CN103088257A - High-strength steel for automobile transmission shaft axle tube - Google Patents
High-strength steel for automobile transmission shaft axle tube Download PDFInfo
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- CN103088257A CN103088257A CN2013100163593A CN201310016359A CN103088257A CN 103088257 A CN103088257 A CN 103088257A CN 2013100163593 A CN2013100163593 A CN 2013100163593A CN 201310016359 A CN201310016359 A CN 201310016359A CN 103088257 A CN103088257 A CN 103088257A
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Abstract
The invention relates to high-strength steel for an automobile transmission shaft axle tube. The high-strength steel consists of the following elements in percentage by weight: 0.03-0.1 percent of C, 0.05-0.2 percent of Si, 1-2.5 percent of Mn, 0-0.025 percent of P, 0-0.001 percent of S, 0-0.15 percent of Al, 0.01-0.1 percent of Nb, 0.01-0.15 percent of Ti and the balance of Fe. The high-strength steel has the positive effects that due to optimized design of the material components and adjustment and setting of the material manufacturing process parameters, the high-strength steel for the transmission shaft axle tube is manufactured by utilizing the principles of solution enhancing, fine-grain enhancing and precipitation enhancing. The material application target is on the automobile transmission shaft axle tube, the strength and the service life of the axle tube can be improved, and the weight of the transmission shaft assembly is reduced by reducing the thickness of the shaft tube, so that energy conservation and emission reduction are realized.
Description
Technical field
The present invention relates to a kind of high-strength steel that is particularly useful for making the truck drive shaft central siphon.
Background technology
The developing direction of Domestic Automotive Industry is environmental protection and energy saving at present, and along with the fast development of Domestic Automotive Industry, the superpower of commercial truck, high rotating speed and lightweight development trend have proposed higher performance requriements to truck drive shaft.
Domestic transmission shafts tube material is mainly the TG480QZ that No. 23.5 steel producing of B440QZR, B480QZR, Anshan iron and steel plant that Baosteel is produced and 15Ti, Tang Gang produce, B440QZR, B480QZR, TG480QZ, material chemical composition is C, Si, S, P, Mn, and tensile strength rank major part is below 480MPa.Domestic transmission shaft tube material will be tried to achieve under prerequisite satisfying loading strength, there is no the potentiality of attenuate welded tube wall thickness, can't reach light-weighted service requirements.
According to documents and materials, Foreign Automobile transmission shaft present situation is: the Japanese car transmission shaft is generally 500MPa with Welded Steel Pipe tensile strength.Motor corporation's vehicle working strengths such as the Mitsubishi of part, Isuzu Motors are the high strength driving shaft tube material of 735MPa, but consumption is not very large, a large amount of use be tensile strength at the material of 500-540MPa, be equivalent to the steel grade of domestic B480QZR and the Geng Gao trade mark.It is 700N/mm that Sumitomo Metal Industries has developed tensile strength
2The used for vehicle transmission shaft Welded Steel Pipe, recently again develop tensile strength be 800N/mm
2Product innovation, its carbon content is all in 0.20% left and right, manganese content is between 0.70-1.40%.The vehicle transmission central siphon of Germany and Sweden adopts 20 and the 20Mn2 material of similar China, and its tensile strength is 600--750MPa, and yield strength is at 500-650MPa.
Aspect the driveshaft applications material, finding Patents has: Japanese Patent, patent inventor: KAWABATAYOSHIKAZU; SAKATA TAKASHI; SAKAGUCHI MASAYUKI; The patent No.: JP2006037205; Article autograph: " Method For Producing Hollow Driveshaft Having Excellent Fatigueresistance "; Patent content: article be the chemical composition of steel pipe: 0.25 to 0.55%C, Si, Mn and Al, carry out modifier treatment after its moulding, surface compress residual stresses is greater than 216Mpa, and maximum can reach 440Mpa, adds as required Cr in chemical constitution, Mo, W, Ni, Cu, B or Ti, the elements such as Nb and V.
It is energy-conservation that present China advocates loss of weight energetically, and advancing automobile component loss of weight and light-weighted paces is long-term problems that automobile industry material technology personnel face.
Summary of the invention
The object of the present invention is to provide the more superior truck drive shaft central siphon high-strength steel of a kind of performance.To realize the technique effect of loss of weight.
Truck drive shaft central siphon high-strength steel of the present invention is made of by weight percentage following element: C0.03～0.1, Si0.05～0.2, Mn1～2.5, P0～0.025, S0～0.001, Al0～0.15, Nb0.01～0.1, Ti0.01～0.15, Fe surplus.
