CN105543703A - Multi-microalloyed antifatigue carburized gear steel and manufacturing method thereof - Google Patents
Multi-microalloyed antifatigue carburized gear steel and manufacturing method thereof Download PDFInfo
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- CN105543703A CN105543703A CN201511001558.2A CN201511001558A CN105543703A CN 105543703 A CN105543703 A CN 105543703A CN 201511001558 A CN201511001558 A CN 201511001558A CN 105543703 A CN105543703 A CN 105543703A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
Abstract
The invention discloses multi-microalloyed antifatigue carburized gear steel and a manufacturing method thereof, belonging to the technical field of carbon gear steel. The multi-microalloyed antifatigue carburized gear steel comprises the following chemical components in percentage by weight: 0.15-0.25 of C, less than or equal to 0.35 of Si, 0.60-0.90 of Mn, less than or equal to 0.015 of P, less than or equal to 0.010 of S, 0.80-1.20 of Cr, 0.15-0.35 of Mo, 0.02-0.08 of Nb, 0.0005-0.0035 of B, 0.02-0.06 of Al, 0.01-0.04 of Ti, less than or equal to 0.015 of [N], less than or equal to 0.0015 of [O] and the balance of Fe and unavoidable impurities. In order to avoid the condition that the hardenability is reduced by grain refinement, the requirements that Ti>=2[N],and B>=([N]-Ti/3.4)/1.4+0.001 are simultaneously met. Due to the adoption of multi-microalloying treatment and a rolling process with the final rolling temperature of 850-900 DEG C and content reduction of impurities such as [O] in steel, fine dispersed second-phase particles are separated out from the steel, and the growth of austenite crystal grains during carburizing heat treatment is avoided, so that fine-crystal-grain carburized gear steel with the grain size of larger than 10 grades is obtained; and the fatigue property is improved.
Description
Technical field
The invention belongs to carbon Pinion Steel technical field, in particular, provide a kind of multicomponent microalloying antifatigue carbonized Gear Steel and manufacture method thereof.
Background technology
20CrMoH steel (being equivalent to SCM420H steel and the SAE4118H steel of the U.S. of Japan) is one of the most frequently used both at home and abroad carbonized Gear Steel, is widely used in the important gear manufactured in car transmissions.Along with the increase day by day of auto output and consumption, the pressure of resource, environment and the energy also constantly being increased, therefore in the urgent need to improving the use properties of automobile, comprising the aspect such as loss of weight and long lifetime.The raising of car transmissions performance to the long lifetime of automobile and loss of weight most important, the fatigue property therefore improving Automobile Gear Steels has great importance.Crystal grain thinning is a kind of important method improving Automobile Gear Steels fatigue property, the result of study of the people such as U.S. Matlock shows, crystal grain thinning is to improving the antifatigue destructive characteristics effect of gear very significantly (MatlockDKetal.MaterialsResearch, 2007,8:453).But, the carbonized Gear Steel being representative with 20CrMoH steel, because needs are through about the 930 DEG C long-time carburizing treatment of high temperature, in cementation process, its austenite crystal is easily grown up, and is difficult to control below 8 grades.
Can the crystal grain of refinement steel by microalloying method, but the size of the Second Phase Precipitation thing that formed of thinning effect and micro alloying element, quantity, distribution and stability etc. are closely related.In Pinion Steel, usually adopt the content of controls Al, formation AlN precipitated phase carrys out crystal grain thinning, but is easily dissolved in steel under carburizing temperature due to AlN precipitated phase, and its thinning effect is limited.In addition, some Pinion Steel is by adding micro alloying element Ti (the 20CrMnTi Pinion Steel as China) or B (the ZF6 Pinion Steel as Germany), form more insoluble TiN and BN and carry out crystal grain thinning, but because Ti easily forms thick TiN particle and BN easily causes grain-size uneven, the controlling of production process difficulty of these Pinion Steels is larger.
