CN106256917A - There is bearing steel and the manufacture method thereof improving fatigue durability - Google Patents

There is bearing steel and the manufacture method thereof improving fatigue durability Download PDF

Info

Publication number
CN106256917A
CN106256917A CN201510760961.7A CN201510760961A CN106256917A CN 106256917 A CN106256917 A CN 106256917A CN 201510760961 A CN201510760961 A CN 201510760961A CN 106256917 A CN106256917 A CN 106256917A
Authority
CN
China
Prior art keywords
less
steel
compositions
steel compositions
gross weight
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
CN201510760961.7A
Other languages
Chinese (zh)
Other versions
CN106256917B (en
Inventor
车星澈
洪承贤
高永尚
丁友相
徐镇裕
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Hyundai Motor Co
Original Assignee
Hyundai Motor Co
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Hyundai Motor Co filed Critical Hyundai Motor Co
Publication of CN106256917A publication Critical patent/CN106256917A/en
Application granted granted Critical
Publication of CN106256917B publication Critical patent/CN106256917B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • 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
    • 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
    • C22C38/18—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

Landscapes

  • 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)
  • Heat Treatment Of Articles (AREA)
  • Rolling Contact Bearings (AREA)

Abstract

The present invention relates to a kind of for having the steel compositions and manufacture method thereof improving fatigue durability.Steel compositions comprises: the carbon (C) of about 0.08wt% to 1.0wt%；The silicon (Si) of about 0.9wt% to 1.6wt%；Phosphorus (P) more than 0wt% and about 0.03wt% or less；Sulfur (S) more than 0wt% and about 0.01wt% or less；The copper (Cu) of about 0.01wt% to 0.1wt%；The aluminum (Al) of about 0.01wt% to 0.06wt%；Nitrogen (N) more than 0wt% and about 0.006wt% or less；Oxygen (O) more than 0wt% and about 0.001wt% or less；One or more in the manganese (Mn) of about 0.5wt% to 1.00wt%, the nickel (Ni) of about 0.1wt% to 0.6wt%, the chromium (Cr) of about 1.4wt% to 1.55wt%, the molybdenum (Mo) of about 0.2wt% to 0.5wt% and the vanadium (V) more than 0wt% and about 0.4wt% or less；And the ferrum (Fe) of composition steel compositions surplus, all wt% are all based on the gross weight of steel alloy compositions.

