CN101096742A - High-strength pinion steel for vehicles - Google Patents
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- CN101096742A CN101096742A CNA2006100282658A CN200610028265A CN101096742A CN 101096742 A CN101096742 A CN 101096742A CN A2006100282658 A CNA2006100282658 A CN A2006100282658A CN 200610028265 A CN200610028265 A CN 200610028265A CN 101096742 A CN101096742 A CN 101096742A
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Abstract
The invention discloses a pinion steel of high-strength automobile, which comprises the following parts: 0.20-0.40% C, 0.20-0.50% Si, 0.50-1.00% Mn, 0.80-1.30% Cr, 0.015-0.080% Nb, 0.030-0.090% V, 0.15-0.55% Mo, 0.015-0.050% Al. The invention minimizes the heat processing deformation quantity with high matching rate, which lengthens the life with low cost.
Description
Technical field
The present invention relates to a kind of Pinion Steel, particularly the automobile high-strength Pinion Steel.
Background technology
Recently, demand along with automobile industry developments such as automobile lightweight and environmental protection and saving fuel oils, the design stress that improves gear promptly requires the main direction of steel high strength conduct automobile gear steel development both at home and abroad, but, problems such as core hardening capacity deficiency, terminal hardenability band control broad in use often appear in the existing new trade mark Pinion Steel of introducing, the gear unstable properties will appear after for some time uses, cause more gear changing difficulty of user, and may produce a series of safety problems, the stability that therefore improves the Pinion Steel performance becomes the task of top priority.
Up to now, 22CrMoH steel (SCM822H that is equivalent to Japan) generally has been used on the automobile axle gear, and the ending quenching hardness scope of these Pinion Steels is that 33～41HRC, hardenability band≤8HRC, grain fineness number require 〉=5 grades.But the developing goal of recent years requires to be hardenability band≤4HRC, grain fineness number 〉=7 grade.Existing Pinion Steel often can not satisfy this respect requirement, and crucial problem is that Composition Control is inhomogeneous, and autstenitic grain size is evenly tiny inadequately to cause its terminal hardening capacity stable inadequately.Therefore, good through hardening performance (narrow hardenability band) and the tiny and uniform high strength gear of the crystal grain steel of exploitation becomes the theme that current steel grade is developed and manufactured experimently.
Existing Pinion Steel is as shown in table 1:
Table 1 (wt%)
| The patent No. | C | Si | Mn | Cr | Mo | Nb | V | Al | Ni | Cu |
| JP 4088148 | 0.1/ 0.2 | 0.05/ 0.10 | 0.3/ 1.0 | 0.5/ 1.5 | (Cr or) 0.5 2.0 | 0.005/ 0.07 | 0.005/ 0.07 | |||
| JP 4083848 | 0.15/ 0.25 | ＜＝ 0.20 | 0.40/ 0.70 | 0.4/ 0.7 | 0.6/ 1.5 | 0.015/ 0.030 | 0.015 /0.03 | 1.0/ 3.0 | ||
| JP 4124217 | 0.13/ 0.25 | ＜＝ 0.05 | 0.3/ 1.0 | 0.1/ 1.0 | 0.2/ 1.0 | 0.01/ 0.10 | ||||
| JP 3061348 | 0.4/ | 0.05/ | 0.3/ | 0.01 | 0.02/ | 0.01/ | 0.001 | 0.001 |
| 1.3 | 1.0 | 1.5 | /1.5 | 0.30 | 0.10 | /2.0 | /0.30 | |||
| JP 10017928 | 0.50/ 0.75 | 0.5/ 1.8 | 0.1/ 0.4 | 0.05 /0.5 | 0.019 /0.05 |
Patent JP 4088148 invention steel mainly by adding an amount of Nb, V to improve the fatigue strength of its tooth root and the flank of tooth, are compared with steel of the present invention, and its C, Si content are lower, be suitable for rapid carburization, but intensity is lower than steel of the present invention relatively, and Cr and adding simultaneously of Mo, and hardening capacity improves not enough;
Patent JP 4083848 invention steel are by bending and the impact fatigue performance of alloying elements such as compound adding Nb, Ni with the raising gear, but this steel grade Nb content is lower, be not enough to bring into play the precipitation strength (solid solution Nb) of Nb and the dual strengthening effect of precipitation strength (niobium carbide), therefore the crystal grain thinning effect of Nb is not fully exerted, cause its intensity slightly inadequate, other alloy contents of this steel are higher simultaneously, and cost increases;
The grain fineness number that patent JP 4124217 invention steel come the refinement steel by the micro alloying elements such as Mo, Ni that add different content, and increase its anti-quenching strain ability, but the main purpose of this steel grade is to improve the toughness and the stability of steel, does not take into full account high-intensity service requirements;
Patent JP 3061348, JP 10017928 invention steel are strong hardened Pinion Steel (high-carbon), add alloying element mainly in order to improve the core toughness of gear.