Recently, the Pinion Steel being carried out crystal grain thinning by Nb microalloying is developed one after another both at home and abroad.Japanese Patent JP2000-160288, by adding the Nb of 0.03-0.06%, make the carburizing temperature of the Pinion Steels such as SCr420H bring up to 1050 DEG C, and austenite crystal does not have remarkable alligatoring; China patent ZL200610089371.7 then carries out microalloying by the Nb adding 0.03-0.15%, and develop a kind of close grain Cr-Ni-Mo system heavy-load gear steel of high strength, its autstenitic grain size is higher than 10 grades.Above Nb microalloying Pinion Steel stops austenite to be grown up by separating out Nb (C, N) particle, and Nb (C, N) has higher than AlN stability, easier than TiN and the BN advantage such as to control.But, in Nb microalloying Pinion Steel, due to Nb (C, N) precipitated phase is separated out at austenite grain boundary, the thermoplasticity low ebb district of steel is highlighted (original austenite crystal prevention strength reduction), result causes it easily surface cracking to occur, and hot-work difficulty strengthens (as finishing temperature or final forging temperature can not lower than 900 DEG C).Relative to Cr system and Cr-Ni-Mo system Pinion Steel, add the Cr-Mo system Pinion Steel (as 20CrMoH steel) after Nb because having Mo and the composition characteristic without Ni, its hot-work problem will be more outstanding.
In addition, the hardening capacity of Pinion Steel can decrease because of grain refining, and according to SAEJ406 standard, grain fineness number often increases one-level, and hardening capacity reduces by 8%.In addition, NbC precipitation can make the C content of solid solution in austenite decline, thus reduces hardening capacity further.As adopted Nb microalloying 20CrMoH crystal grain thinning to improve fatigue property, also must consider because grain refining and NbC separate out the hardening capacity decline problem caused.Obviously, can effectively improve Pinion Steel hardening capacity by adding B, but must guarantee that the B added does not have the effect of raising hardening capacity because BN separates out simultaneously.Therefore, when developing fine grain carburizing gear steel, being necessary to carry out multicomponent microalloying treatment process, fully utilizing the advantage of various micro alloying element.
Summary of the invention
The object of the present invention is to provide a kind of multicomponent microalloying antifatigue carbonized Gear Steel and manufacture method thereof, solve the easy alligatoring of existing Pinion Steel carburizing crystal grain, technical barrier that fatigue property is low.After this Pinion Steel carburizing and quenching, grain fineness number improves more than 2 grades, and grain fineness number is greater than 10 grades; Bending fatigue strength (σ after carburizing
-1) than 20CrMoH Pinion Steel raising more than 15%, contact fatigue life (L
10) improve more than 30% than 20CrMoH Pinion Steel.
According to above-mentioned purpose, the technical solution used in the present invention is: (1) by adding micro alloying element Nb, the growing up of austenite crystal when forming NbC and Nb (C, N) to stop carburizing, thus ensure that autstenitic grain size is greater than 10 grades; (2) by adding the elements such as B, Ti, utilizing multicomponent microalloying method, to improve Pinion Steel 800-900 DEG C of thermoplasticity, preventing because plasticity reduces and causing hot-work difficulty to increase; (3) by adding Ti >=2 [N], B >=([N]-Ti/3.4)/1.4+0.001, the hardening capacity of steel is not because grain refining and NbC separate out and reduce to utilize the B of solid solution to ensure; (4) by adding the elements such as Mn, Al, can ensure to obtain low [O] content, thus improving fatigue property; (5) reduce the impurity contents such as P, S, to improve the toughness of cementation zone and matrix, improve fatigue property further; (6) by reducing finishing temperature to 850-900 DEG C, initial grain before refinement carburizing, thus guarantee that autstenitic grain size is greater than 10 grades.
The specific chemical composition (% by weight) of steel of the present invention is: C0.15-0.25, Si≤0.35, Mn0.60-0.90, P≤0.015, S≤0.010, Cr0.80-1.20, Mo0.15-0.35, Nb0.02-0.08, B0.0005-0.0035, Al0.02-0.06, Ti0.01-0.04, [N]≤0.015, [O]≤0.0015, all the other are Fe and inevitable impurity.For ensureing that hardening capacity does not reduce because of grain refining, require Ti >=2 [N], B >=([N]-Ti/3.4)/1.4+0.001 simultaneously.
The effect of each element and proportioning are according to as follows:
C: main solution strengthening element.For ensureing enough working strengths, C content must more than 0.15%; But C content higher than 0.25% time toughness can be made significantly to reduce, unfavorable to gear center toughness.Therefore, C content is because controlling at 0.15-0.25%.