Description

There is bearing steel and the manufacture method thereof improving fatigue durability
Cross reference to related applications
According to 35 U.S.C. § 119, this application claims that on June 22nd, 2015 produces at Korean Intellectual The priority of korean patent application No.10-2015-0088341 that power office submits to is complete disclosed in it Portion's content includes in way of reference into the application.
Technical field
The present invention relates to for having the composition of steel and manufacturer thereof improving fatigue durability bearing Method.Specifically, composition of steel can comprise hardness that the double carbide of nodularization substantially improves with offer, Intensity and toughness, and improve fatigue strength and fatigue life.
Background technology
Recently, environmental problem is risen in the whole world, therefore has sought to according to including all works Such problem of industry and the method that reduces fuel.Specifically, in order to reduce fuel consumption, car Industrial circle is it has been proposed that improve the fuel efficiency of vehicle motor and reduce the weight of vehicle. Such as, the weight by reducing vehicle can increase the fuel efficiency of vehicle.But, when reducing car Weight time, it may appear that problem is because intensity and durability required for vehicle can not obtain To meeting.So, the maximum target of automotive industry is to solve this problem.
Therefore, under eco-friendly trend, in automotive industry, have based on European directive By 2021, the discharge capacity of carbon dioxide is reduced to the 27% of 95g/km its discharge capacity the most current The various environmentally friendly vehicle of target be developed.Further, in order to meet in the U.S. To 2025 corporation average fuel economy (CAFE) the 54.5mpg of setting (23.1km/l), vehicular manufacturer's development technique is to reduce size and to improve fuel economy.
Generally, along with increase or the increase of additional components weight of number of components, should reduce and be used for The weight of these component materials.In this case, reduce method as weight, be used for realizing The material of high intensity or the heat treatment technics on hardened material surface have been frequently used.Further, Along with component shape complicates, accurate connection, low distortion weld and low deformation heat treatment technology Used.In addition, as the technology for reducing noise, reduce due to heat treatment The technology of the deformation caused and for reducing noise and removing the technology of dust and used.
Specifically, for making the high property of the maximized electromotor of vehicle fuel economy and variator Can and high efficiency technology be developed, and this technology can include the increase of gear quantity, the most general Read starter, high efficiency double pump system, the hybrid technology of fusion, relate to automatic/hand fusion Variator and the technology etc. of hybrid transmission.
The steel alloy used in relating to electromotor and the such technology of variator is starting The carrier frame of machine parts, manually or automatically variator, ring gear, gear, axle, lock unit Hub etc. are used, and 32% can be corresponded approximately to based on engine weight within the engine and arrive 40% uses this steel alloy electromotor and in the transmission can be suitable based on gearbox weight Steel alloy is used in about 58wt% to 62wt%.Specifically, as transmission components such as, tooth Wheel or the material of axle, develop highly enriched and high durability material along with to reduce weight and The demand simplified persistently is needed.But, for parts miniaturization, reduce part dimension or change The technology entering fuel efficiency is the most problematic.Such as, increase when the load being applied on engine components Added-time, owing to burning, rubbing, abrasion etc., the quality of parts can be lowered and viability Can be reduced.Further, since the increase of parts rigidity and the shortage of durable material, can occur Surface damage, and when steel alloy uses in the situation not having lubricant, surface temperature can be increased, Thus hardness can be lowered at high temperature or in needing a large amount of environment rotated.
Therefore, the durability of bearing steel needs to be reinforced in the related art.
Generally, the gear of transmission for vehicles is carried out engine power to directly transmitting differential system In system and transmit the parts of the effect of rotation or power between two or more axles, in order to make to send out Motivation power adapts to the driving condition of vehicle.Answer additionally, the gear of variator receives bending simultaneously Power and contact stress.In gear, when durable material deficiency, owing to lacking flexural fatigue Fatigue damage that intensity causes (tooth is damaged) and owing to lacking the fatigue that contact fatigue strength causes Damage (depression) may happen frequently.Therefore, in gear, need such as high rigidity, intensity, The physical property of toughness, fatigue strength and fatigue life.
In the related art, conventional bearings steel, such as include the ferrum (Fe) as main component, The carbon (C) of 1.00wt%, the silicon (Si) of 0.27wt%, the manganese (Mn) of 0.38wt%, 0.012wt% Phosphorus (P), the sulfur (S) of 0.005wt%, the copper (Cu) of 1.46wt%, the nickel of 0.05wt% (Ni), the chromium (Cr) of 1.46wt%, the molybdenum (Mo) of 0.02wt%, the aluminum of 0.017wt% (Al), the SUJ2 of the oxygen (O) of the nitrogen (N) of 0.0035wt% and 0.0006wt% is Through being typically employed.But, this steel in terms of durability problematic thus at surface damage In (peeling), problematic and pinion shaft pin abrasion is serious.
Therefore, the present inventor have been attempt to be developed for have improvement physical property such as hardness, The bearing of intensity, toughness, fatigue strength and fatigue life and the steel compositions of bearing steel, and Its manufacture method.
Summary of the invention
In preferred aspect, the present invention is provided to steel compositions and the manufacture method thereof of bearing.Steel Compositions can comprise the ferrum (Fe) as main component, carbon (C), silicon (Si), manganese (Mn), Phosphorus (P), sulfur (S), copper (Cu), nickel (Ni), chromium (Cr), molybdenum (Mo), aluminum (Al), nitrogen (N), oxygen (O) and vanadium (V) with improve physical property such as hardness, Intensity and toughness thus improve durability, fatigue strength and fatigue life.
The illustrative embodiments of the present invention provides the steel compositions for bearing, and it comprises: about 0.08wt% to 1.0wt% amount carbon (C), about 0.9wt% to 1.6wt% measure silicon (Si), More than 0wt% and about 0.03wt% or lesser amount of phosphorus (P), more than 0wt% and about 0.01 Wt% or lesser amount of sulfur (S), about 0.01wt% to 0.1wt% amount copper (Cu), about 0.01 The aluminum (Al) of wt% to 0.06wt% amount, more than 0wt% and about 0.006wt% or less amount Nitrogen (N), more than 0wt% and about 0.001wt% or lesser amount of oxygen (O)；And balance The ferrum (Fe) of steel compositions weight, all of wt% is all based on the gross weight of steel compositions.
Should be appreciated that all of weight % (wt%) as referred to herein is all based on steel or steel alloy Gross weight, unless otherwise indicated.
Additionally, the steel compositions of the present invention also can comprise manganese (Mn), and preferably, manganese (Mn) Content can be about the amount of 0.5wt% to 1.00wt%.
The steel compositions of the present invention also can comprise nickel (Ni), and preferably, nickel (Ni) contains Amount can be about the amount of 0.1wt% to 0.6wt%.
The steel compositions of the present invention also can comprise chromium (Cr), and preferably, chromium (Cr) contains Amount can be about the amount of 1.4wt% to 1.55wt%.