As can be seen, such steel grade generally all needs to carry out follow-up carburizing treatment, requires the hardenability band must be very narrow, so that the heat treatment deformation of the gear of producing in batches is less, the pairing rate improves, therefore must those composition fluctuations to the big element of hardening capacity influence of strict control.Existing homemade Pinion Steel all exists hardening capacity deficiency or the narrow inadequately problem of hardenability band control, does not satisfy the requirement of current automotive performance stability and high efficiency.In addition, metals resources such as China Mo, Ni are abundant to be lacked, and costs an arm and a leg.Therefore, the content that reduces this dvielement in the steel has the significance of energy efficiency.
Summary of the invention
The object of the present invention is to provide a kind of high-strength pinion steel for vehicles, have hardening capacity excellence (narrow hardenability band) and tiny, the low-cost characteristics of uniform crystal particles.
For achieving the above object, technical scheme of the present invention is,
High-strength pinion steel for vehicles, its composition quality per-cent be,
C：0.20～0.40
Si：0.20～0.50
Mn：0.50～1.00
Cr：0.80～1.30
Nb：0.015～0.080
V：0.015～0.10
Mo：0.15～0.55
Al：0.015～0.050
All the other are Fe and unavoidable impurities.
Steel of the present invention adds hardening capacity and the intensity that Nb has improved steel, and its reason is because Nb has added the back refinement grain-size of original austenite, has improved the comprehensive mechanical property of steel; The recovery rate of Nb in molten steel nearly 100%, alloying is accurate, and it is little to be reflected on the performance data dispersity; In addition, the carbonitride of Nb can " pinning " crystal boundary when steel rolling, stops grain growth, and solid solution Nb in crystal boundary enrichment concentration up to (atomic ratio) more than 1.0%, intracrystalline is lower, so it has the dual ability that crystal boundary moves that pulls strongly.It is in order to make its ratio (2: 3) that exists with precipitate form and solid solution attitude in thermal distortion reach best, can to save cost simultaneously that the content of Nb is controlled at 0.015～0.08wt%.
V be a kind of can refinement the grain structure of steel and the element that improves intensity, toughness and the wear resistance of steel, and when it when high temperature fuses into austenite, can increase the hardening capacity of steel.The carbide of V and nitride can play the effect of precipitation strength.When the content of V was lower than 0.030wt%, strengthening effect was not obvious, but a large amount of precipitations of the carbide of V and nitride will cause the toughness of steel to descend, and therefore the content of controlling V is taked to add Nb simultaneously and improved the loss in toughness that adding V brings below 0.090wt%.
Carbon is to guarantee the necessary composition of gear working strength, but when alleviating vehicle weight requirement high strength, should limit carbon content, and simultaneously, carbon is the vital element of hardening capacity that influences steel.It is not enough that carbon content is lower than 0.20% strength of gear teeth, and can not guarantee the requirement of good hardening capacity, is higher than the requirement that can not satisfy the gear center toughness after 0.40%.Therefore, determine that carbon content is 0.2～0.4%.
