CN105624560B - A kind of bearing steel and its manufacturing method with improved fatigue durability - Google Patents

A kind of bearing steel and its manufacturing method with improved fatigue durability Download PDF

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Publication number
CN105624560B
CN105624560B CN201510818333.XA CN201510818333A CN105624560B CN 105624560 B CN105624560 B CN 105624560B CN 201510818333 A CN201510818333 A CN 201510818333A CN 105624560 B CN105624560 B CN 105624560B
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alloy composite
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bearing steel
chromium
total weight
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CN105624560A (en
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车星澈
洪承贤
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Hyundai Motor Co
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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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C21D1/32—Soft annealing, e.g. spheroidising
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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 by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/36—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for balls; for rollers
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Rolling Contact Bearings (AREA)
  • Sliding-Contact Bearings (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

A kind of alloy composite for the bearing steel with improved fatigue durability and a kind of method of bearing steel of the manufacture comprising it are disclosed.The alloy composite includes: the total weight based on the alloy composite, the carbon (C) of about 0.8~1.0wt%, the silicon (Si) of about 0.35~0.9wt%, the manganese (Mn) of about 0.5~1.0wt%, the nickel (Ni) of about 0.6~1.5wt%, the chromium (Cr) of about 1.2~1.55wt%, the molybdenum (Mo) of about 0.2~0.5wt%, the aluminium (Al) of about 0.01~0.06wt%, about 0.01~0.1wt% copper (Cu) and constitute the iron (Fe) of alloy composite surplus.Since the preferred alloy composite of spheroidized carbide complex can provide improved intensity, hardness and fatigue life.

Description

A kind of bearing steel and its manufacturing method with improved fatigue durability
Cross reference to related applications
The application is special according to the South Korea that 35U.S.C. § 119 requires on November 24th, 2014 to submit to Korean Intellectual Property Office The priority of sharp application number 10-2014-164102, it is open to be incorporated herein by reference with it.
Technical field
The present invention relates to a kind of alloy composites for bearing steel, and it includes the double carbides of nodularization to improve hardness And fatigue durability and it is a kind of manufacture the bearing steel containing the alloy composite method.
Background technique
In automobile industry, developed various Cleaning Equipments, with based on European directive until 2021 by titanium dioxide It is target that the discharge amount of carbon, which is reduced to about 95g/km, is at present horizontal about 27%.In addition, automaker has developed A kind of technology with reduce the size of vehicle and improve fuel economy with meet about 54.5mpg (about 23.2km/l), its be in beauty Specified value of the state until enterprise's average fuel economy (CAFE) in 2025.
Specifically, in order to maximize the fuel economy of vehicle, high performance engine and speed changer have been developed And efficient technology, and this technological development may include increasing gear, the starter of new concept, efficient double pump System, fusion hybridization (fusion hybrid) technology, can merge speed changer from automatic/hand and hybrid gearbox spreads out Raw technology etc..
The special-purpose steel used in technology related with speed changer be used in the carrier of speed changer, gear, ring gear, In axis, synchronizer hub etc., and special-purpose steel can the about 58~62wt% of the total weight based on steel include in the car.Specifically, Pinion shaft, needle bearing and engine valve transmission base swing arm etc. for speed changer, due to reducing the need of weight and miniaturization It asks, has had already appeared high-intensitive to exploitation and high durable material continuous demands.For example, having used the chromium containing about 1.5wt% (Cr) SUJ2 steel.
However, miniaturization due to component such as bearing and size reduce caused by component deterioration increase, the material Durability may reduce, this may also result in the damage to surface.In turn, when not lubricating, surface temperature can be can increase, Hardness in high temperature and high revolving speed environment may be decreased.
In particular, to for by rotary shaft be fixed to predetermined position, support shaft weight and be applied to the load of axis and make axis The bearing of rotation, repeating load can proportionally apply with revolution, therefore, in order to bear to repeat load, need the resistance to of its material Fatigability, wearability etc..
For example, by converter or electric furnace make steel, while maintaining strongly reducing atmosphere cast ladle refining with Reduce the amount of non-metallic inclusion and in the state that oxygen content is reduced to about 12ppm or less by vacuum degassing process Further purification is to manufacture bearing steel.Hereafter, the bearing steel of purification is frozen by slab or steel ingot by casting technique, is split DIFFUSION TREATMENT is stitched to remove the segregation at the center for being present in the material and big carbide, and is rolled.Hereafter, for implementation Strong slow cool down operation in steel rolling mill softener material to generate bearing steel wire rod or pole stock, and by nodularization heat at Wire rod produced is fabricated to bearing products by reason, forging, quenching, tempering and process of lapping etc..
In above-mentioned manufacturing process, the heat treatment process for nodularization mainly passes through to be diffused at high temperature, and shape At spherical particle by be similar to Ostwald cure principle growth process to form spherodized structure.