The steel compositions of the present invention also can comprise molybdenum (Mo), and preferably, molybdenum (Mo) contains Amount can be about the amount of 0.2wt% to 0.5wt%.
The steel compositions of the present invention also can comprise vanadium (V), and preferably, the content of vanadium (V) May be greater than 0wt% and the amount of about 0.4wt% or less.
Alternatively, the steel compositions of the present invention may also include selected from manganese (Mn), nickel (Ni), One or more in chromium (Cr), molybdenum (Mo) or vanadium (V), and preferably, manganese (Mn) Content can be about the amount of 0.5wt% to 1.00wt%, the content of nickel (Ni) can be about The amount of 0.1wt% to 0.6wt%, the content of chromium (Cr) can be about 1.4wt% to 1.55wt%'s Amount, the content of molybdenum (Mo) can be about the amount of 0.2wt% to 0.5wt%, and the containing of vanadium (V) Amount may be greater than 0wt% and the amount of about 0.4wt% or less.
Present invention also offers steel compositions or steel alloy compositions, it can be become be grouped into by above, Substantially become to be grouped into by above, or mainly become to be grouped into by above.Such as the steel of bearing Compositions can consist of the following composition, and substantially consists of the following composition, or by following component base This composition, following component is: the carbon (C) of about 0.08wt% to 1.0wt% amount；About 0.9wt% Silicon (Si) to 1.6wt% amount；More than 0wt% and about 0.03wt% or lesser amount of phosphorus (P)； More than 0wt% and about 0.01wt% or lesser amount of sulfur (S)；About 0.01wt% to 0.1wt% The copper (Cu) of amount；The aluminum (Al) of about 0.01wt% to 0.06wt% amount；More than 0wt% and It is about 0.006wt% or lesser amount of nitrogen (N)；More than 0wt% and about 0.001wt% or more A small amount of oxygen (O)；Constituting (Fe) of steel compositions surplus, all of wt% is all based on alloy The gross weight of steel compositions.Further, the steel compositions for bearing can consist of the following composition, Substantially consisting of the following composition, or be substantially made up of following component, following component is: about 0.08 The carbon (C) of wt% to 1.0wt% amount；The silicon (Si) of about 0.9wt% to 1.6wt% amount；Greatly In 0wt% and about 0.03wt% or lesser amount of phosphorus (P)；More than 0wt% and about 0.01 Wt% or lesser amount of sulfur (S)；The copper (Cu) of about 0.01wt% to 0.1wt% amount；About 0.01 The aluminum (Al) of wt% to 0.06wt% amount；More than 0wt% and about 0.006wt% or less amount Nitrogen (N)；More than 0wt% and about 0.001wt% or lesser amount of oxygen (O)；Selected from about 0.5wt% to 1.00wt% amount manganese (Mn), about 0.1wt% to 0.6wt% measure nickel (Ni), About 1.4wt% to 1.55wt% amount chromium (Cr), about 0.2wt% to 0.5wt% measure molybdenum (Mo), More than one or more in 0wt% and about 0.4wt% or lesser amount of vanadium (V)；And and structure Becoming (Fe) of steel compositions surplus, all of wt% is all based on the gross weight of steel alloy compositions.
Another illustrative embodiments of the present invention provides the method manufacturing bearing steel.The method Can comprise: manufacture the wire rod comprising steel alloy compositions；Heat treatment of wires is for first nodularization； By the wire rod wire drawing of heat treatment；Secondary heat treatment by the wire rod of wire drawing for secondary nodularization；Will The wire rod forging of secondary heat treatment；Quench the wire rod quenching that will be forged；And will be quenched Wire rod is tempered.
Specifically, steel alloy compositions can comprise: about 0.08wt% to 1.0wt% amount carbon (C), The silicon (Si) of about 0.9wt% to 1.6wt% amount, more than 0wt% and about 0.03wt% or more A small amount of phosphorus (P), more than 0wt% and about 0.01wt% or lesser amount of sulfur (S), about 0.01wt% to 0.1wt% amount copper (Cu), about 0.01wt% to 0.06wt% measure aluminum (Al), More than 0wt% and about 0.006wt% or lesser amount of nitrogen (N), more than 0wt% and be about 0.001wt% or lesser amount of oxygen (O)；Constitute (Fe) of steel alloy compositions surplus, institute Some wt% are all based on the gross weight of steel alloy compositions.It is selected from additionally, steel alloy also can comprise About 0.5wt% to 1.00wt% amount manganese (Mn), about 0.1wt% to 0.6wt% measure nickel (Ni), About 1.4wt% to 1.55wt% amount chromium (Cr), about 0.2wt% to 0.5wt% measure molybdenum (Mo), More than one or more in 0wt% and about 0.4wt% or lesser amount of vanadium (V).
As the term is employed herein " spheroidising " or " spheroidising " refer to heat treatment Process, it is especially useful in based on iron class alloy steel or its composition.Specifically, spheroidising can refer to by In the carbide of ferrum class steel grade or carbide composite, shape or the crystal form of carbon change over, example Such as spherical form, class is spherical or elliptical shape is to provide the physical property of satisfaction, such as machinery The heat treatment process of intensity, heat-resisting quantity, ductility, machinability etc..In spheroidising During, temperature rises to up to iron class alloy steel.
For first spheroidising heat treatment can about 720 DEG C to 850 DEG C temperature perform about 4 By 8 hours.
For secondary spheroidising secondary heat treatment can about 720 DEG C to 850 DEG C temperature perform About 4 to 8 hours.
Quenching can about 840 DEG C to 860 DEG C temperature perform 0.5 to 2 hours.
Tempering can about 150 DEG C to 190 DEG C temperature perform 0.5 to 2 hours.
Include selected from M it is preferred that the bearing steel manufactured can comprise3C、M7C3, and M23C6 The carbide composite of one or more in carbide and MC carbide.
As used herein, term " carbide composite " refers to comprise at least carbon and other yuan The compound of element, other elements described have more weak elecrtonegativity so that being positive electricity when carbon is combined Property or part electropositive.Carbide composite can at least carbon and metal be properly formed, and gold Genus can be alkali metal, alkaline-earth metal or transition metal, late transition metal, lanthanide series or Actinides, and do not limit.Specifically, M3C、M7C3, and M23C6In carbide M can be one or more in chromium (Cr), ferrum (Fe) and manganese (Mn) and M in MC carbide can be one or more in vanadium (V) and molybdenum (Mo).
Comprise the ferrum (Fe) as main component, carbon (C), silicon (Si), manganese (Mn), Phosphorus (P), sulfur (S), copper (Cu), nickel (Ni), chromium (Cr), molybdenum (Mo), aluminum (Al), the bearing of the steel compositions of nitrogen (N), oxygen (O) and vanadium (V) or bearing steel Double carbide such as Me can be comprised3C、Me7C3、Me23C6(Me:Cr, Fe, Mn), I.e. alloy composition and control process conditions by regulation bearing steel can be formed compound subtly Carbide.So, hardness, intensity and the toughness of the physical property of bearing steel such as bearing can quilt Significantly improve, and therefore improve durability, fatigue strength and fatigue life.And, can Obtaining highly enriched bearing steel, therefore reduced by its thickness, weight can reduce about 20% etc., And also ensure that the degree of freedom of Car design and reduce cost.
Car two parts that the bearing steel being made up of such as above-mentioned alloy that the present invention also provides for manufactures. Such as, transmission for a vehicle and electromotor can comprise steel described above or alloy by use The bearing mnanufacture of steel, in order to possibly improve the durability of vehicle and reduce vehicle weight, thus changing Enter fuel efficiency and prevent the pollution of the environment.
Other aspects of the present invention are disclosed following.
Accompanying drawing explanation
Fig. 1 illustrates the stream manufacturing bearing steel exemplary method according to an illustrative embodiment of the invention Cheng Tu.
Detailed description of the invention