Add Cr in the steel and can improve its hardening capacity and intensity, wear resistance, and play certain antioxygenation.Cr content is lower than 0.8%, and is very unobvious to the contribution of intensity and hardening capacity.In addition, Cr obviously reduces the toughness of quenching and tempering steel, does not have too big influence but content is lower than at 1.30% o'clock.Meanwhile, Cr has reduced the activity of carbon, can prevent to heat, the decarburization behavior in the rolling and heat treatment process, has therefore increased reliability.When Cr amount less than 0.8% the time, this effect is just not obvious.So Cr content is controlled at 0.8～1.30%.
Mo can obviously improve the hardening capacity and the heat resistance of steel, prevents temper brittleness and overheated tendency, and the energy crystal grain thinning, improves the intensity and the toughness of steel.Cr content can obviously increase the plasticity of steel less than 0.6% o'clock, reduced hot cracking tendency, but was higher than at 0.55% o'clock, and Mo increases the reheat crack(ing) tendency of steel, and simultaneously, Mo costs an arm and a leg, and cost is higher, generally should save use.So Mo content generally is controlled at 0.15～0.55%.
Mn can be dissolved in ferrite, plays solution strengthening, can also strengthen austenitic stability, reduces M
sPoint improves hardening capacity, and simultaneously, Mn helps eliminating the deleterious effect of S, helps deoxidation again.But find to act on less than 0.5% the time less when the Mn amount.After Mn content surpassed 1.0%, hardening capacity improved very big, and toughness degenerates when hot rolling, so that influenced the production of steel wire.Therefore Mn content is controlled between 0.5～1.0%.
The present invention also provides the chemical ingredients of series of gears steel.Usually in fact, the control of the hardening capacity of Pinion Steel and bandwidth thereof is that the content of the elements such as carbon, manganese, chromium by changing steel and distributing is realized.But the adding of these elements will certainly reduce the toughness of steel to some extent, even inadequately tiny its stability decreases that makes of crystal grain in the tissue, and it is bigger to cause rigidity to fluctuate.The problem of hardening capacity deficiency or hardenability band broad all occurs as the SCM822H of Japan after the production domesticization and the SAE8620H of the U.S. etc., this has a strong impact on the use properties of gear.By after adding an amount of Nb, V, Mo content can be reduced to lower level, has saved cost among the present invention, and through hardening performance (hardenability band) does not descend.Its reason be since the adding refinement of alloying elements such as Nb, V initial austenite grain-size and in matrix, formed the tiny precipitated phase that hinders dislocation glide, strengthened the uniform and stable property of its tissue.Simultaneously, obviously improved the hardening capacity of steel, and hardenability band control is narrower, and performance inconsistency is little.
Beneficial effect of the present invention
In the steel of the present invention because compound Nb, the V of having added, refinement the grain-size of original austenite, increased steel hardening capacity, improved the comprehensive mechanical property of steel; In addition, being added in when having improved hardness of steel of alloying elements such as Nb, V, Al improved the toughness of steel.These effects are improved significantly intensity, toughness and the hardening capacity of steel, and make its hardenability band wide region be controlled on the higher level (≤4HRC).
Can greatly improve the hardening capacity of steel among the present invention behind compound adding niobium, vanadium, the aluminium micro alloying element, the through hardening bandwidth is obviously dwindled, thereby the performance that has reduced product is the fluctuation range of hardness especially, makes that finally gear thermal treatment after strain amount is less, and the pairing rate improves; Simultaneously, adopt the method for compound interpolation niobium, vanadium to give full play to the good complementary action of the two strength and toughness, its over-all properties improves greatly.In addition, hardening capacity scope that the present invention comes stabilized steel from the angle of grain refining has changed always the idea that the purity that promptly improves steel from the angle of steel-making increases stability.Therefore, the new gear steel of handling in this way can be made heavily stressed, the stable strict automobile gear of performance requriements.In addition, compare with existing Pinion Steel, steel of the present invention is with low cost, reduced the consumption of strategic elements such as Mo, Ni, and by having improved the comprehensive mechanical property of steel behind Nb, V, the Al micro alloying element, this meets energy-saving and cost-reducing mentality of designing fully.