Si: reductor, adds during smelting.But cementation zone is easily oxidized, thus reduces cementation zone toughness, Gears Fatigue Strength is reduced.Therefore, for ensureing deoxidation effect and improving infiltration layer toughness, Si content should control below 0.35%.
Mn: the effective element of deoxidation and desulfurization, adds during smelting; Also be ensure hardening capacity element simultaneously.But similar with Si, cementation zone is easily oxidized, reduces cementation zone toughness, Gears Fatigue Strength is reduced.Therefore, for ensureing deoxidation effect and improving infiltration layer toughness, Mn content should control at 0.60-0.90%.
P: form microsegregation when solidification of molten steel, during heating temperatures, segregation is to crystal boundary after austenite subsequently, and the fragility of steel is enlarged markedly, thus is unfavorable for the raising of gear fatigue property, therefore P content should control below 0.015%.
S: inevitably impurity, forms MnS inclusion and can worsen the toughness of steel at grain boundary segregation, thus be unfavorable for the raising of gear fatigue property.Therefore, S content should control below 0.010%.
Cr: the hardening capacity that effectively can improve steel, to obtain required intensity.For guaranteeing gear through hardening, should 0.80% be not less than, but the cold-forming property of steel can be worsened when Cr content is higher.Therefore, Cr content should control at 0.80-1.20%.
Mo: the hardening capacity that simultaneously effectively can improve matrix and cementation zone.Lower than 0.15% time above-mentioned effect not obvious; But when content is more than 0.35%, promote that grain boundary ferrite film is formed, unfavorable to thermoplasticity, and cost is higher.Therefore, Mo content should control at 0.15-0.35%.
Nb: forming carbonitride can crystal grain thinning, thus effectively reduce carburizing and quenching distortion, and improve toughness.Lower than 0.02% time more than act on not obvious, higher than 0.08% time effect increase not obvious, reach capacity.Therefore, Nb content should control at 0.02-0.08%.
B: segregation improves grain-boundary strength to crystal boundary, improves high-temp plastic and hardening capacity.Lower than 0.0005% time more than act on not obvious, higher than 0.0035% time effect increase not obvious, reach capacity.Simultaneously form BN in order to avoid contained B all combines with [N] and above effect can not be played, require B >=([N]-Ti/3.4)/1.4+0.001.Therefore, B content should control at 0.0005-0.0025%, and B >=([N]-Ti/3.4)/1.4+0.001.
Al: can effectively deoxidation and form AlN crystal grain thinning, content lower than 0.02% time more than act on not obvious, higher than 0.06% time effect increase not obvious, and thick inclusion may be formed, worsen the toughness of steel.Therefore, Al content should control at 0.02-0.06%.
Ti: forming TiN can crystal grain thinning, thus improve toughness and fatigue property; Reduction B combines with [N] and forms BN to guarantee the raising hardening capacity effect of B simultaneously; In addition, the high-temp plastic of Nb bearing steel can be improved.Lower than 0.01% time more than act on not obvious, higher than 0.04% time to form thick TiN unfavorable to fatigue property.Therefore, Ti content should control at 0.01-0.04%, and Ti >=2 [N].
[N]: smelt inevitable gas, can combine with Ti, Nb, B, Al etc. and form compound, thus crystal grain thinning, but also can segregation crystal boundary and reduce grain-boundary strength.Higher than 0.015% time detrimental action obvious.Therefore, [N] content should control below 0.015%.
[O]: obnoxious flavour, seriously reduces fatigue property.[O] content should be controlled below 0.0015% by multiple deoxidation means.
The present invention can adopt converter, electric arc furnace and induction furnace are smelted, and can again through Fruit storage, then pours into steel ingot or continuous casting becomes base, after cogging, be rolled into the products such as bar.In addition, during rolling, should ensure that finishing temperature is below 900 DEG C, makes the second-phases such as Nb (C, N) fully separate out, and Austenite Grain Growth when avoiding cooling subsequently, thus guarantee that original grain degree is more than 10 grades before carburizing treatment.The technical parameter of concrete technology step and control is as follows:
(1) electric furnace, converter and induction furnace smelting+refining, control cleanliness factor P≤0.015%, S≤0.010%, carbon, alloying element and micro alloying element control in target zone;
(2) Fruit storage, controls [N]≤0.0150%, [O]≤0.0015%;
(3) teeming or continuous casting become base;
(4) bar is rolled into after cogging, Heating temperature 1200 ~ 1250 DEG C, finishing temperature 850 ~ 900 DEG C.
