，Si：0.01～0.23％，Mn：0.5～1.2％，Ti：0～0.043％，B：0～0.0042％，N：0.004～0.009％，Al：0.016～0.045％，Ca+Mg：0.001～0.006％。
  3. 如权利要求1或2所述的电机轴用高强韧无缝钢管，其特征在于，在不可避免的杂质中，P≤0.020％，S≤0.008％，O≤0.0030％。
  4. 如权利要求3所述的电机轴用高强韧无缝钢管，其特征在于，在不可避免的杂质中，P≤0.015％，S≤0.005％，O≤0.0025％。
  5. 如权利要求1或2所述的电机轴用高强韧无缝钢管，其特征在于，其各化学元素质量百分含量进一步满足下述各项的至少其中之一：
    C：0.45～0.55％，
    0＜Si≤0.20％，
    Mn：0.6～1.0％，
    Ti：0.02～0.04％，
    B：0.002～0.004％，
    N：0.0045～0.0085％，
    Al：0.015～0.035％，
    Ca+Mg：0.001～0.004％。
  6. 如权利要求1或2所述的电机轴用高强韧无缝钢管，其特征在于，其微观组织为铁素体+珠光体。
  7. 如权利要求1或2所述的电机轴用高强韧无缝钢管，其特征在于，其经过调质热处理的微观组织为马氏体+体积相比例为1-25％残余奥氏体；优选地，残余奥氏体比例为3-24％。
  8. 如权利要求1或2所述的电机轴用高强韧无缝钢管，其特征在于，其屈服强度Rp0.2≥400MPa，抗拉强度Rm≥550MPa，延伸率A50≥22％。
  9. 如权利要求1或2所述的电机轴用高强韧无缝钢管，其特征在于，其经过调质热处理的性能满足：屈服强度Rp0.2≥1000MPa，抗拉强度Rm≥1400MPa，延伸率A50≥5％，其硬度≥58HRC，强塑积大于15000MPa％，抗扭转性能≥300KN。
  10. 一种如权利要求1-9中任意一项所述的电机轴用高强韧无缝钢管的制造方法，其特征在于，包括步骤：
    (1)制得管坯；
    (2)加热、穿孔、热轧和张减；
    (3)中间热处理：将热轧管料在650～800℃温度区间进行退火，保温时间为20～80min；
    (4)冷拔；
    (5)冷拔管热处理：在750～820℃温度区间进行正火，保温时间为20～60min，以获得铁素体+珠光体组织；
    优选地，该方法还包括以下步骤：
    (6)调质：控制淬火温度820～880℃，保温15～30min，水冷；控制回火温度150～300℃，保温20～40min，空冷。
  11. 如权利要求10所述的制造方法，其特征在于，在步骤(2)中，将管坯在1210～1280℃加热保温30～150min。
  12. 如权利要求10所述的制造方法，其特征在于，在步骤(2)中，控制穿孔温度为1150～1250℃。
  13. 如权利要求10所述的制造方法，其特征在于，在步骤(2)中，控制热连轧温度为1000～1200℃。
  14. 如权利要求10所述的制造方法，其特征在于，在步骤(2)中，控制张减温度为950～1000℃。
  15. 如权利要求10所述的制造方法，其特征在于：
    在步骤(1)中，所述管坯由电路或转炉冶炼、精炼浇筑制造，采用连铸切割得到所需尺寸，优选地，还包括进行中间热处理并冷拔至所需规格和尺寸精度的步骤；和/或
    在步骤(5)中，正火处理得到的管材无全脱碳，半脱碳深度≤150μm。
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