Embodiment
Embodiments of the invention are referring to table 2.
Table 2 wt%
| C | Si | Mn | Cr | Mo | Al | Nb | V | Ni | Fe | |
| Embodiment 1 | 0.22 | 0.24 | 0.73 | 0.89 | 0.43 | 0.032 | 0.031 | 0.062 | Surplus | |
| Embodiment 2 | 0.23 | 0.21 | 0.70 | 1.00 | 0.35 | 0.030 | 0.051 | 0.071 | Surplus | |
| Embodiment 3 | 0.38 | 0.20 | 0.50 | 0.80 | 0.54 | 0.050 | 0.015 | 0.100 | Surplus | |
| Embodiment 4 | 0.35 | 0.50 | 1.00 | 1.20 | 0.15 | 0.015 | 0.080 | 0.030 | Surplus | |
| Embodiment 5 | 0.20 | 0.30 | 0.74 | 0.95 | 0.31 | 0.020 | 0.025 | 0.090 | Surplus | |
| Embodiment 6 | 0.30 | 0.25 | 0.70 | 1.30 | 0.40 | 0.030 | 0.050 | 0.020 | Surplus | |
| Embodiment 7 | 0.40 | 0.43 | 0.65 | 1.10 | 0.26 | 0.030 | 0.065 | 0.045 | Surplus | |
| Comparative example 1 | 0.23 | 0.28 | 0.82 | 1.09 | 0.41 | 0.03 | Surplus | |||
| Comparative example 2 | 0.15 | 0.07 | 0.61 | 0.99 | 0.033 | 0.80 | 0.56 | Surplus | ||
| Comparative example 3 | 0.21 | 0.15 | 0.54 | 0.62 | 1.03 | 0.022 | 0.022 | 2.00 | Surplus |
Annotate: comparative example 1 grade of steel is Japanese trade mark SCM822H (being equivalent to Chinese trade mark 22CrMoH)
Comparative example 2 grades of steel are patent (JP 4083848)
Comparative example 3 grades of steel are patent (JP 4088148)
The grain fineness number of table 3 test steel detects
| Grade of steel | Grain size number |
| Embodiment 1 | 8 |
| Embodiment 2 | 9 |
| Embodiment 3 | 7 |
| Embodiment 4 | 9 |
| Embodiment 5 | 7 |
| Embodiment 6 | 8 |
| Embodiment 7 | 8 |
| Comparative example 1 | 5 |
| Comparative example 2 | 5 |
| Comparative example 3 | 7 |
The test steel is measured grain fineness number with relative method in the table 2, evaluates its grain size number with the first levels of the standard figure among the YB 27-77.Table 3 is the grain size number assay of test steel.As can be seen, steel of the present invention makes the obvious refinement of crystal grain in its tissue through adding Nb, V, Al element.
Behind 925 ℃ of normalizings, 925 ℃ of following end quenchings and measure its ending quenching hardness (pressing GB/T 5216-2004), its result is as shown in table 4 after medium-frequency induction furnace is smelted, forged for test steel in the table 2; Get the steel ingot different sites simultaneously and make hardenability test, detect the hardenability band scope (being shown in Table 5) of test steel.As can be seen, after in steel, adding niobium and vanadium, the control of the hardening capacity of steel of the present invention and hardenability band all obviously is better than contrasting steel B1 and B2, and in the steel of the present invention by compound interpolation Nb, V, Al element, its hardening capacity and bandwidth are controlled and have all been obtained raising in various degree.