The present invention is compared with existing Carbonized Gear Steel for Automobile 20CrMoH, steel of the present invention not only crystal grain is tiny, and toughness and fatigue property increase substantially, thus the life-span of car transmissions gear can be made to improve, maybe can adopt comparatively fine module gear transmission equal-wattage, thus create conditions for automobile loss of weight.
Embodiment
According to above-mentioned designed chemical composition ranges, 500kg induction furnace has been smelted 3 stoves (heat (batch) number 1-3) steel of the present invention, in addition also have the 2 stove steel of the present invention (heat (batch) number 4-5) smelted through 30t industrial furnace+furnace outer refining process (EAF+LF+VD) and 3 stove 20CrMoH compared steel (heat (batch) number 6-8), its specific chemical composition is as shown in table 1.Pouring molten steel becomes ingot, and through hammer cogging, is finally rolled into φ 55mm bar.The finishing temperature that 20CrMoH compared steel adopts is 900 DEG C, and the finishing temperature that invention steel adopts is 880 DEG C and 850 DEG C, table 2.
Invention steel and compared steel are processed into normal room temperature tension specimen (L
0=5d
0, d
0=5mm), Charpy notch impact specimen (10mm × 10mm × 55mm), carburizing metallographic specimen (φ 10mm × 25mm), rotary bending fatigue sample (φ 14mm × 160mm), rolling contact fatigue sample (φ 50mm × 10mm) and steel end-quenched (φ 25mm × 120mm).Tension specimen becomes final size with impact specimen through 860 DEG C of insulation oil quenchings, 180 DEG C of tempering, 2 hours post-treatment, and carries out corresponding test by GB, and its mechanical property is as shown in table 2.After steel end-quenched is incubated 30 minutes through 930 DEG C, air cooling normalizing treatment is processed into standard test specimen, and carry out end quenching test by GB and measure ending quenching hardness, J10 point hardness value is in table 2.
Metallographic specimen and fatiguespecimen cool to 830 DEG C of oil coolings after carburizing in 930 DEG C, 7 hours (surperficial carbon potential 1%), finally by 180 DEG C, air cooling after 2 low-temperature tempering.After carburizing thermal treatment, metallographic specimen is again through grinding, polishing, and after supersaturation picric acid aqueous corrosion, utilize division lines method to record the original austenite grain degree of cementation zone, result is as shown in table 2.In addition, invention steel and compared steel sample Carburized Characteristic do not have significant difference: surface hardness is all at about HRC60, and case depth is about 1.2mm, and cementation zone carbide is 1 grade, and martensite and residual austenite are 1-2 level.
After rotary bending fatigue sample after carburizing thermal treatment and rolling contact fatigue sample are carried out being finish-machined to final size, on rotating bending fatigue machine, measure fatigue strength by national standard respectively and measure contact fatigue life on rolling contact fatigue-testing machine.Wherein fatigue strength adopts lifting and lowering method to record, and load added by contact fatigue is 4410MPa.Experiment on fatigue properties result also arranges in table 2.
As can be seen from table 2 result, the impelling strength of steel of the present invention is apparently higher than compared steel 20CrMoH, and the grain fineness number of cementation zone is more than 10 grades, and compared steel is below 8 grades.In fatigue property, the bending fatigue strength (σ of invention steel
-1) improve more than 15%, the specified contact fatigue life (L of invention steel than compared steel 20CrMoH
10) improve more than 30% than compared steel 20CrMoH.In addition, the end quenching J10 hardness value of invention steel is suitable with compared steel 20CrMoH, illustrates that its hardening capacity does not obviously reduce because of grain refining.
The chemical composition of table 1 embodiment and compared steel, % by weight
The mechanical property of table 2 embodiment and compared steel, grain size number and fatigue property
Claims (2)
1. a multicomponent microalloying antifatigue carbonized Gear Steel, is characterized in that, chemical component weight % is: C0.15-0.25, Si≤0.35, Mn0.60-0.90, P≤0.015, S≤0.010, Cr0.80-1.20, Mo0.15-0.35, Nb0.02-0.08, B0.0005-0.0035, Al0.02-0.06, Ti0.01-0.04, [N]≤0.015, [O]≤0.0015; Surplus is Fe and inevitable impurity; Require Ti >=2 [N], B >=([N]-Ti/3.4)/1.4+0.001 simultaneously.
2. the manufacture method of a multicomponent microalloying antifatigue carbonized Gear Steel according to claim 1, converter, electric arc furnace and induction furnace is adopted to smelt, again through Fruit storage, then pour into steel ingot or continuous casting becomes base, the technical parameter being rolled into bar concrete technology step and control after cogging is as follows:
(1) electric furnace, converter and induction furnace smelting+refining, control cleanliness factor P≤0.015%, S≤0.010%, carbon, alloying element and micro alloying element control in target zone;
(2) Fruit storage, controls [N]≤0.0150%, [O]≤0.0015%;
(3) teeming or continuous casting become base;
(4) bar is rolled into after cogging, Heating temperature 1200 ~ 1250 DEG C, finishing temperature 850 ~ 900 DEG C.
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Cited By (7)
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| CN109023102A (en) * | 2018-09-21 | 2018-12-18 | 首钢集团有限公司 | A kind of super harden ability axle steel of microalloying |
| CN111570513A (en) * | 2020-05-25 | 2020-08-25 | 江苏联峰实业有限公司 | Fine-grain gear steel and preparation method thereof |
| CN113234998A (en) * | 2021-04-21 | 2021-08-10 | 马鞍山钢铁股份有限公司 | Nb-Ti microalloyed high temperature resistant carburized gear steel and manufacturing method thereof |
| CN113416899A (en) * | 2021-06-24 | 2021-09-21 | 马鞍山钢铁股份有限公司 | Nb and B microalloyed gear steel and preparation method, heat treatment method, carburization method and carburized gear steel thereof |
| CN114000055A (en) * | 2021-10-21 | 2022-02-01 | 山东钢铁股份有限公司 | Boron microalloyed gear steel and preparation method thereof |
| CN115537678A (en) * | 2021-06-30 | 2022-12-30 | 宝山钢铁股份有限公司 | Steel for high-temperature carburization gear and manufacturing method thereof |
| JP7477343B2 (en) | 2020-03-31 | 2024-05-01 | 株式会社神戸製鋼所 | Case hardening steel with excellent machinability, manufacturability and grain coarsening prevention properties |
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Cited By (9)
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| CN109023102A (en) * | 2018-09-21 | 2018-12-18 | 首钢集团有限公司 | A kind of super harden ability axle steel of microalloying |
| JP7477343B2 (en) | 2020-03-31 | 2024-05-01 | 株式会社神戸製鋼所 | Case hardening steel with excellent machinability, manufacturability and grain coarsening prevention properties |
| CN111570513A (en) * | 2020-05-25 | 2020-08-25 | 江苏联峰实业有限公司 | Fine-grain gear steel and preparation method thereof |
| CN113234998A (en) * | 2021-04-21 | 2021-08-10 | 马鞍山钢铁股份有限公司 | Nb-Ti microalloyed high temperature resistant carburized gear steel and manufacturing method thereof |
| CN113416899A (en) * | 2021-06-24 | 2021-09-21 | 马鞍山钢铁股份有限公司 | Nb and B microalloyed gear steel and preparation method, heat treatment method, carburization method and carburized gear steel thereof |
| CN113416899B (en) * | 2021-06-24 | 2022-04-19 | 马鞍山钢铁股份有限公司 | Nb and B microalloyed gear steel and preparation method, heat treatment method, carburization method and carburized gear steel thereof |
| CN115537678A (en) * | 2021-06-30 | 2022-12-30 | 宝山钢铁股份有限公司 | Steel for high-temperature carburization gear and manufacturing method thereof |
| CN115537678B (en) * | 2021-06-30 | 2024-01-09 | 宝山钢铁股份有限公司 | Steel for high-temperature carburized gear and manufacturing method thereof |
| CN114000055A (en) * | 2021-10-21 | 2022-02-01 | 山东钢铁股份有限公司 | Boron microalloyed gear steel and preparation method thereof |
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