Hereinafter, the preferred illustrative embodiment of the present invention will be described in detail.Before this, exist The term or the word that use in specification and claims should not be construed as limited to typical case or word Allusion quotation implication, and should be construed to that there is implication and the concept meeting the technology of the present invention spirit, based on Inventor can suitably define the concept of term to describe his/her invention in the best way Principle.Therefore, the embodiment that this specification describes is only the most preferably enforcement of the present invention Mode and do not represent all technical spirits of the present invention.It will therefore be appreciated that carrying in the application The friendship time has various equivalences and the amendment replacing embodiment.
Should be appreciated that where used in this disclosure, term " includes " and/or " comprising " regulation The existence of described feature, integer, step, operation, element and/or composition, but be not excluded for One or more other features, certificate, step, operation, element, composition and/or a combination thereof Exist or add.As used herein, term "and/or" includes the one in Listed Items or many Any and all combination planted.
Unless specifically stated otherwise or from context it is clear that as the term is employed herein " about " understand For in normal tolerance range, such as in 2 standard deviations of meansigma methods." about " it is appreciated that For 10%, 9%, 8%, 7%, 6%, 5%, 4%, 3%, 2%, 1%, 0.5%, 0.1%, Setting within 0.05% or 0.01%.Unless context clearly dictates otherwise, otherwise this In provide all numerical value all by " about " modify.
Be appreciated that term used herein above " vehicle " or " vehicle " or other be similar to Term generally includes motor vehicles, and such as passenger vehicle includes SUV (SUV), public affairs Altogether automobile, truck, various commercial car, boats and ships include various ship and canoe, aircraft, etc., And include hybrid electric vehicle, electric motor car, plug-in hybrid electric vehicle, hydrogen energy source car and other replace Replacing fuel car (such as, from the fuel that non-oil resource is derivative).As set forth herein, mixed Closing power car is the vehicle with two or more power resources, such as gasoline-powered and electricity Motor-car.
Hereinafter, the invention will now be more particularly described.The present invention relates to that there is the axle improving fatigue durability Hold steel and manufacture method thereof, and on the one hand, the present invention relates to have and improve fatigue durability Bearing steel.
Steel compositions for bearing can have improvement fatigability.Steel compositions can comprise: more than 0 Wt% and about 0.03wt% or lesser amount of phosphorus (P), more than 0wt% and about 0.01wt% Or lesser amount of sulfur (S), the copper (Cu) of about 0.01wt% to 0.1wt% amount, about 0.01wt% To the aluminum (Al) of 0.06wt% amount, more than 0wt% and about 0.006wt% or lesser amount of nitrogen (N), more than 0wt% and about 0.001wt% or lesser amount of oxygen (O), and steel group is constituted (Fe) of compound surplus, all of weight % (wt%) is all based on the gross weight of steel compositions.
Specifically, according to the needs of the present invention, the steel compositions for bearing can suitably comprise About 0.8wt% to 1.0wt% amount carbon (C), about 0.9wt% to 1.6wt% measure silicon (Si), About 0.5wt% to 1.00wt% amount manganese (Mn), about 0.1wt% to 0.6wt% measure nickel (Ni), About 1.4wt% to 1.55wt% amount chromium (Cr), about 0.2wt% to 0.5wt% measure molybdenum (Mo), And more than one or more in 0wt% and about 0.4wt% or lesser amount of vanadium (V).
Hereinafter, each of steel compositions composition and content thereof will be described in detail
(1) carbon (C)
Carbon (C) can be the important intensity to ensure bearing steel as used herein, and makes residual Remaining austenite consolidates.
Preferably, the content of carbon (C) gross weight based on steel alloy compositions can be about 0.8wt% Amount to 1.0wt%.When the content of carbon (C) is less than about 0.8wt%, it is not possible to sufficiently obtain Must be as the intensity of the steel that bearing steel uses and the reduction that fatigue strength etc. can be caused.On the other hand, When the content of carbon (C) is greater than about 1.0wt%, undissolved big carbide is stayed in steel, Therefore the processing characteristics between fatigue strength, viability etc. can be reduced and quench etc. can quilt Reduce.
(2) silicon (Si)
Silicon (Si) can be used as reducing agent, and the formation of suppression steel alloy pin-and-hole as used herein, Thus increase the strong of steel alloy by the solution strengthening effect as the solid being dissolved in substrate Degree, and increase the activity of carbon (C) etc..
Preferably, the content of silicon (Si) gross weight based on steel alloy compositions can be about 0.9wt% Amount to 1.6wt%.When the content of silicon (Si) is less than about 0.9wt%, the oxygen of dioxygen oxidation Compound (oxide by oxygen) may not be removed fully and stay in steel alloy, therefore closes The intensity of Jin Gang can be lowered and cannot obtain solution strengthening effect.When the content of silicon (Si) is big When about 2.0wt%, due to in-house permeable reactive, such as by excess silicon (Si) and carbon (C) site competition reaction, can occur decarbonization, and owing to the hardness before quenching increases, Processing characteristics can be reduced rapidly.
(3) manganese (Mn)
Manganese (Mn) can improve the quenching property of steel alloy and can improve steel alloy as used herein Deng intensity.
Preferably, the content of manganese (Mn) can be about the amount of 0.5wt% to 1.0wt%.Work as manganese (Mn), when content is less than about 0.5wt%, the improved effect of steel alloy quenching property is lowered. On the other hand, when the content of manganese (Mn) is greater than about 1.0wt%, the processing characteristics before quenching The MnS that can be lowered and reduce center segregation and fatigue life can be precipitated.
(4) nickel (Ni)
Nickel (Ni) can make the crystal grain micronization of steel alloy and at austenite and ferrum as used herein Ferritic can be solid solution to strengthen substrate.Additionally, nickel can improve low-temperature impact toughness with hard Change ability, and reduce the temperature of A1 transfer point to expand austenite.And then, nickel can increase carbon Activity.
Preferably, the content of nickel (Ni) can be about the amount of 0.1wt% to 0.6wt%.Work as nickel (Ni) when content is less than about 0.1wt%, may be not enough to obtain crystal grain micronization effect with And the improved effect of such as solution strengthening and substrate strengthening.On the other hand, containing as nickel (Ni) During amount greater than about 0.6wt%, red brittleness etc. can be caused in steel alloy.
(5) chromium (Cr)
Chromium (Cr) can improve the quenching property of steel alloy as used herein, it is provided that hardening, And simultaneously, make the tissue micronization of steel alloy and by this tissue of heat treatment spheroidising.Enter one Step, the thin layer in the hardenable cementite of chromium.
Preferably, the content of chromium (Cr) can be about the amount of 1.5wt% to 3.0wt%.Work as chromium (Cr), when content is less than about 1.5wt%, quenching property and hardening can be limited and can not be obtained The enough micronizations that must organize and spheroidising.On the other hand, it is more than when the content of chromium (Cr) About during 3.0wt%, what the increase effect of content may be not enough, therefore manufacturing cost can be increased.
(6) molybdenum (Mo)
Molybdenum (Mo) increases the quenching property of steel alloy thus in tempering and offer as used herein The hardening of steel alloy, toughness etc. are improved after anti-fragility.Further, molybdenum can reduce the work of carbon Property.