The hardening capacity (HRC) of table 4 test steel
| Grade of steel | 1.5 | 3 | 5 | 7 | 9 | 11 | 13 | 15 | 20 | 25 | 30 |
| Embodiment 1 | 48.7 | 47.8 | 46.4 | 45.8 | 45.4 | 43.6 | 41.0 | 39.2 | 37.3 | 35.3 | 32.6 |
| Embodiment 2 | 45.2 | 45.0 | 44.5 | 43.7 | 43.5 | 42.4 | 40.2 | 38.4 | 34.5 | 31.6 | 29.5 |
| Embodiment 3 | 49.7 | 48.5 | 47.4 | 46.0 | 45.6 | 44.4 | 42.5 | 40.8 | 36.7 | 33.6 | 31.5 |
| Embodiment 4 | 44.2 | 43.5 | 42.8 | 40.6 | 38.9 | 36.0 | 34.4 | 32.1 | 30.9 | 28.9 | 27.8 |
| Embodiment 5 | 45.4 | 44.8 | 43.9 | 42.7 | 41.8 | 38.6 | 36.4 | 34.5 | 32.3 | 29.8 | 26.9 |
| Embodiment 6 | 48.8 | 47.2 | 46.1 | 44.0 | 43.5 | 42.1 | 40.8 | 38.7 | 36.5 | 32.2 | 30.9 |
| Comparative example 1 | 45.0 | 44.8 | 43.5 | 36.5 | 33.6 | 30.1 | 28.2 | 26.4 | 24.3 | 23.4 | 22.5 |
| Comparative example 2 | 38.4 | 36.2 | 30.4 | 28.4 | 25.0 | 19.8 | 16.9 | 14.1 | 13.0 | 12.9 | 13.1 |
| Comparative example 3 | 50.2 | 48.5 | 45.2 | 43.6 | 42.2 | 40.1 | 38.9 | 38.0 | 35.7 | 33.5 | 30.2 |
The hardenability band (HRC) of table 5 test steel
| Grade of steel | 1.5 | 3 | 5 | 7 | 9 | 11 | 13 | 15 | 20 | 25 | 30 |
| Embodiment 1 | 3.2 | 2.4 | 1.4 | 2.7 | 3.5 | 3.1 | 3.9 | 2.3 | 2.4 | 3.9 | 2.2 |
| Embodiment 2 | 1.5 | 2.3 | 1.2 | 1.3 | 2.6 | 2.1 | 2.8 | 3.3 | 2.4 | 2.6 | 2.0 |
| Embodiment 3 | 3.7 | 3.8 | 1.6 | 4.2 | 4.1 | 3.5 | 3.6 | 4.0 | 3.6 | 2.9 | 3.7 |
| Embodiment 4 | 1.1 | 2.1 | 2.5 | 2.2 | 3.5 | 2.5 | 3.4 | 2.8 | 3.0 | 3.8 | 3.2 |
| Embodiment 5 | 3.4 | 3.6 | 3.0 | 2.9 | 2.4 | 1.7 | 3.5 | 4.5 | 4.1 | 4.0 | 3.5 |
| Embodiment 6 | 2.6 | 2.0 | 1.5 | 2.4 | 1.9 | 2.8 | 3.4 | 2.3 | 1.8 | 3.3 | 2.6 |
| Comparative example 1 | 5 | 4 | 4.8 | 4.5 | 2.9 | 2.7 | 2.8 | 1.9 | 1.6 | 0.8 | 2.5 |
| Comparative example 2 | 7 | 7 | 9 | 9 | 10 | 10 | 9 | 8 | 7 | 9 | 8.5 |
| Comparative example 3 | 4.2 | 3.4 | 5.0 | 2.3 | 2.7 | 5.2 | 6.0 | 4.5 | 3.6 | 3.4 | 2.9 |
The test steel is made gear through field conduct, and (carburized layer depth is that the sample after 1.4～1.6mm) carries out the monodentate fatigue-bending test, and the load of rotating bending fatigue machine is 90Nm, and rotating speed is 3000r/min with carburizing and quenching again.As can be seen from Table 6, steel of the present invention is because the compound grain structure that added Nb, V refinement, and its flexural fatigue performance all is higher than or approaches to contrast steel.