However, nodularization needs to spend a very long time since nodularization heat treatment process needs the growth of spherical particle, because This manufacturing cost increases.In this way, possibly can not be obtained when the bearing deterioration due to caused by miniaturization, size reduction etc. increases Enough intensity and viability.
Therefore, the present inventor attempts to develop by generation nodularization double carbide a kind of for example strong with improved physical property The bearing steel and its manufacturing method of degree and viability.
Summary of the invention
The present invention provides a kind of tool by imperceptibly forming nodularization double carbide in bearing steel in a preferred aspect, There is the bearing steel of improved intensity, viability etc..Especially, which can pass through the component of the alloy of adjusting bearing steel It is manufactured with content and control process conditions.
Exemplary embodiments of the present invention provide a kind of alloy composite for bearing steel, may include: being based on The total weight of the alloy composite, the carbon (C) of about 0.8~1.0wt%, the silicon (Si) of about 0.35~0.9wt%, about 0.5~ The manganese (Mn) of 1.0wt%, the nickel (Ni) of about 0.6~1.5wt%, about 1.2~1.55wt% chromium (Cr), about 0.2~0.5wt% Molybdenum (Mo), the aluminium (Al) of about 0.01~0.06wt%, the copper (Cu) of about 0.01~0.1wt% and constitute alloy composite surplus Iron (Fe).The alloy composite also includes selected from greater than 0wt% and being about 0.38wt% or less vanadium (V) and be greater than 0wt% and be about 0.02wt% or one of less niobium (Nb) or a variety of.
Preferably, which can also be also comprising about 0.006wt% or less nitrogen (N), about 0.001wt% or more Few oxygen (O), about 0.03wt% or less phosphorus (P) and about 0.01wt% or less sulphur (S) etc..
It is understood that all wt% (wt%) herein referred to are all based on the total weight of alloy composite, unless separately It is described.
Alloy composite of the invention is additionally provided, can be made of said components, or can be substantially by above-mentioned group It is grouped as.For example, the composition for being used for bearing steel can be composed of the following components, or it is consists essentially of: Total weight based on alloy composite, the carbon (C) of about 0.8~1.0wt%, the silicon (Si) of about 0.35~0.9wt%, about 0.5~ The manganese (Mn) of 1.0wt%, the nickel (Ni) of about 0.6~1.5wt%, about 1.2~1.55wt% chromium (Cr), about 0.2~0.5wt% Molybdenum (Mo), the aluminium (Al) of about 0.01~0.06wt%, the copper (Cu) of about 0.01~0.1wt% and constitute alloy composite surplus Iron (Fe).In addition, the alloy composite can be composed of the following components, or it is consists essentially of: based on institute State the total weight of alloy composite, the carbon (C) of about 0.8~1.0wt%, the silicon (Si) of about 0.35~0.9wt%, about 0.5~ The manganese (Mn) of 1.0wt%, the nickel (Ni) of about 0.6~1.5wt%, about 1.2~1.55wt% chromium (Cr), about 0.2~0.5wt% Molybdenum (Mo), the aluminium (Al) of about 0.01~0.06wt%, the copper (Cu) of about 0.01~0.1wt%, selected from being greater than 0wt% and be about 0.38wt% or less vanadium (V) and be greater than 0wt% and be about 0.02wt% or one of less niobium (Nb) or it is a variety of and Constitute the iron (Fe) of alloy composite surplus.
On the other hand, the present invention provides a kind of method for manufacturing bearing steel.This method may include:
720~850 DEG C at a temperature of by containing alloy composite wire rod be heat-treated 4~8 hours, with nodularization composite carbon Compound；
By the wire rod wire drawing of the heat treatment；
720~850 DEG C at a temperature of by wire rod secondary heat treatment 4~8 hours of wire drawing, with nodularization double carbide；
The wire rod of secondary heat treatment is forged to form bearing steel；With
Quenching is quickly cooled down, and is tempered the bearing steel of formation.
Especially, which can have following components, and the component includes the total weight based on alloy composite, The carbon (C) of about 0.8~1.0wt%, the silicon (Si) of about 0.35~0.9wt%, the manganese (Mn) of about 0.5~1.0wt%, about 0.6~ The nickel (Ni) of 1.5wt%, the chromium (Cr) of about 1.2~1.55wt%, the molybdenum (Mo) of about 0.2~0.5wt%, about 0.01~ The aluminium (Al) of 0.06wt%, the copper (Cu) of about 0.01~0.1wt% and the iron (Fe) for constituting alloy composite surplus.The alloy group It closes object also and may include selected from greater than 0wt% and being about 0.38wt% or less vanadium (V) and be greater than 0wt% and be about 0.02wt% Or one of less niobium (Nb) or a variety of.In turn, above-mentioned alloy composite may also comprise about 0.006wt% or less nitrogen (N), about 0.001wt% or less oxygen (O), about 0.03wt% or less phosphorus (P) and about 0.01wt% or less sulphur (S)。
Term " carbide complex " as used herein refers to including at least carbon and is positive or portion when in conjunction with carbon Divide the compound of other elements of positive lower electronegativity.Carbide complex can be at least properly formed with carbon and metal, And the metal can be alkali metal, alkaline-earth metal or transition metal, late transition metal, group of the lanthanides or actinium series, there is no limit.