Preferably, the content of molybdenum (Mo) can be about the amount of 0.2wt% to 0.5wt%.Work as molybdenum (Mo) when content is less than about 0.2wt%, may be not sufficient to ensure that steel alloy hardening and Toughness etc..On the other hand, when the content of molybdenum (Mo) is greater than about 0.5wt%, steel alloy Processability (machinability) and productivity ratio etc. can be lowered and the increase effect of content may not Foot therefore manufacturing cost increases.
(7) vanadium (V)
As used herein vanadium (V) can form precipitate such as carbide, strengthening matrix organization and Therefore intensity and wearability are improved by precipitation strengthening effect.Additionally, vanadium can reduce the activity of carbon, And and then, under same cooling rate, the intensity of steel alloy can be increased by adding vanadium.
Preferably, the content of vanadium (V) may be greater than 0wt% and about 0.4wt% or less Amount.When the content of vanadium (V) is greater than about 0.4wt%, the toughness of steel alloy and hardness etc. can quilts Reduce.
(8) aluminum (Al)
Aluminum (Al) can be used as reducing agent and in order to improve steel alloy cleaning as used herein Therefore spend and can be reacted to form nitride with the nitrogen (N) in steel alloy makes crystal grain micronized Element.
Preferably, the content of aluminum (Al) can be about the amount of 0.01wt% to 0.06wt%.Work as aluminum (Al), when content is less than about 0.01wt%, possibly the reducing agent with crystal grain, cleaning cannot be obtained Spend the enough effect relevant with micronization.On the other hand, it is greater than about when the content of aluminum (Al) During 0.06wt%, coarse oxide inclusion etc. can be formed to reduce the fatigue life etc. of steel.
(9) nitrogen (N)
Nitrogen (N) can make austenite consolidate as used herein, makes crystal grain micronization and improves alloy The tensile strength of steel, yield strength and percentage elongation etc..But, when comprising the nitrogen of excess, can Form impurity or AlN (aluminium nitride) to reduce viability.
Preferably, the content of nitrogen (N) may be greater than 0wt% and about 0.006wt% or less Amount.When the content of nitrogen (N) is more than 0.006wt%, can cause fragility and the viability etc. can It is reduced.
(10) oxygen (O)
Oxygen (O) can increase the generation of steel alloy impurity to be dropped by contact fatigue as used herein Low cleaning degree and make steel alloy deteriorate.
Preferably, the content of oxygen (O) can be about the amount of 0.001wt% or less.As oxygen (O) Content more than 0.001wt% time, owing to contact fatigue can increase the impurity of steel alloy to deteriorate conjunction Jin Gang.
(11) phosphorus (P)
Phosphorus (P) can include that crystal particle crystal boundary segregation is to reduce the toughness of steel alloy as used herein.
Preferably, the content of phosphorus (P) may be greater than 0wt% and about 0.03wt% or less Amount.When the content of phosphorus (P) is greater than about 0.03wt%, it is possible to decrease the toughness of steel alloy.
(12) sulfur (S)
As used herein sulfur (S) can increase the machinability of steel alloy to promote to process, and by The toughness of steel alloy also can be reduced and by reacting formation MnS with manganese (Mn) in cyrystal boundary segregation And reduce the fatigue life of steel alloy.
Preferably, the content of sulfur (S) may be greater than 0wt% and about 0.01wt% or less Amount.When the content of sulfur (S) is greater than about 0.01wt%, it is possible to decrease the toughness of steel alloy thus Reduce the fatigue life of steel.
(13) copper (Cu)
Copper (Cu) can improve the hardening etc. of steel alloy as used herein.
Preferably, the content of copper (Cu) can be about the amount of 0.01wt% to 0.1wt%.Work as copper (Cu) when content is less than about 0.01wt%, not available enough hardening improved effects.With Time, when the content of copper (Cu) is greater than about 0.1wt%, owing to limiting beyond solid solution, steel strong Degree improved effect saturable, and therefore manufacturing cost can increase and cause red brittleness.
Owing to can there is excellent hardness, strong for the steel compositions of the bearing that comprises mentioned component Degree, fatigue strength and fatigue life.Therefore, during steel compositions may be used on vehicle part etc.. Such as, the steel compositions for bearing is applied to the automatic or manual variator etc. of vehicle, and In transmission components, bearing steel may be used on carrier frame, ring gear, gear, axle, with In step device hub etc..
Hereinafter, in yet another aspect, the present invention relates to manufacture and there is the axle improving fatigue durability The method holding steel.
Those skilled in the art can suitably manufacture according to the present invention with reference to disclosed known technology Have improve fatigue durability bearing steel.
The method with the bearing steel improving fatigue durability constructed in accordance comprises the steps that
Such as, as it is shown in figure 1, the method comprises the steps that the alloy being mixed for bearing (S10) Composition of steel；By steel alloy (S20) at the temperature heat treatment about 4 to 8 of about 720 DEG C to 850 DEG C Hour for first nodularization；By steel alloy (S30) wire drawing of heat treatment；By by the conjunction of wire drawing Jin Gang (S40) about 720 DEG C to 850 DEG C temperature secondary heat treatment about 4 to 8 hours with In secondary nodularization；The steel alloy (S50) of secondary heat treatment is forged；At about 840 DEG C to 860 DEG C Temperature the steel alloy (S60) being forged of about 0.5 to 2 hours is quenched；At about 150 DEG C To the temperature of 190 DEG C, the steel alloy (S70) of quenching is tempered about 0.5 to 2 hours.
In the method manufacturing steel alloy, double carbide can be formed and by spheroidising in steel. Specifically, double carbide can include selected from M3C、M7C3, and M23C6Carbide and being One or more in sedimentary MC carbide.M can be metal or transition metal and not have Restricted.
Preferably, M3C and M7C3Carbide, and M23C6M in carbide can be choosing One or more in chromium (Cr), ferrum (Fe), manganese (Mn), and in MC carbide M can be selected from one or more from vanadium (V) and molybdenum (Mo).When above-mentioned compound When carbide is formed, the intensity of bearing steel and hardness etc. can be modified, and durability etc. can quilt Extend.
The method can include using the steel alloy for bearing to manufacture wire rod, as mentioned above.Such as, Can by will selected from carbon (C), silicon (Si), manganese (Mn), nickel (Ni), chromium (Cr), One or more compositions in molybdenum (Mo) or vanadium (V) add and are mixed into as main component Ferrum (Fe), phosphorus (P), sulfur (S), copper (Cu), aluminum (Al), nitrogen (N), The wire rod of above-mentioned alloying component is comprised with manufacture in oxygen (O).Therefore the wire rod manufactured can be further It is heat-treated for first nodularization, such as little the temperature about 4 to 8 of about 720 DEG C to 850 DEG C Time (S20)；Wire drawing (S30)；Secondary heat treatment is used for secondary nodularization, such as, at about 720 DEG C To the temperature about 4 to 8 hours (S40) of 850 DEG C；Forging (S50)；Quenching, such as about The temperature of 840 DEG C to 860 DEG C about 0.5 to 2 hours (S60)；And tempering, such as at about 150 DEG C To the temperature about 0.5 to 2 hours (S70) of 190 DEG C.
The quenching of manufacture method can perform about 0.5 to 2 hours the temperature of about 840 DEG C to 860 DEG C, And tempering can perform about 0.5 to 2 hours the temperature of about 150 DEG C to 190 DEG C.
When hardening heat be less than about 840 DEG C or the cool time be less than about 0.5 little constantly, unevenly Form the tissue of cooling rapidly thus cause material deviation.On the other hand, it is more than when hardening heat About 860 DEG C or cool time be greater than about 2 little constantly, by first and secondary spheroidising heat treatment shape The double carbide of the spheroidising become can be dissolved.