The mentality of designing of the high-strength vehicle axle tube steel that the present invention relates to is to utilize grain refining, precipitation strength to form the strengthening mechanism of steel in conjunction with original solution strengthening, the carbon content control is below 0.1%, reduce the addition of the elements such as harmful element sulphur, take niobium, titanium as main strengthening element, add up to addition to be controlled at below 0.45%.In the process of controlled rolling and cooling, niobium and titanium elements form carbon compound Ti (C, N), Nb (C, N) and separate out also disperse distribution, and Nb (C, N), Ti (C, N) compound have the effect of refinement ferrite crystal grain, thereby improve armor plate strength.
Through the standby steel plate of hot rolling, its mechanical property is truck drive shaft central siphon of the present invention: yield strength Rp0.2 〉=570MPa, tensile strength Rm 〉=700MPa, elongation A 〉=13% with high-strength steel; Realize improving truck driving-shaft assembly work-ing life and light-weighted purpose.
Alloying element Mn is one of main solution strengthening element of the present invention, and it is by making hot-rolled steel sheet grain refining and solution strengthening improve intensity.Mn content is low, and armor plate strength is not enough, the Mn too high levels, and Sheet Forming Ability descends, so the present invention controls its content between 1.0-2.5%.
Alloying element Ti and nitrogen, oxygen, carbon have extremely strong avidity, and the TiC bonding force is strong, stable, the difficult decomposition, only is heated to more than 1000 ℃ in steel and could dissolves in sosoloid lentamente.Before not dissolving in, the titanium carbide particulate has the effect that stops grain growth.The structural alloy steel of titaniferous has good mechanical property and processing performance, and main drawback is that hardening capacity is slightly poor.Therefore the Ti content requirement in the present invention is between 0.01-0.15%
Alloy element Nb is combined with C and is formed carbide, is near the ferrite crystal boundary and the inner important element that forms precipitate density different zones of crystal grain.When Nb content hanged down, the inner precipitate density of ferrite crystal grain was not enough, and when Nb content was high, grain boundaries precipitate density was also high, caused plasticity to descend.Therefore, the Nb content requirement in the present invention is between 0.01-0.1%.
The truck drive shaft central siphon high tensile steel plate of the present invention of making as follows:
Usually habitual various starting material are pressed the mentioned component proportioning, smelt in oxygen converter, after tapping, molten steel becomes the slab of thickness 250mm through furnace rear refining, continuous casting, slab reheats 1230 ℃ of insulations through walking beam furnace, open the bundle temperature and be controlled at 1230 ℃, finishing temperature is controlled at 850～900 ℃, and it is cooling that the band steel goes out to carry out after finishing train laminar flow, and the roll bending temperature is controlled at below 600 ℃.Carry out the multi-pass aximal deformation value rolling when the roughing of austenite recrystallization district, guarantee large draft, make austenite crystal fully broken, the end temp that guarantees simultaneously roughing is in the perfect recrystallization district, to avoid producing mixed grain structure.The district carries out continuous finish rolling in non-recrystallization temperature below 950 ℃, and increases the finish rolling draft, and austenite crystal is fully flattened, and at the inner slip band that forms of crystal grain, provides more nucleation site during for ferritic transformation.
Positively effect of the present invention is by the optimization design to material composition, and the adjustment of material fabrication process parameters and formulation utilize solution strengthening, refined crystalline strengthening, precipitation strength principle to realize the manufacturing of high strength driving shaft tube steel.The application target of material can improve intensity and the life-span of central siphon on the truck drive shaft central siphon, reduce the weight of driving-shaft assembly by the attenuate of central siphon thin and thick, realizes energy-saving and emission-reduction.
Description of drawings
Fig. 1 observes the microstructure picture of central siphon cross section under LEXT-OLS3000 type laser confocal microscope;
Wherein: be (a) to use at present the microstructure picture of 440QZ steel automobile transmission shaft tube;
(b) be the microstructure picture with material 1 vehicle transmission central siphon processed in the embodiment of the present invention;
(c) be the microstructure picture with material 2 vehicle transmission central siphon processed in the embodiment of the present invention;
Fig. 2 is the CCT graphic representation (wherein: a is material 2, and b is material 1) that the crystal grain physical size of passing through to obtain after actual measurement composition and cooling controlling and rolling controlling process of central siphon material of the present invention is calculated gained;
Fig. 3 is the TTT graphic representation (wherein: a is material 2, and b is material 1) that passes through to survey the crystal grain physical size gained that obtains after composition and cooling controlling and rolling controlling process of central siphon material of the present invention;
Fig. 4 is the actual measurement CCT graphic representation of central siphon material 2 of the present invention;
Fig. 5 is the actual measurement CCT graphic representation of central siphon material 1 of the present invention.