Term as used herein " spheroidising " or " nodularization " refer to a kind of heat treatment process, in particular for iron-based conjunction Jin Gang or combinations thereof object.Specifically, spheroidising may refer to heat treatment process, will include carbide in iron-based steel or The shape or crystal form of the carbon of carbide complex become, such as spherical form, sphere or ellipse, to provide required object Rationality can such as mechanical strength, heat-resisting quantity, ductility, machinability.In spheroidising, temperature, which can increase to, surpasses iron Base alloy-steel.
Preferably, quenching can about 840~860 DEG C at a temperature of carry out about 0.5~2 hour, and being tempered can be It is carried out at a temperature of about 150~190 DEG C about 0.5~2 hour.
Preferably, the double carbide may include selected from M3C、M7C3、M23C6With one of MC carbide or a variety of, When M is metal, or especially transition metal when.
Preferably, the M3C、M7C3And M23C6M in carbide can be selected from one in chromium (Cr), iron (Fe) and manganese (Mn) Kind is a variety of.
Preferably, the M in the MC carbide is in chromium (Cr), iron (Fe), vanadium (V), niobium (Nb) and molybdenum (Mo) It is one or more.
A kind of vehicle part is also provided, can be made of the bearing steel of above-mentioned alloy composite.
In this way, composition according to the present invention, bearing steel can be used promote the thickness of vehicle to reduce, weight saving, The freedom degree etc. of design, and its cost can be effectively reduced by imperceptibly forming double carbide etc. in bearing steel, with Improve intensity, hardness, the fatigue life etc. of bearing steel, and promotes highly enriched.
Specific embodiment
Term or word used in specification and claims should not be construed as limited by common or dictionary meanings, And should be interpreted that with the meaning and concept for meeting technical spirit of the invention, term can suitably be defined based on inventor Concept come describe in the best way his/her invention principle.
It should be understood that term "comprising" and/or " comprising " when used in this manual, specify defined spy The presence of sign, integer, step, operations, elements, and/or components, but it is not excluded for one or more other features, integer, step, behaviour Make, the presence or addition of component, assembly unit and/or their combination.As used herein term "and/or" includes one or more Any and all combinations in project listed by a correlation.
Unless stated otherwise or from context it is clear that the term as used herein " about " be interpreted as it is normal in this field In the margin of tolerance, such as in 2 standard deviations of average value." about " can be understood as specified value 10%, 9%, 8%, 7%, in 6%, 5%, 4%, 3%, 2%, 1%, 0.5%, 0.1%, 0.05% or 0.01%.Unless clearly may be used from the context See, numerical value provided in this article is all modified by term " about ".
It will also be appreciated that term as used herein " vehicle " or " vehicle or other similar term generally include Motor vehicles such as include the car of sport utility vehicle (SUV), bus, truck, various commerial vehicles, including various ships The ship of ship and naval vessel, aircraft etc., and including hybrid vehicle, electric car, plug-in hybrid vehicle, hydrogen power Vehicle and other alternative fuel vehicles (such as fuel derived from non-oil resource).As mentioned in this article, hybrid electric vehicle It is that there is the vehicle of two or more power sources, such as petrol power and electrodynamic vehicle.
Hereinafter, the present invention is described in detail.The present invention relates to a kind of with improved fatigue durability, such as Intensity, hardness and the bearing steel of fatigue life and its manufacturing method, the bearing steel can be applied to vehicle etc. engine and In transmission device.
A kind of alloy composite for bearing steel may include: carbon (C), silicon (Si), manganese (Mn), nickel (Ni), chromium (Cr), molybdenum (Mo), aluminium (Al) and copper (Cu), and constitute the iron (Fe) of alloy composite surplus.The alloy composite also may include selected from vanadium (V) and one of niobium (Nb) or a variety of.In addition, alloy composite also may include selected from nitrogen (N), oxygen (O), phosphorus (P) and sulphur (S) One of or it is a variety of.
Preferably, which may include: the total weight based on alloy composite, the carbon of about 0.8~1.0wt% (C), the silicon (Si) of about 0.35~0.9wt%, the manganese (Mn) of about 0.5~1.0wt%, the nickel (Ni) of about 0.6~1.5wt%, about The chromium (Cr) of 1.2~1.55wt%, the molybdenum (Mo) of about 0.2~0.5wt%, the aluminium (Al) of about 0.01~0.06wt%, about 0.01 The copper (Cu) of~0.1wt% and the iron (Fe) for constituting alloy composite surplus.Alternatively, the alloy composite may include: based on conjunction The total weight of golden composition, silicon (Si), the about 0.5~1.0wt% of the carbon (C) of about 0.8~1.0wt%, about 0.35~0.9wt% Manganese (Mn), the nickel (Ni) of about 0.6~1.5wt%, the chromium (Cr) of about 1.2~1.55wt%, about 0.2~0.5wt% molybdenum (Mo), the aluminium (Al) of about 0.01~0.06wt%, the copper (Cu) of about 0.01~0.1wt%, selected from being greater than 0wt% and be about 0.38wt% or less vanadium (V) and it is greater than 0wt% and is about 0.02wt% or one of less niobium (Nb) or a variety of, and Constitute the iron (Fe) of alloy composite surplus.
It specifically, may include the double carbide etc. of nodularization for the alloy composite of bearing steel, and their shape At can substantially be influenced by element such as vanadium (V) and niobium (Nb).
Double carbide may include selected from M3C、M7C3、M23C6With one of MC carbide or a variety of, when M be metal or When transition metal, sediment etc. can be.The intensity of bearing steel, hardness can be improved in double carbide including above-mentioned carbide Deng, and extend viability etc..
Specifically, the M3C、M7C3And M23C6M in carbide may include in chromium (Cr), iron (Fe) and manganese (Mn) It is one or more, and the M in the MC carbide may include selected from chromium (Cr), iron (Fe), vanadium (V), niobium (Nb) and molybdenum One of (Mo) or it is a variety of.
Hereinafter, each ingredient of alloy composite will be described in detail.
(1) carbon (C)
As used herein carbon (C) can be improved the intensity of steel and stablize remaining austenite.Carbon can be based on composition Total weight is included in alloy composite with the amount of about 0.8~1.0wt%.It, may when carbon (C) content is less than about 0.8wt% The intensity of steel cannot be fully obtained, and may cause the reduction etc. of fatigue strength.When carbon (C) content is greater than about 1.0wt% When, undissolved big carbide can be retained, to reduce fatigue strength, viability etc., and reducing before quenching can Processability etc..It is therefore preferred that carbon (C) content is about 0.8~1.0wt%.
(2) silicon (Si)
Silicon (Si) used herein can be deoxidier, and facilitate the intensity for increasing steel by solid solution strengthening effect, And improve the activity of carbon (C).Silicon can the total weight based on composition alloy group is included in the amount of about 0.35~0.9wt% It closes in object.When silicon (Si) content is less than about 0.35wt%, oxide is not enough to remove, and remains in the steel of generation, from And make the strength deterioration of steel, and possibly can not obtain enough solid solution strengthening effects.When silicon (Si) content is greater than 0.9wt% When, decarburization can occur by osmosis in the tissue, such as anti-by excessive silicon (Si) and carbon (C) generation site competition Answer, and due to before quenching the increase processability of hardness can reduce rapidly.It is therefore preferred that silicon (Si) content is about 0.35~0.9wt%.
(3) manganese (Mn)
As herein manganese (Mn) used the hardenability and toughness of steel can be improved, so as to improve resistance to rolling fatigue life characteristic Deng.Manganese can the total weight based on composition be included in alloy composite with the amount of about 0.5~1.0wt%.When manganese (Mn) contains When amount is less than about 0.5wt%, possibly sufficient hardenability can not be obtained, accordingly, it is possible to reduce processability.When manganese (Mn) content is big When about 1.0wt%, the processability before quenching and fatigue life can be reduced, and the center segregation of MnS reduction may be made heavy It forms sediment.It is therefore preferred that manganese (Mn) content is about 0.5~1.0wt%.
(4) nickel (Ni)
As herein nickel (Ni) used may be used to the micronization of crystal grain steel, improve solution strengthening, matrix is strengthened, low temperature Impact flexibility, harden ability etc. reduce the temperature of A1 transformation temperature, promote the expansion of austenite structure, and improve carbon activity etc..Nickel can It is included in alloy composite with the total weight based on composition with the amount of about 0.6~1.5wt%.When nickel (Ni) content is less than about When 0.6wt%, it may be unable to fully obtain the effect of crystal grain micronization, and possibly can not obtain sufficient improvement, such as Solution strengthening and matrix are strengthened.When nickel (Ni) content is greater than about 1.5wt%, red brittleness etc. may occur in steel.Therefore, Preferably, nickel (Ni) content is 0.6~1.5wt%.
(5) chromium (Cr)
As herein chromium (Cr) used the hardenability of steel can be improved, harden ability is provided, and at the same time keeping the tissue of steel micro- Dusting and nodularization.Chromium can the total weight based on composition be included in alloy composite with the amount of about 1.2~1.55wt%.When When chromium (Cr) content is less than about 1.2wt%, then hardenability and harden ability may be limited, and possibly can not be obtained adequately The micronization and nodularization of tissue.When chromium (Cr) content is greater than about 1.55wt%, the effect for increasing content may not be enough, therefore Increase manufacturing cost.It is therefore preferred that chromium (Cr) content is about 1.2~1.55wt%.