When temperature be less than about 150 DEG C or tempering time be less than about 0.5 little constantly, may not protect The physical property such as toughness of card bearing steel.On the other hand, when temperature be greater than about 190 DEG C or Tempering time is greater than about 2, and little the hardness of bearing steel etc. can be reduced rapidly constantly, is therefore difficult to Improve viability.
Meanwhile, each temperature in the first of manufacture method and secondary ball heat-transformation process is both less than The time of about 720 DEG C or nodularization heat treatment be less than about 4 little constantly, it may be necessary to double carbide A large amount of nodularization times, and therefore manufacturing cost can increase sharply.On the other hand, when first with two When temperature in secondary nodularization heat treatment is greater than about 850 DEG C, owing to the double carbide formed is molten Solve, cooling procedure is formed thin layer composite carbide and replaces the probability of spherical double carbide Can significantly increase.And then, when first and secondary ball heat treatment time be greater than about 8 little constantly, The Oxygen potential of double carbide can be slowed thus the manufacturing cost that increases sharply.
Below embodiment, the present invention will be more fully described by embodiment.
These embodiments are merely to illustrate the present invention, it is clear that to those skilled in the art, The scope of the present invention will be not interpreted as being limited to these examples.
According to an illustrative embodiment of the invention, in order to compare, there is improvement fatigue durability axle Hold the physical property of steel, comparative example and to have the embodiment of composition described in following list 1 produced.
First and the heat treatment temperature of secondary nodularization, hardening heat and time and the temperature applied
It is shown in table 2 below with the condition of time.
[table 1]
Table 1 illustrates the constituent of the comparative example 1 to 10 of the bearing steel according to prior art and contains Amount, and arrive constituent and the content of embodiment 3 according to the embodiment 1 that goes out of the present invention.
[table 2]
Table 2 illustrates, in comparative example 1 to 10 and the enforcement of the constituent and content with table 1 In the manufacturing condition of example 1 to 3, in first and the temperature of heat treatment of secondary nodularization, quenching temperature Degree and time, temperature and time.Herein, all of comparative example 1 to 10 and example 1 to 3 meet according to the present invention in the temperature for the first time and in the heat treatment of secondary nodularization, hardening heat With time and temperature and time.
[table 3]
Table 3 illustrates, room temperature hardness, the hardness of 300 DEG C, when surface pressing is 6.2GPa 150 DEG C of rotation numbers for the rotary bending tester in L10 life-span and viability, examine Consider to the condition according to table 2 to prepare and there is the constituent of table 1 and the comparative example 1 to 10 of content After example 1 to 3,1 when surface pressing is 6.2GPa, by using micro Vickers hard Degree meter according to KS B 0081 measuring method, measures the hardness of room temperature, 300 DEG C hard at 300gf Degree and the hardness of 150 DEG C.For the rotation number of rotary bending tester, in maximum deflection power Square is about 20kgfm, rotation number is about 200RPM to 3000RPM, maximum load about 100kg Or under conditions of less and three phase electric power is 220V and 7KW, by using diameter about 4mm Normal line footpath by rotary bending tester, according to KS B ISO 1143 measuring method, Measure the L10 life-span.The L10 life-span is the viability of sample, and means until about 10% Sample rotation number of rotary bending tester when being destroyed.
Therefore, the hardness of room temperature (about 25 DEG C) is looked back, it is possible to confirm, from the enforcement of table 3 Example 1 to 3, compared with comparative example 1 to 10, the hardness of room temperature improves 8.9% to 17.5%. Additionally, look back the hardness of 300 DEG C, it is possible to confirm the embodiment 1 to 3 from table 3, and compare Example 1 to 10 is compared, and the hardness of room temperature improves 14.4% to 19.4%.
It is able to verify that, when surface pressing is 6.2GPa, to the L10 life-span at 150 DEG C The rotation number of rotary bending tester, the average of embodiment 1 to 3 be 18,469,333 and About twice for the average 9055000 of comparative example 1 to 10 is high.That is, it is able to verify that from table 3, The bearing steel of the present invention improves 192.3% to 221.1% compared with prior art.
Rotation number based on rotary bending tester, in order to compare comparative example 1 to 10 and reality Execute the viability of example 1 to 3, the rotation number of the rotary bending tester of comparative example 1 It is 8400000, is set as the basis of 100% viability.Comparative example 1 based on The rotation number of rotary bending tester compare, it is shown that comparative example 2 to 10 and embodiment 1 The rotation number of the rotary bending tester to 3 is increased or decreased the difference of degree and is expressed as hundred Mark.That is, for comparing the hundred of the viability of comparative example 1 to 10 and embodiment 1 to 3 Mark, is to represent to remain comparative example 2 to 10 and embodiment 1 to 3 on the basis of comparative example 1 The rotation number of rotary bending tester relatively increase and reduce the value of degree.
Herein, by comparative example and the comparison of the viability of embodiment, permissible from table 3 Find out, identical with the rotation number of rotary bending tester, the durability of embodiment 1 to 3 Life-span is that the about twice of the viability of comparative example 1 to 10 is many.
As it has been described above, hardness and viability in order to check why embodiment compare comparative example Hardness and the more preferable reason of viability, be included in comparative example 1 and embodiment 1 to 3 The type of double carbide and vol% be shown in table 4 below.
[table 4]
Table 4 illustrates the content of the double carbide being included in comparative example 1 and embodiment 1 to 3. As shown in table 4, the double carbide of comparative example 1 mainly includes M3C and a small amount of MoC, but Embodiment 1 relatively consistently includes VC and NbC and M to embodiment 33C and MoC. The difference of double carbide composition can be considered as why embodiment has more more preferable than comparative example In the reason of hardness and viability one.
Therefore, it is possible to experimentally confirm, the satisfied composition according to the present invention and content range are also Various compound carbonizing is included by the embodiment 1 to 3 prepared according to the heat treatment process of the present invention Things etc., therefore have intensity more more preferable than comparative example 1 to 10 and viability.
As it has been described above, describe the present invention relevantly with only certain exemplary embodiments of this invention, But embodiment is only explanation and the present invention is not limited to this.Described embodiment can pass through Field that the present invention belongs to technical staff makes and being altered or modified, and is made without departing from the scope of the present invention, and The present invention technical spirit and following by the equivalent scope of the claim being described in various replace It is all possible for changing and revising.