Embodiment
By following examples, the present invention is described in further detail.
Technical scheme of the present invention is achieved in that the design of central siphon material optimal components is to reduce as far as possible A
r3And carbon equivalent, composition and preparation technology according to design, two composition high-strength vehicle transmission shaft tube materials have been prepared by weight percentage, below name material 1 and material 2, chemical composition is as shown in table 1, surplus is iron, and the mentality of designing of composition is to adopt low C (below 0.15%), high Mn (approximately 1.5%) to add Nb-Ti combined microalloying technology.Simultaneously, Nb-Ti gets height (material 2) and low (material 1) two groups, and in order to reduce carbon equivalent, corresponding C, Mn gets low (material 1) and high (material 2) two groups.Its mechanical property is as shown in table 2, can see that in table 2 its intensity compares with original central siphon material, and yield strength and tensile strength have all improved a lot.
The photo of Fig. 1 adopts the microstructure of LEXT-OLS3000 type confocal laser scanning microscope central siphon cross section, wherein (a) is the microstructure of former central siphon, is mainly ferrite, also has a small amount of pearlitic structure at the ferrite grain boundaries, cleaner in crystal grain, can't see precipitate; (b) be the microstructure of material 1 of the present invention, be mainly ferrite and a small amount of bainite, grain boundaries has the perlite of minute quantity, and intracrystalline has a small amount of precipitate; (c) be the microstructure of material 2 of the present invention, be mainly the ferrite of white and the bainite of grey, the intracrystalline precipitate is more, is disperse and distributes, and the grain size of three kinds of central siphons is also inhomogeneous and be not equi-axed crystal, with directivity, is rolling result later.The mean diameter of utilizing division lines method to record a, b and three kinds of central siphon material grains of c is about 5.37 μ m, 4.57 μ m, 3.98 μ m, and namely the crystal grain of material 2 is minimum.Grain boundaries and 750MPa central siphon ferrite crystal grain at the 600MPa central siphon are inner, can observe tiny precipitated phase particle, and more in 750MPa central siphon tissue, and seeing grain refining and separate out precipitation should be the main mechanism of strengthening.
High strength central siphon material C CT, TTT curve determination:
By the crystal grain physical size that obtains after actual measurement composition and cooling controlling and rolling controlling process, utilize the JMatPro software for calculation, calculated respectively the CCT of material 2 and 1 two steel grades of material and TTT curve as shown in Fig. 2,3.
As can be seen from the figure both CCT, TTT curve are very approaching, and explanation can be adopted same cooling controlling and rolling controlling process.In addition, it can also be seen that from these curves, the product major part that obtains after controlled rolling and controlled cooling is ferrite, if after controlled rolling Slow cooling, can obtain a small amount of pearlitic structure; If cooling fast after controlled rolling, there is a small amount of bainite to form in the later stage that changes.The product of isothermal transformation is mainly also take ferritic structure as main; When if the temperature of isothermal transformation is low, just there are a small amount of perlite or bainite structure to occur.Simultaneously, also be not difficult to find out, the steel of this constituents almost cannot form martensite under existing manufacturing condition.
Fig. 4, Fig. 5 are the actual measurement CCT curve of these two kinds of samples, with the CCT curve comparison that calculates, although this two suites line detail section has small difference, and, the rule of cooling transformation process or consistent.Both under general hot rolling working condition, the Fine Texture of Material that obtains after the process laminar flow is cooling was mainly to be made of ferrite, and the content of bainite is few.
The CCT curve of two steel of contrast, no matter be the curve that calculates, or the curve of actual measurement can be found out, material 2 is wider than the bainite transformation interval of material 1, that is to say, under same cooling conditions, except ferrite, also more can easily obtain a small amount of bainite structure, this is mainly that this is also that it can obtain more high-intensity reason because it contains due to the micro alloying element of volume more.
Utilize HXD-1000 type microhardness tester, under load 500g, loading time 15s condition, the Vickers' hardness that records three kinds of central siphon matrixes is as shown in table 2.As can be seen from the table, the hardness of primitive axis tube material matrix is minimum, and invention material 1 and 2 hardness are higher.
Material of the present invention can be used for making the cardan-shaft tube of automobile all size, as be used on Φ 120mm and Φ 89mm cardan-shaft tube, the thin and thick of central siphon can be reduced to respectively 4mm and 3.5mm by original 6mm and 5mm, difference loss of weight 5.42Kg/m and 4.065Kg/m., when improving cardan-shaft tube intensity, alleviate the transmission shaft overall weight, realize the transmission shaft lightweight.
The chemical composition of two kinds of intensity truck drive shaft central siphons of table 1
The hardness of table 2 high strength central siphon and former central siphon matrix
Table 3 high strength central siphon and the contrast of former central siphon mechanical property
| Material | Yield strength Rp0.2 (Mp) | Tensile strength Rm (Mp) | Elongation A5 (%) |
| |
587 | 735 | 17 |
| |
607 | 870 | 14 |
| 440QZ | ≥430MPa | 500-630 | ≥24％ |
| 480QZ | ≥470MPa | 550-680 | ≥24％ |
Claims (2)
1. a truck drive shaft central siphon high-strength steel, is characterized in that being comprised of by weight percentage following element: C0.03～0.1, Si0.05～0.2, Mn1～2.5, P0～0.025, S0～0.001, Al0～0.15, Nb0.01～0.1, Ti0.01～0.15, Fe surplus.
2. method for preparing the described high-strength steel steel plate of claim 1 is characterized in that comprising the following steps:
A. the various starting material that will usually habitually practise are pressed the mentioned component proportioning, smelt in oxygen converter;
B. after the tapping, molten steel becomes the slab of thickness 250mm through furnace rear refining, continuous casting;
C. slab reheats insulation more than 1230 ℃ through walking beam furnace, start rolling temperature is controlled at 1230 ℃, finishing temperature is controlled at 850～900 ℃, it is cooling that the band steel goes out to carry out after finishing train laminar flow, the roll bending temperature is controlled at below 600 ℃, carry out the multi-pass aximal deformation value during roughing rolling, non-recrystallization temperature below 950 ℃ district carries out continuous finish rolling, and increases the finish rolling draft.
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| CN2013100163593A CN103088257A (en) | 2013-01-16 | 2013-01-16 | High-strength steel for automobile transmission shaft axle tube |
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| CN2013100163593A CN103088257A (en) | 2013-01-16 | 2013-01-16 | High-strength steel for automobile transmission shaft axle tube |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106480367A (en) * | 2015-08-28 | 2017-03-08 | 宝钢集团新疆八钢铁有限公司 | A kind of production method of high-strength cold-formed automobile axle housing steel |
| CN108149165A (en) * | 2016-12-05 | 2018-06-12 | 宜兴市零零七机械科技有限公司 | A kind of machining center material of transmission shaft |
| CN108253009A (en) * | 2017-12-28 | 2018-07-06 | 四川飞亚动力科技股份有限公司 | A kind of lightweight bent axle |
| CN112322983A (en) * | 2020-11-12 | 2021-02-05 | 包头钢铁（集团）有限责任公司 | Ti + Nb microalloyed component steel hot-rolled steel strip for steam shaft and preparation method thereof |
| CN112410651A (en) * | 2020-11-10 | 2021-02-26 | 包头钢铁（集团）有限责任公司 | Preparation method of 550 MPa-grade excellent-performance steel strip for automobile transmission shaft pipe |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011006781A (en) * | 2009-05-25 | 2011-01-13 | Nippon Steel Corp | Automobile undercarriage component having excellent low cycle fatigue property and method for producing the same |
-
2013
- 2013-01-16 CN CN2013100163593A patent/CN103088257A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011006781A (en) * | 2009-05-25 | 2011-01-13 | Nippon Steel Corp | Automobile undercarriage component having excellent low cycle fatigue property and method for producing the same |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106480367A (en) * | 2015-08-28 | 2017-03-08 | 宝钢集团新疆八钢铁有限公司 | A kind of production method of high-strength cold-formed automobile axle housing steel |
| CN108149165A (en) * | 2016-12-05 | 2018-06-12 | 宜兴市零零七机械科技有限公司 | A kind of machining center material of transmission shaft |
| CN108253009A (en) * | 2017-12-28 | 2018-07-06 | 四川飞亚动力科技股份有限公司 | A kind of lightweight bent axle |
| CN112410651A (en) * | 2020-11-10 | 2021-02-26 | 包头钢铁（集团）有限责任公司 | Preparation method of 550 MPa-grade excellent-performance steel strip for automobile transmission shaft pipe |
| CN112322983A (en) * | 2020-11-12 | 2021-02-05 | 包头钢铁（集团）有限责任公司 | Ti + Nb microalloyed component steel hot-rolled steel strip for steam shaft and preparation method thereof |
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Application publication date: 20130508 |