(6) molybdenum (Mo)
As herein molybdenum (Mo) used can improve the tired of steel by increasing hardenability or the intensity of steel after tempering The labor service life.Molybdenum can the total weight based on composition be included in alloy composite with the amount of about 0.2~0.5wt%.Work as molybdenum (Mo) content be less than about 0.2wt% when, the fatigue life of steel may be unable to fully improve, when molybdenum (Mo) content be greater than 0.5wt%, Machinability and productivity of steel etc. may reduce.It is therefore preferred that molybdenum (Mo) content is about 0.2~0.5wt%.
(7) aluminium (Al)
As herein aluminium (Al) used can be used as strong deoxidier, and cleannes of steel caused by improving.In turn, Al can react in steel with nitrogen (N) to form nitride, so that crystal grain be made to be micronized.Aluminium can be based on the total weight of composition It is included in alloy composite with the amount of about 0.01~0.06wt%.When aluminium (Al) content is less than about 0.01wt%, then may Adequately effect relevant to the micronization of deoxidier, cleaning and crystal grain can not be obtained.When aluminium (Al) content is greater than about When 0.06wt%, coarse oxide inclusion etc. can be formed to reduce the fatigue life etc. of steel.It is therefore preferred that aluminium (Al) Content is about 0.01~0.06wt%.
(8) copper (Cu)
As herein copper (Cu) used can improve the harden ability of steel etc..Copper can the total weight based on composition with about The amount of 0.01~0.1wt% is included in alloy composite.When copper (Cu) content is less than about 0.01wt%, possibly can not obtain The effect that enough harden ability improves, when copper (Cu) content is greater than about 0.1wt%, due to that can exceed that solid solubility limits System, the effect that the intensity of steel improves may be saturated to increase manufacturing cost, and lead to red brittleness.It is therefore preferred that copper (Cu) Content is about 0.01~0.1wt%.
(9) vanadium (V)
As herein vanadium (V) used can form sediment such as carbide etc., passing through precipitating enhancement effect enhances matrix Tissue improves intensity and wearability, and is micronized crystal grain, and can be highly strong under the cooling rate relatively the same with SUJ2 Change.Vanadium can the total weight based on composition to be greater than 0wt% and be about 0.38wt% or less amount is included in alloy combination In object.When vanadium (V) content is greater than about 0.38wt%, the toughness and hardness of steel may be greatly reduced.It is therefore preferred that vanadium (V) content is greater than 0wt% and is about 0.38wt% or less.
(10) niobium (Nb)
As herein niobium (Nb) used can be at high temperature respectively in conjunction with carbon and nitrogen, to promote carbide and nitride It is formed, and improves the intensity and low-temperature flexibility of steel.Niobium can the total weight based on composition to be greater than 0wt% and be about 0.02wt% or less amount are included in alloy composite.It is strong due to steel when niobium (Nb) content is greater than about 0.02wt% The improvement rate of degree and low-temperature flexibility has dropped compared with increased content, may this compared to the benefit manufacturing cost that can be obtained It is increased in matter.In addition, niobium (Nb) is likely to be present in the solid solution state in ferrite when content is more than above range In, therefore impact flexibility may reduce.It is therefore preferred that niobium (Nb) content is greater than 0wt% and is about 0.02wt% or more It is few.
(11) nitrogen (N)
Nitrogen (N) can be impurity, can react to form AlN with aluminium (Al), to reduce the viability etc. of steel.Cause This, it is preferable that it is about 0.006wt% or less that nitrogen (N) content, which is limited in the total weight based on composition,.
(12) oxygen (O)
Oxygen (O) can be impurity, reduce the cleanliness of steel, and so that steel is degenerated by contact fatigue.It is therefore preferred that It is about 0.001wt% or less that oxygen (O) content, which is limited in the total weight based on composition,.
(13) phosphorus (P)
Phosphorus (P) can be impurity, induces cyrystal boundary segregation, reduces the toughness of steel.It is therefore preferred that phosphorus (P) content quilt It is about 0.03wt% or less for being limited in the total weight based on composition.
(14) sulphur (S)
The machinability of steel can be improved in sulphur (S), is easier processing, but sulphur (S) can reduce steel by cyrystal boundary segregation Toughness, and can react to form MnS with manganese (Mn), to reduce the fatigue life of steel.It is therefore preferred that sulphur (S) content is limited System is about 0.01wt% or less in the total weight based on composition.
The bearing steel that various typical embodiments according to the present invention contain alloy composite as a result, can have the resistance to of improvement Fatigability, therefore, bearing steel can be applied in auto parts etc..Specifically, bearing steel can be applied to vehicle etc. engine and In the bearing of speed changer.
Hereinafter, on the other hand, there is the side of the bearing steel of improved fatigue durability the present invention relates to a kind of manufacture Method.