Claims (20)

1., for a steel compositions for bearing, it comprises:
The carbon (C) of about 0.8wt% to 1.0wt%；
The silicon (Si) of about 0.9wt% to 1.6wt%；
Phosphorus (P) more than 0wt% and about 0.03wt% or less；
Sulfur (S) more than 0wt% and about 0.01wt% or less；
The copper (Cu) of about 0.01wt% to 0.1wt%；
The aluminum (Al) of about 0.01wt% to 0.06wt%；
Nitrogen (N) more than 0wt% and about 0.006wt% or less；
Oxygen (O) more than 0wt% and about 0.001wt% or less；With
Constitute the ferrum (Fe) of described steel compositions surplus,
All of wt% is all based on the gross weight of described steel compositions.
2. steel compositions as claimed in claim 1, it also comprises: based on described steel compositions The manganese (Mn) of gross weight, about 0.5wt% to 1.00wt%.
3. steel compositions as claimed in claim 1, it also comprises: based on described steel compositions The nickel (Ni) of gross weight, about 0.1wt% to 0.6wt%.
4. steel compositions as claimed in claim 1, it also comprises: based on described steel compositions The chromium (Cr) of gross weight, about 1.4wt% to 1.55wt%.
5. steel compositions as claimed in claim 1, it also comprises: based on described steel compositions The molybdenum (Mo) of gross weight, about 0.2wt% to 0.5wt%.
6. steel compositions as claimed in claim 1, it also comprises: based on described steel compositions Gross weight, the vanadium (V) more than 0wt% and about 0.4wt% or less.
7. steel compositions as claimed in claim 1, it also comprises: be selected from about 0.5wt% to 1.00 The manganese (Mn) of wt%, the nickel (Ni) of about 0.1wt% to 0.6wt%, about 1.4wt% to 1.55wt% Chromium (Cr), the molybdenum (Mo) of about 0.2wt% to 0.5wt% and more than 0wt% and about 0.4wt% Or one or more in less vanadium (V), all of wt% is all based on the total of described steel compositions Weight.
8. steel compositions as claimed in claim 1, it substantially consists of the following composition:
The carbon (C) of about 0.08wt% to 1.0wt%；
The silicon (Si) of about 0.9wt% to 1.6wt%；
Phosphorus (P) more than 0wt% and about 0.03wt% or less；
Sulfur (S) more than 0wt% and about 0.01wt% or less；
The copper (Cu) of about 0.01wt% to 0.1wt%；
The aluminum (Al) of about 0.01wt% to 0.06wt%；
Nitrogen (N) more than 0wt% and about 0.006wt% or less；
Oxygen (O) more than 0wt% and about 0.001wt% or less；And
Constitute the ferrum (Fe) of described steel compositions surplus,
All of wt% is all based on the gross weight of described steel compositions.
9. steel compositions as claimed in claim 1, it substantially consists of the following composition:
The carbon (C) of about 0.08wt% to 1.0wt%；
The silicon (Si) of about 0.9wt% to 1.6wt%；
Phosphorus (P) more than 0wt% and about 0.03wt% or less；
Sulfur (S) more than 0wt% and about 0.01wt% or less；
The copper (Cu) of about 0.01wt% to 0.1wt%；
The aluminum (Al) of about 0.01wt% to 0.06wt%；
Nitrogen (N) more than 0wt% and about 0.006wt% or less；
Oxygen (O) more than 0wt% and about 0.001wt% or less；
Selected from the manganese (Mn) of about 0.5wt% to 1.00wt%, the nickel (Ni) of about 0.1wt% to 0.6wt%, The chromium (Cr) of about 1.4wt% to 1.55wt%, the molybdenum (Mo) of about 0.2wt% to 0.5wt% and One or more in vanadium (V) more than 0wt% and about 0.4wt% or less；And
Constitute the ferrum (Fe) of described steel compositions surplus,
All of wt% is all based on the gross weight of described steel compositions.
10. the method manufacturing bearing steel, described method includes:
Manufacture the wire rod comprising steel alloy compositions；
By described wire rod heat treatment for first nodularization；
By the wire rod wire drawing of described heat treatment；
By described by the wire rod secondary heat treatment of wire drawing for secondary nodularization；
The wire rod of described secondary heat treatment is forged；
Quench and the described wire rod being forged is quenched；And
The described wire rod being quenched is tempered,
Wherein said steel alloy compositions comprises: the carbon (C) of about 0.08wt% to 1.0wt%；About The silicon (Si) of 0.9wt% to 1.6wt%；Phosphorus (P) more than 0wt% and about 0.03wt% or less； Sulfur (S) more than 0wt% and about 0.01wt% or less；About 0.01wt% to 0.1wt%'s Copper (Cu)；The aluminum (Al) of about 0.01wt% to 0.06wt%；More than 0wt% and about 0.006 The nitrogen (N) of wt% or less；Oxygen (O) more than 0wt% and about 0.001wt% or less； With the ferrum (Fe) of the described steel compositions surplus of composition, all of wt% is all based on described steel alloy group The gross weight of compound.
11. methods as claimed in claim 10, wherein said steel alloy compositions also comprises selected from about The manganese (Mn) of 0.5wt% to 1.00wt%, the nickel (Ni) of about 0.1wt% to 0.6wt%, about 1.4wt% To the chromium (Cr) of 1.55wt%, the molybdenum (Mo) of about 0.2wt% to 0.5wt% and more than 0wt% And one or more in the vanadium (V) of about 0.4wt% or less, all of wt% is all based on institute State the gross weight of steel alloy compositions.
12. methods as claimed in claim 10, the wherein said heat treatment for first nodularization is about The temperature of 720 DEG C to 850 DEG C performs about 4 to 8 hours.
13. methods as claimed in claim 10, the wherein said secondary heat treatment for secondary nodularization Perform about 4 to 8 hours the temperature of about 720 DEG C to 850 DEG C.
14. methods as claimed in claim 10, wherein said quenching is the temperature of about 840 DEG C to 860 DEG C Degree performs about 0.5 to 2 hours.
15. methods as claimed in claim 10, wherein said tempering is the temperature of about 150 DEG C to 190 DEG C Degree performs about 0.5 to 2 hours.
16. methods as claimed in claim 10, wherein said bearing steel comprises double carbide.
17. methods as claimed in claim 16, wherein said double carbide comprises selected from M3C、 M7C3, and M23C6One or more in carbide and MC carbide, wherein M is metal Or transition metal.
18. methods as claimed in claim 16, wherein said M3C、M7C3, and M23C6Carbonization M in thing is one or more in chromium (Cr), ferrum (Fe) and manganese (Mn) and institute Stating the M in MC carbide is one or more in vanadium (V) and molybdenum (Mo).
19. 1 kinds of vehicle parts, it comprises steel compositions as claimed in claim 1.
20. vehicle parts as claimed in claim 19, wherein said vehicle part is electromotor or speed change The bearing of device.
CN201510760961.7A 2015-06-22 2015-11-10 Bearing steel with improved fatigue durability and method of making the same Active CN106256917B (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR10-2015-0088341 2015-06-22
KR1020150088341A KR101685490B1 (en) 2015-06-22 2015-06-22 Bearing alloy steel improved fatigue durability and the method of manufacturing the same