The fatigue property of table 6 test steel
| Grade of steel | Bending fatigue strength (Mpa) | Circulation cycle (* 10 6Inferior) (l) |
| Embodiment 1 | 1310 | 9.5 |
| Embodiment 2 | 1390 | More than 10 |
| Embodiment 3 | 1270 | 8.5 |
| Embodiment 4 | 1395 | More than 10 |
| Embodiment 5 | 1220 | 8.0 |
| Embodiment 6 | 1290 | 9.3 |
| Comparative example 1 | 1170 | 6.0 |
| Comparative example 2 | 1280 | 8.0 |
| Comparative example 3 | 1210 | 9.0 |
Annotate: (1) Contact Stress of Gear is 600kgf/mm
2
The present invention compares with existing pinion steel, all in different scopes, this is because due to the difference of steel grade service condition, simultaneously to carbon content, the alloy of existing pinion steel adds mainly take the intensity that improves steel as main, with the purpose of steel microalloying of the present invention certain difference is arranged. In addition, compare with existing pinion steel, steel of the present invention is mainly by behind an amount of Nb of compound adding, V, the Al, the crystal grain of steel obtains refinement, quenching degree improves, the cooperation of intensity and toughness is better than existing pinion steel, and the alloying element content integral body that the present invention adds will be lower than existing pinion steel, so cost is lower.
Claims (1)
1. high-strength pinion steel for vehicles, its composition quality per-cent be,
C 0.20～0.40
Si 0.20～0.50
Mn 0.50～1.00
Cr 0.80～1.30
Nb 0.015～0.080
V 0.015～0.10
Mo 0.15～0.55
Al 0.015～0.050
All the other are Fe and unavoidable impurities.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006100282658A CN100473746C (en) | 2006-06-28 | 2006-06-28 | High-strength pinion steel for vehicles |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006100282658A CN100473746C (en) | 2006-06-28 | 2006-06-28 | High-strength pinion steel for vehicles |
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| Publication Number | Publication Date |
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| CN101096742A true CN101096742A (en) | 2008-01-02 |
| CN100473746C CN100473746C (en) | 2009-04-01 |
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| CNB2006100282658A Expired - Fee Related CN100473746C (en) | 2006-06-28 | 2006-06-28 | High-strength pinion steel for vehicles |
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| CN102011057A (en) * | 2010-12-27 | 2011-04-13 | 承德建龙特殊钢有限公司 | CrMnTi series gear steel and processing technique thereof |
| CN104195452A (en) * | 2014-08-27 | 2014-12-10 | 南京创贝高速传动机械有限公司 | Drive gear and preparation method thereof |
| CN104928588A (en) * | 2015-05-14 | 2015-09-23 | 机械科学研究院浙江分院有限公司 | High-temperature carburizing steel and melting method |
| CN105316592A (en) * | 2014-07-29 | 2016-02-10 | 宝钢特钢有限公司 | High-strength high-tenacity gear steel and fabrication method thereof |
| CN105543644A (en) * | 2015-12-03 | 2016-05-04 | 抚顺特殊钢股份有限公司 | Novel manufacturing technology of super-large size gear steel SCM822H for industrial speed reducer |
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| CN105316592A (en) * | 2014-07-29 | 2016-02-10 | 宝钢特钢有限公司 | High-strength high-tenacity gear steel and fabrication method thereof |
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| CN106048426B (en) * | 2015-04-14 | 2020-03-27 | 现代自动车株式会社 | Carbon steel composition for steering rack having reduced thermal strain and method for manufacturing same |
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| CN112962023A (en) * | 2021-01-29 | 2021-06-15 | 江苏永钢集团有限公司 | Narrow hardenability gear steel and manufacturing method thereof |
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