The method of bearing steel of the manufacture with improved fatigue durability may include: the at a temperature of general at 720~850 DEG C Wire rod containing alloy composite is heat-treated 4~8 hours, so that double carbide nodularization；By the wire rod wire drawing of heat treatment；? By the wire rod secondary heat treatment of wire drawing 4~8 hours at a temperature of 720~850 DEG C, so that double carbide nodularization；It forges secondary The wire rod of heat treatment, to form bearing steel；Quenching is quickly cooled down, and by the bearing steel tempering of formation.
Specifically, which may include: the total weight based on the alloy composite, about 0.8~1.0wt%'s Carbon (C), the silicon (Si) of about 0.35~0.9wt%, the manganese (Mn) of about 0.5~1.0wt%, about 0.6~1.5wt% nickel (Ni), The chromium (Cr) of about 1.2~1.55wt%, the molybdenum (Mo) of about 0.2~0.5wt%, the aluminium (Al) of about 0.01~0.06wt%, about The copper (Cu) of 0.01~0.1wt% and the iron (Fe) for constituting alloy composite surplus.Alternatively, the alloy composite may include: base In the total weight of the alloy composite, the carbon (C) of about 0.8~1.0wt%, the silicon (Si) of about 0.35~0.9wt%, about 0.5 The manganese (Mn) of~1.0wt%, the nickel (Ni) of about 0.6~1.5wt%, the chromium (Cr) of about 1.2~1.55wt%, about 0.2~ The molybdenum (Mo) of 0.5wt%, the aluminium (Al) of about 0.01~0.06wt%, the copper (Cu) of about 0.01~0.1wt%, selected from being greater than 0wt% and be about 0.38wt% or less vanadium (V) and be greater than 0wt% and be about 0.02wt% or less niobium (Nb) in one Kind is a variety of, and constitutes the iron (Fe) of alloy composite surplus.
In the method for manufacturing the bearing steel, it can be formed in the steel (alloy composite) and the nodularization double carbide, And the double carbide may include selected from MC, M for sediment7C3、M23C6With one of MC carbide or a variety of, work as M When being metal or transition metal.Intensity and hardness of bearing steel etc. can be improved in double carbide including above-mentioned carbide, and Extend viability etc..
Preferably, MC, M7C3And M23C6M in carbide may include selected from one of chromium (Cr), iron (Fe) and manganese (Mn) Or it is a variety of, and the M in MC carbide may include selected from one of chromium (Cr), iron (Fe), vanadium (V), niobium (Nb) and molybdenum (Mo) Or it is a variety of.
Quench about 840~860 DEG C at a temperature of carry out 0.5~2 hour, and it is described tempering at about 150~190 DEG C At a temperature of carry out 0.5~2 hour.
When hardening heat is below about 840 DEG C or the cool time is less than about 0.5 hour, due to that may not be able to be formed uniformly It is quenched tissue, it may occur however that material deviation.When hardening heat is greater than about 860 DEG C or the sudden fiery time is greater than about 2 hours, by primary The spherical double carbide to be formed is heat-treated with secondary nodularization to be dissolved.
In addition, possibly can not be obtained enough when tempering temperature is below about 150 DEG C or tempering time is less than about 0.5 hour Physical property such as bearing steel toughness.When tempering temperature is greater than about 190 DEG C or tempering time is greater than about 2 hours, due to axis Holding hardness of steel etc. can reduce rapidly, it may be difficult to improve viability.
When the heat treatment temperature and secondary heat treatment temperature to nodularization double carbide can respectively be less than about 720 DEG C or When nodularization heat treatment time is less than about 4 hours, it may be necessary to be used for double carbide a large amount of nodularization times, therefore manufacturing cost can It increases sharply.
On the other hand, when primary and secondary heat treatment temperature is greater than about 850 DEG C, since the double carbide of formation may A possibility that dissolving, forming sheet type double carbide during cooling rather than spherical double carbide can dramatically increase.
When primary and two heat treatment times are greater than about 8 hours, the Oxygen potential of double carbide may decline with fast Speed increases manufacturing cost.
Embodiment
Hereinafter, the present invention is described in more detail by embodiment.These embodiments are merely to illustrate this hair Bright, the scope of the present invention is not construed as being limited to these embodiments, this it will be apparent to those skilled in the art that.
It is according to the present invention such as hardness and durability in order to check the physical property of bearing steel made according to the present invention Manufacturing method manufactures the comparative example 1~10 with the composition as described in the following table 1 and the reality with the composition as described in the following table 2 Apply example 1~3.
[table 1]
[table 2]
In the comparative example 1~10 of table 1 and the Examples 1 to 3 of table 2, in the fabrication process, a treatment temperature set It is about 800 DEG C, secondary heat treatment temperature is set as about 720 DEG C, and hardening heat and time are respectively set as about 850 DEG C and about 1 small When, tempering temperature and time are respectively set as about 150 DEG C and about 1 hour.
It here, comparative example 1~10 does not include one of vanadium (V) and niobium (Nb) or a variety of, or even if include a kind of or more Kind, the content range of vanadium (V) or niobium (Nb) has exceeded content range of the invention, or even if vanadium (V) or niobium (Nb) content model The satisfaction present invention is enclosed, the content range of one or more residual components is unsatisfactory for content range of the invention.
On the contrary, Examples 1 to 3 includes one or more of vanadium (V) and niobium (Nb), content range meets of the invention Content range, the content range of residual components also meet content range of the invention.
As described above, having the physical of discrepant comparative example 1~10 and Examples 1 to 3 on its composition to check Difference between energy is compared the physical property, and is arranged in table 3.
[table 3]
In table 3, hardness at room temperature, the hardness at 300 DEG C, the surface stress conditions of 6.2GPa at 150 DEG C Under to the revolution of the rotary bending fatigue test in L10 service life, and in view of these hardness and revolution compare comparative example and reality Apply the viability of example.
Here, it in the case where hardness, uses and uses micro-vickers hardness tester [Manufacturer:Future Tech, Model:FM-700] KS B 0811 measure.It is such as visible by table 3, it can be seen that in about 25 DEG C of at room temperature hard Degree is higher by about 11% than in comparative example 1~10 in Examples 1 to 3, and the hardness at 300 DEG C is in Examples 1 to 3 than right It is also high by about 16% in ratio 1~10.
The revolution of rotary bending tester is measured at 150 DEG C, and is made by 1143 measuring method of KS B ISO With the L10 service life of the standard linear diameter of rotary bending tester measurement 4mm.The L10 service life is the rated fatigue service life of sample, And mean the total revolution for being destroyed rotary bending tester until the 10% of sample.
. in this case it can be seen that at 150 DEG C, under the surface stress conditions of 6.2GPa, about the L10 service life In the case where the revolution of rotary bending tester, the average value of Examples 1 to 3 is 18399000 times, and than comparative example 1 Average value 9009000 times of~10 are higher by about 2 times.
In order to compare the resistance to of comparative example 1~10 and Examples 1 to 3 on the basis of the revolution of rotary bending tester In the long property service life, the revolution of the rotary bending tester of 8400000 comparative examples 1 is set as to 100% durability longevity The standard of life, and the rotary bending tester based on comparative example 1 is as standard, by comparative example 2~10 and Examples 1 to 3 Rotary bending tester revolution between increased or decrease and be expressed as percentage.
That is, the percentage of the viability for comparing comparative example 1~10 and Examples 1 to 3 is indicated based on comparison The relative increase and reduction of the revolution of the rotary bending tester of example 1, remaining comparative example 2~10 and Examples 1 to 3.
Here, compared by the viability of comparative example and embodiment, it can be seen that with rotary bending tester Revolution it is the same, the viability of Examples 1 to 3 is higher by about twice than the viability of comparative example 1~10.
As described above, in order to check why embodiment hardness and viability than the more preferable reason of comparative example, The type and vol% of the double carbide for including in comparative example 1 and Examples 1 to 3 are described in the following table 4.
[table 4]
In table 4, compare include comparative example 1 and the double carbide in example 1~3 content.As shown in table 4, it compares Double carbide in example 1 mainly includes Me3C and a small amount of MoC, but Examples 1 to 3 relatively consistently include VC and NbC with And Me3C and MoC.This species diversity on the composition of double carbide may be considered why embodiment has more than comparative example The reason of good hardness and viability.
It therefore, can be with experiments prove that meet component according to the present invention and content range, and by according to the present invention The Examples 1 to 3 of heat treatment process manufacture include various double carbides etc., and therefore have more than comparative example 1~10 Good intensity and viability.
As described above, the present invention is illustrated various exemplary implementation schemes of the invention, but the embodiment party Case is merely illustrative, and the invention is not limited thereto.Without departing from the scope of the invention, those skilled in the art can To be altered or modified about embodiment described in the invention, wanted in technical spirit of the invention and the right being described below It asks in the equivalency range of book, variations and modifications are all possible.

Claims (10)

1. a kind of alloy composite for bearing steel, it includes:
The carbon (C) of 0.8~1.0wt%；
The silicon (Si) of 0.35~0.9wt%；
The manganese (Mn) of 0.5~1.0wt%；
The nickel (Ni) of 0.64~1.5wt%；
The chromium (Cr) of 1.2~1.55wt%；
The molybdenum (Mo) of 0.22~0.5wt%；
The aluminium (Al) of 0.01~0.06wt%；
The copper (Cu) of 0.01~0.1wt%；
Selected from being greater than 0wt% and be 0.38wt% or less vanadium (V) and greater than 0wt% and be 0.02wt% or less niobium One of (Nb) or it is a variety of；And the iron (Fe) of alloy composite surplus is constituted,
All wt% are based on the total weight of the alloy composite.
2. alloy composite according to claim 1, wherein the alloy composite also includes 0.006wt% or less Nitrogen (N), 0.001wt% or less oxygen (O), 0.03wt% or less phosphorus (P) and 0.01wt% or less sulphur (S), institute Some wt% are based on the total weight of the alloy composite.
3. alloy composite according to claim 1, composed of the following components:
The carbon (C) of 0.8~1.0wt%；
The silicon (Si) of 0.35~0.9wt%；
The manganese (Mn) of 0.5~1.0wt%；
The nickel (Ni) of 0.64~1.5wt%；
The chromium (Cr) of 1.2~1.55wt%；
The molybdenum (Mo) of 0.22~0.5wt%；
The aluminium (Al) of 0.01~0.06wt%；
The copper (Cu) of 0.01~0.1wt%；
Selected from being greater than 0wt% and be 0.38wt% or less vanadium (V) and greater than 0wt% and be 0.02wt% or less niobium One of (Nb) or it is a variety of, and
The iron (Fe) of the alloy composite surplus is constituted,
All wt% are based on the total weight of the alloy composite.
4. a kind of method for manufacturing bearing steel comprising following steps:
720~850 DEG C at a temperature of by containing alloy composite wire rod be heat-treated 4~8 hours, with nodularization compound carbonizing Object；
By the wire rod wire drawing of the heat treatment；
720~850 DEG C at a temperature of by wire rod secondary heat treatment 4~8 hours of the wire drawing, with nodularization double carbide；
The wire rod of the secondary heat treatment is forged, to form bearing steel；With
Quenching is quickly cooled down, and is tempered the bearing steel of the formation, wherein the alloy composite includes: being based on the alloy The total weight of composition, the carbon (C) of 0.8~1.0wt%, the silicon (Si) of 0.35~0.9wt%, 0.5~1.0wt% manganese (Mn), the nickel (Ni) of 0.6~1.5wt%, the chromium (Cr) of 1.2~1.55wt%, the molybdenum (Mo) of 0.2~0.5wt%, 0.01~ The aluminium (Al) of 0.06wt%, the copper (Cu) of 0.01~0.1wt% and the iron (Fe) for constituting the alloy composite surplus,
Wherein it is described quenching 840~860 DEG C at a temperature of carry out 0.5~2 hour, and it is described tempering at 150~190 DEG C At a temperature of carry out 0.5~2 hour.
5. according to the method described in claim 4, wherein the alloy composite also includes to be selected from greater than 0wt% and be 0.38wt% or less vanadium (V) and be greater than 0wt% and be one of 0.02wt% or less niobium (Nb) or a variety of, institute Some wt% are based on the total weight of the alloy composite.
6. according to the method described in claim 4, wherein the double carbide includes being selected from M3C、M7C3、M23C6It is carbonized with MC One of object is a variety of, and wherein M is transition metal.
7. according to the method described in claim 6, the wherein M3C、M7C3And M23C6M in carbide is selected from chromium (Cr), iron (Fe) and one of manganese (Mn) or a variety of.
8. according to the method described in claim 6, wherein the M in the MC carbide be selected from chromium (Cr), iron (Fe), vanadium (V), One of niobium (Nb) and molybdenum (Mo) are a variety of.
9. a kind of vehicle part, it includes alloy composites according to claim 1.
10. vehicle part according to claim 9, wherein the vehicle part is the bearing of engine or speed changer.
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Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1950531A (en) * 2004-04-28 2007-04-18 杰富意钢铁株式会社 Member for machine construction and production method therefor
CN103890209A (en) * 2011-10-20 2014-06-25 新日铁住金株式会社 Bearing steel and method for producing same

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH09329147A (en) * 1996-04-10 1997-12-22 Nippon Seiko Kk Water resistant long-life rolling bearing
JP3463651B2 (en) * 2000-04-18 2003-11-05 住友金属工業株式会社 Bearing steel
JP5820326B2 (en) * 2012-03-30 2015-11-24 株式会社神戸製鋼所 Steel for bearings with excellent rolling fatigue characteristics and method for producing the same
JP5990428B2 (en) * 2012-08-21 2016-09-14 株式会社神戸製鋼所 Steel for bearings with excellent rolling fatigue characteristics and method for producing the same
DE102015220299A1 (en) * 2014-11-21 2016-05-25 Hyundai Motor Company Bearing steel with improved durability and method for producing desselbigen
KR101685490B1 (en) * 2015-06-22 2016-12-13 현대자동차주식회사 Bearing alloy steel improved fatigue durability and the method of manufacturing the same

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1950531A (en) * 2004-04-28 2007-04-18 杰富意钢铁株式会社 Member for machine construction and production method therefor
CN103890209A (en) * 2011-10-20 2014-06-25 新日铁住金株式会社 Bearing steel and method for producing same

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