Publications (2)

Publication Number Publication Date
CN106256917A true CN106256917A (en) 2016-12-28
CN106256917B CN106256917B (en) 2021-04-27

Family

ID=57466871

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201510760961.7A Active CN106256917B (en) 2015-06-22 2015-11-10 Bearing steel with improved fatigue durability and method of making the same

Country Status (4)

Country Link
US (1) US20160369370A1 (en)
KR (1) KR101685490B1 (en)
CN (1) CN106256917B (en)
DE (1) DE102015220728A1 (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109868420A (en) * 2017-12-04 2019-06-11 现代自动车株式会社 Ferritic steel
CN110846586A (en) * 2019-12-16 2020-02-28 北京机科国创轻量化科学研究院有限公司 Steel for high-strength high-toughness high-wear-resistance steel ball and preparation method thereof
CN112030079A (en) * 2019-06-03 2020-12-04 现代自动车株式会社 Method for manufacturing high carbon bearing steel and high carbon bearing steel manufactured by the same

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20160145702A1 (en) * 2014-11-24 2016-05-26 Hyundai Motor Company Bearing steel having improved fatigue durability and method of manufacturing the same
JP6467441B2 (en) * 2017-01-17 2019-02-13 トクセン工業株式会社 Needle wire
CN111378814B (en) * 2018-12-29 2021-12-24 东莞科力线材技术有限公司 Preparation method of axis wire of copier
CN111304545A (en) * 2019-12-09 2020-06-19 无锡市法兰锻造有限公司 Low-temperature steel forging produced by using continuous casting billet and manufacturing method thereof

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6165289A (en) * 1996-02-08 2000-12-26 Nsk Ltd. Water-resistant long-life rolling bearing
JP2001294972A (en) * 2000-04-18 2001-10-26 Sumitomo Metal Ind Ltd Steel for bearing
JP2002105600A (en) * 2000-09-26 2002-04-10 Sanyo Special Steel Co Ltd High hardness corrosion resistant steel having excellent workability
KR20110027350A (en) * 2009-09-10 2011-03-16 주식회사 포스코 Steel having high ductility and method for manufacturing the same
CN103527612A (en) * 2012-07-04 2014-01-22 现代自动车株式会社 Long life and a manufacturing method of the pinion shaft

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3614113B2 (en) * 2001-03-16 2005-01-26 住友金属工業株式会社 Steel material for bearing element parts with excellent machinability
KR20150088341A (en) 2011-12-29 2015-08-03 삼성전기주식회사 Spindle Motor
DE102015220299A1 (en) * 2014-11-21 2016-05-25 Hyundai Motor Company Bearing steel with improved durability and method for producing desselbigen
US20160145702A1 (en) * 2014-11-24 2016-05-26 Hyundai Motor Company Bearing steel having improved fatigue durability and method of manufacturing the same

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6165289A (en) * 1996-02-08 2000-12-26 Nsk Ltd. Water-resistant long-life rolling bearing
JP2001294972A (en) * 2000-04-18 2001-10-26 Sumitomo Metal Ind Ltd Steel for bearing
JP2002105600A (en) * 2000-09-26 2002-04-10 Sanyo Special Steel Co Ltd High hardness corrosion resistant steel having excellent workability
KR20110027350A (en) * 2009-09-10 2011-03-16 주식회사 포스코 Steel having high ductility and method for manufacturing the same
CN103527612A (en) * 2012-07-04 2014-01-22 现代自动车株式会社 Long life and a manufacturing method of the pinion shaft

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109868420A (en) * 2017-12-04 2019-06-11 现代自动车株式会社 Ferritic steel
CN109868420B (en) * 2017-12-04 2022-07-12 现代自动车株式会社 Ferritic steel
CN112030079A (en) * 2019-06-03 2020-12-04 现代自动车株式会社 Method for manufacturing high carbon bearing steel and high carbon bearing steel manufactured by the same
US11578383B2 (en) 2019-06-03 2023-02-14 Hyundai Motor Company Method for manufacturing high-carbon bearing steel and high-carbon bearing steel manufactured therefrom
CN110846586A (en) * 2019-12-16 2020-02-28 北京机科国创轻量化科学研究院有限公司 Steel for high-strength high-toughness high-wear-resistance steel ball and preparation method thereof

Also Published As

Publication number Publication date
KR101685490B1 (en) 2016-12-13
CN106256917B (en) 2021-04-27
US20160369370A1 (en) 2016-12-22
DE102015220728A1 (en) 2016-12-22

Similar Documents

Publication Publication Date Title
CN106256917A (en) There is bearing steel and the manufacture method thereof improving fatigue durability
KR102386638B1 (en) Steel for carburized bearing parts
CN106065455B (en) Carburized alloy steel with improved durability and method for manufacturing same
JP5202043B2 (en) Rolling parts and manufacturing method thereof
CN105624560B (en) A kind of bearing steel and its manufacturing method with improved fatigue durability
KR101685489B1 (en) The Alloy Steel Which Is Used as The High Tough Outer Wheel of Constant Velocity Joint And The Method of The Same
JP2001152252A (en) Roll bearing
CN106048456B (en) Carburized alloy steel with improved durability and method for manufacturing same
JP4923776B2 (en) Rolling and sliding parts and manufacturing method thereof
CN104520459B (en) Steel material for high frequency induction hardening
CN104846294B (en) The method of non-normalizing steel compositions and connecting rod and manufacture connecting rod using the composition
JP2016098436A (en) Bearing steel having enhanced fatigue durability and manufacturing method
CN105671445A (en) Carburized alloy steel having superior durability and method of manufacturing the same
CN107299294A (en) High-strength spring steel with excellent corrosion resistance
JP3593255B2 (en) Manufacturing method of high strength shaft
CN106350745A (en) Overheating-insensitive fine grained alloy steel for use in double high-frequency heat treatment and method of manufacturing the same
EP1277847A1 (en) Case hardening steel and carburized part using same
CN1611625A (en) Cr-Mo alloy steel for change gear
JP2014185379A (en) Hydrogen-brittle type carbonitrided bearing part excellent in surface fatigue strength
CN106987766A (en) Axletree steel alloy and the manufacture method using its vehicle axle
CN115679196B (en) Seamless steel tube for self-lubricating automobile driving shaft and manufacturing method thereof
CN106435388A (en) Carburized steel and method of manufacturing the same
CN113265592B (en) Outer ring of variable oil pump and manufacturing method thereof
CN107299276A (en) High-strength spring steel with excellent corrosion resistance
JP3607583B2 (en) Steel for power transmission parts and power transmission parts

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant