CN105568158A - Nickel-chromium-free impact-resistant bearing steel and producing method thereof - Google Patents
Nickel-chromium-free impact-resistant bearing steel and producing method thereof Download PDFInfo
- Publication number
- CN105568158A CN105568158A CN201410554526.4A CN201410554526A CN105568158A CN 105568158 A CN105568158 A CN 105568158A CN 201410554526 A CN201410554526 A CN 201410554526A CN 105568158 A CN105568158 A CN 105568158A
- Authority
- CN
- China
- Prior art keywords
- steel
- refining
- rolled
- billet
- temperature
- 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
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses nickel-chromium-free impact-resistant bearing steel and a producing method thereof. The nickel-chromium-free impact-resistant bearing steel comprises the following components by weight: 0.58-0.68% of C, 1.25-1.55% of Si, 0.28-0.58% of Mn, 0.58-0.68% of Mo, 0.15-0.25% of V, 0.015-0.08% of Nb, 0.010-0.040% of Al, less than or equal to 0.015% of P, less than or equal to 0.25% of Cu, less than or equal to 0.0010% of O, less than or equal to 0.015% of S, and the balance of Fe and unavoidable impurities. The preparation method of the steel adopts a two-step technologic process, including: 1, carrying out initial refining in an electric arc furnace (or a converter), then carrying out vacuum refining in a ladle furnace, and at last carrying out continuous casting and pouring; 2, carrying out hot working for rolling the finished material with a rolling mill. The steel disclosed by the invention is free of precious alloy elements such as chromium and nickel, low in cost and simple in producing process; the bearing product prepared by the steel can be applied to the severe working environment and is long in service life.
Description
Technical field
The invention belongs to field of alloy steel, relate generally to a kind of shock-resistant bearing steel and manufacture method thereof of Chrome-free nickel.
Background technology
The bearing that the mechanical means such as engineering machinery, mining, excavation are used, because of its Working environment very severe, often bear too much shock load, work-ing life is very low.Tradition high-carbon-chromium bearing steel such as GCr15, GCr15SiMn etc., although have certain wear resistance because carbon content is higher but its shock-resistant ability is comparatively weak.And carburizing bearing steel, the carburizing bearing steels such as such as G20CrNi2MoA, G20Cr2Ni4Mo, because of often expensive containing higher alloying element, carburization process is comparatively complicated in addition, so its application is also subject to a definite limitation.
For solving the problem, achieve some achievements both at home and abroad in the research of shock-resistant bearing steel, wherein, patent achievement is as shown in table 1.
The shock-resistant bearing steel patent documentation of table 1 compares
Patent in table 1 is the patent of invention of shock-resistant bearing steel.Patent No. CN102605256 " one mixes rare earth bearing steel and preparation method thereof ", a kind of high-carbon-chromium bearing steel in essence, improving toughness by adding rare earth element, adopting the processing method of vacuum induction+remelting, manufacturing cost is high, adding of rare earth element be not easy to control.The common feature of patent No. CN100587099, CN101724742, CN101624677, CN101376948 does not add Cr, by adopting the microalloy element such as V, Nb, Ti, Re to obtain relatively good toughness to solve impact property, but impact resistance under being difficult to meet complex working conditions.Patent No. CN101230441 is a kind of typical Cr-Ni-Mo steel adding Nb, V, is reached the object improving toughness by microalloy effect.Patent No. JP07278740, JPS62274052 are carburizing bearing steels, reaching the interior tissue after surface abrasion resistance, thermal treatment by surface carburization process is tempered sorbite, impact resistance generally can meet complicated working condition, but carburization process complex process, general Bearing Manufacturing Enterprise be difficult to grasp or manufacturing cost high.
In sum, existing shock-resistant bearing steel still has the following disadvantages: (1) existing high-carbon-chromium bearing steel impact resistance is bad; (2) existing Cr-Ni bearing steel, the carburizing bearing steels such as such as G20CrNi2MoA, G20Cr2Ni4Mo, on the one hand because expensive alloying elements content is high, carburization process is complicated on the other hand, is difficult to meet the simple requirement of low cost process; (3) the existing bearing steel not containing Cr, Ni can solve carbide problem, but is difficult to the impact property requirement under solution complex working conditions.
Summary of the invention
The present invention devises the shock-resistant bearing steel of a kind of Chrome-free ni-type, not adopting valuable Cr-Ni alloying element namely by adding the alloying elements such as silicon, manganese, molybdenum and corresponding Composition Design in steel, obtaining the excellent bearing steel of impact resistance through smelting-vacuum refinement-cast-rolling-annealing.
For achieving the above object, the technical solution adopted in the present invention is as follows:
A shock-resistant bearing steel for Chrome-free nickel, it comprises the following component of percentage:
C:0.58 ~ 0.68%; Si:1.25 ~ 1.55%; Mn:0.28 ~ 0.58%; Mo:0.58 ~ 0.68%; V:0.15 ~ 0.25%; Nb:0.015 ~ 0.08%; Al:0.010 ~ 0.040%; P :≤0.015%; Cu :≤0.25%; O :≤0.0010%; S :≤0.015%; Surplus is Fe and inevitable impurity.
Preferably, also Nb:0.030 ~ 0.060% is comprised in component of the present invention.
The proportioning reason of above-mentioned each component is as follows:
Carbon: it is generally acknowledged, carbon makes toughness deteriorate.But carbon is the important element ensureing bearing steel intensity and wear resisting property, in shock-resistant bearing steel, ensure the carbon content that certain intensity rank must be certain.The carbon content controlling 0.58 ~ 0.68% can ensure.
Silicon: silicon energy Some substitute chromium, nickel element effect improve intensity, at smelting process still good reductive agent and reductor.Meanwhile, in steel, silicon can reduce the concentration gradient of carbon, promotes carbon diffusion under austenitic state, and it can suppress the precipitation of carbide, can improve toughness.In steel of the present invention, silicon controls to coordinate with other elements 1.25 ~ 1.55% to meet obdurability requirement.
Manganese: manganese can partly replace chromium to keep intensity, and manganese is the principal element that can significantly improve hardening capacity.But manganese has the shortcoming promoting austenitizing grain growth in steel, should be controlled the content of manganese.Adding Fe content in invention steel is 0.28 ~ 0.58%.
Molybdenum: molybdenum energy crystal grain thinning, improves hardening capacity, can ensure that steel have certain intensity rank, can reduce temper brittleness in addition, avoid steel to occur brittle rupture in the Working environment of complexity.The effect highly significant of appropriate molybdenum content in steel, not only can improve the hardening capacity in part heart portion, obviously suppresses the formation of non-martensite, can also improve piece surface hardness.In steel of the present invention, control Mo:0.58 ~ 0.68%.
Vanadium, niobium: typical crystal grain thinning element, the vanadium of 0.15 ~ 0.25%, selects the niobium adding 0.030-0.060% can improve the grain-size of steel, obtains good toughness.But too much vanadium or niobium often cause corresponding carbide to assemble, and impact the reduction of toughness.
Aluminium: aluminium is reductor and crystal grain thinning element, but test shows, and too much Al often forms Al2O3 class non-metallic inclusion, and the non-metallic inclusion of these difficult distortion often becomes repeated stress failure source, affects the shock resistance of bearing.What control finished product 0.010 ~ 0.040% in this steel grade is significant technical characteristic.
Phosphorus, sulphur, copper: the impurity element in steel, significantly can reduce plasticity and the toughness of steel.Particularly phosphorus harm is maximum, copper :≤0.25%, sulphur :≤0.015%, phosphorus :≤0.010%.
Simultaneously lead, antimony, bismuth, titanium, nitrogen, oxygen are the impurity elements in steel, should reduce its content as far as possible in technical qualification permission situation.
A manufacture method for shock-resistant bearing steel as described in the present invention, it comprises the steps:
After batching, carry out that molten steel just refines successively, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, before cast, first under the vacuum condition not higher than the pressure of 133Pa, process at least 15min, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled;
First for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain finished product bar.
The present invention compared with prior art, has outstanding feature and remarkable advantage:
1, invention steel is not containing chromium nickel expensive alloying elements, and cost is low, and manufacturing process is brief.
2, invention steel is after being rolled into bar or wire rod, makes bearing goods and can be applicable to the harsh environments such as engineering machinery, mining, excavation, can bear too much shock load, high life.
3, invention steel is after being rolled into bar or wire rod, original grain degree 7 ~ 11 grades.
4, invention Steel Clearness is high: inclusion behavior low (detect can meet according to GB/T10561: A≤2, B≤2, C≤1, D≤1); Gas content (oxygen≤10ppm, hydrogen≤1.0ppm).
Embodiment
Below in conjunction with embodiment, the invention will be further described, but protection scope of the present invention is not only confined to embodiment.
Embodiment 1:
One, by the formula in table 2, control C is 0.58%, Si is 1.55%, Mn is 0.33%, Mo is 0.59%, Cu is 0.20%, P is 0.008%, S is 0.010%, Nb is 0.04%, Al is 0.011%, V is 0.18%, O is 0.0010%, surplus is iron and impurity, after batching, carry out molten steel successively just to refine, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, first under the vacuum condition not higher than the pressure of 133Pa, at least 15min is processed before cast, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled,
Two, first for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain product bar.
Embodiment 2:
One, by the formula in table 2, control C is 0.67%, Si is 1.28%, Mn is 0.58%, Mo is 0.66%, Cu is 0.15%, P is 0.004%, S is 0.008%, Al is 0.026%, V is 0.25%, O is 0.0009%, surplus is iron and impurity, after batching, carry out molten steel successively just to refine, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, first under the vacuum condition not higher than the pressure of 133Pa, at least 15min is processed before cast, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled,
Two, first for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain product bar.
Embodiment 3:
One, by the formula in table 2, control C is 0.61%, Si is 1.54%, Mn is 0.28%, Mo is 0.68%, Cu is 0.10%, P is 0.007%, S is 0.015%, Nb is 0.03%, Al is 0.010%, V is 0.23%, O is 0.0007%, surplus is iron and impurity, after batching, carry out molten steel successively just to refine, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, first under the vacuum condition not higher than the pressure of 133Pa, at least 15min is processed before cast, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled,
Two, first for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain product bar.
Embodiment 4:
One, by the formula in table 2, control C is 0.60%, Si is 1.50%, Mn is 0.38%, Mo is 0.58%, Cu is 0.12%, P is 0.010%, S is 0.013%, Al is 0.040%, V is 0.15%, O is 0.0004%, surplus is iron and impurity, after batching, carry out molten steel successively just to refine, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, first under the vacuum condition not higher than the pressure of 133Pa, at least 15min is processed before cast, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled,
Two, first for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain product bar.
Embodiment 5:
One, by the formula in table 2, control C is 0.67%, Si is 1.48%, Mn is 0.47%, Mo is 0.62%, Cu is 0.09%, P is 0.009%, S is 0.004%, Nb is 0.06%, Al is 0.038%, V is 0.25%, O is 0.0006%, surplus is iron and impurity, after batching, carry out molten steel successively just to refine, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, first under the vacuum condition not higher than the pressure of 133Pa, at least 15min is processed before cast, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled,
Two, first for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain product bar.
Embodiment 6:
One, by the formula in table 2, control C is 0.59%, Si is 1.36%, Mn is 0.57%, Mo is 0.64%, Cu is 0.12%, P is 0.005%, S is 0.003%, Al is 0.029%, V is 0.24%, O is 0.0007%, surplus is iron and impurity, after batching, carry out molten steel successively just to refine, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, first under the vacuum condition not higher than the pressure of 133Pa, at least 15min is processed before cast, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled,
Two, first for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain product bar.
Embodiment 7:
One, by the formula in table 2, control C is 0.68%, Si is 1.25%, Mn is 0.39%, Mo is 0.67%, Cu is 0.08%, P is 0.008%, S is 0.002%, Al is 0.037%, V is 0.19%, O is 0.0009%, surplus is iron and impurity, after batching, carry out molten steel successively just to refine, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, first under the vacuum condition not higher than the pressure of 133Pa, at least 15min is processed before cast, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled,
Two, first for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain product bar.
The chemical composition of table 2 embodiment rod iron, wt%
The rod iron each embodiment obtained quenches at 880 DEG C ~ 910 DEG C, then carries out oil cooling or water-cooled; Tempering within the scope of 460 DEG C again ~ 580 DEG C, obtains the mechanical property shown in table 3.
Table 3 embodiment rod iron performance
Select in embodiment to add Nb, energy refining grain size; Hardening capacity can be improved under the effect of Mo element; The effect improving microstructure segregation can be played for large gauge rod iron.Therefore, can select to add Nb when required bearing size is larger and improve grain-size, coordinate can improve hardening capacity with other elements, improve core structure state.
Above embodiment not only represents above 7 compositions combination, any combination in scope all can overcome the defect that the impact property of high carbon steel is not good, carburizing bearing steel expensive alloying elements content is many (carburization process is complicated, cost is high), can reach the integrated performance index of more than 80J under 1380Mpa level intensity.And bearing machining process is simple, factory in work-ing life (for mine bearing, invention steel is 2.5 times of conventional high-carbon fatigue life of bearing)
To sum up, the present invention compared with prior art, has outstanding feature and remarkable advantage:
1, invention steel is not containing chromium nickel expensive alloying elements, and cost is low, and manufacturing process is brief.
2, invention steel is after being rolled into bar or wire rod, makes bearing goods and can be applicable to the harsh environments such as engineering machinery, mining, excavation, can bear too much shock load, high life.
3, invention steel is after being rolled into bar or wire rod, original grain degree 7 ~ 11 grades.
4, invention Steel Clearness is high: inclusion behavior low (detect can meet according to GB/T10561: A≤2, B≤2, C≤1, D≤1); Gas content (oxygen≤10ppm, hydrogen≤1.0ppm).
Last it is noted that above embodiment only in order to illustrate the present invention and and unrestricted technical scheme described in the invention; Therefore, although this specification sheets with reference to each above-mentioned embodiment to present invention has been detailed description, those of ordinary skill in the art should be appreciated that and still can modify to the present invention or equivalent to replace; And all do not depart from technical scheme and the improvement thereof of the spirit and scope of the present invention, it all should be encompassed in right of the present invention.
Claims (3)
1. a shock-resistant bearing steel for Chrome-free nickel, is characterized in that, comprises the following component of percentage:
C:0.58 ~ 0.68%; Si:1.25 ~ 1.55%; Mn:0.28 ~ 0.58%; Mo:0.58 ~ 0.68%; V:0.15 ~ 0.25%; Nb:0.015 ~ 0.08%; Al:0.010 ~ 0.040%; P :≤0.015%; Cu :≤0.25%; O :≤0.0010%; S :≤0.015%; Surplus is Fe and inevitable impurity.
2. shock-resistant bearing steel as claimed in claim 1, is characterized in that, also comprise Nb:0.030 ~ 0.060%.
3. a manufacture method for shock-resistant bearing steel as claimed in claim 1 or 2, is characterized in that, comprise the steps:
After batching, carry out that molten steel just refines successively, refining, continuous casting, obtain steel ingot, the constituent content wherein controlled in the molten steel after just refining reaches P≤0.035wt%, C >=0.05wt%, liquid steel temperature after first refining is not less than 1620 DEG C, lime or synthetic slag is added in molten steel before refining first after just refining, deoxidation during refining to add Al to Al content be 0.02 ~ 0.05wt%, stirring is not less than 5min, before cast, first under the vacuum condition not higher than the pressure of 133Pa, process at least 15min, after pouring into rectangular bloom during cast, direct-on-line heat is sent and is rolled;
First for described rectangular bloom rolling-cogging is become billet, again described billet hot-work is rolled into bar, wherein, when rectangular bloom rolling-cogging being become billet, the charging temperature of first control rectangle base is 600 ~ 900 DEG C, and be incubated 20 ~ 40min at such a temperature, 1250 ~ 1290 DEG C are warming up to again at 120 ~ 200min, be rolled after insulation 60 ~ 180min, when described billet is thermally processed into bar, controlling Heating temperature is 1060 ~ 1260 DEG C, heat-up time 80 ~ 120min, during to the male and female face temperature difference≤40 DEG C of billet, be rolled, controlling finishing temperature is 760 ~ 900 DEG C, obtain product bar.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410554526.4A CN105568158B (en) | 2014-10-17 | 2014-10-17 | Nickel-chromium-free impact-resistant bearing steel and producing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410554526.4A CN105568158B (en) | 2014-10-17 | 2014-10-17 | Nickel-chromium-free impact-resistant bearing steel and producing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105568158A true CN105568158A (en) | 2016-05-11 |
| CN105568158B CN105568158B (en) | 2017-05-24 |
Family
ID=55878770
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201410554526.4A Active CN105568158B (en) | 2014-10-17 | 2014-10-17 | Nickel-chromium-free impact-resistant bearing steel and producing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105568158B (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106591697A (en) * | 2016-11-09 | 2017-04-26 | 安徽千禧精密轴承制造有限公司 | Bearing alloy steel and heat treatment method thereof |
| CN106636922A (en) * | 2016-12-28 | 2017-05-10 | 内蒙古包钢钢联股份有限公司 | Steel for high-strength microalloying wear-resistant ball material and production method of steel |
| CN107761003A (en) * | 2017-09-20 | 2018-03-06 | 上海汽车粉末冶金有限公司 | The powder metallurgy sintered method of bearing cap |
| CN109321837A (en) * | 2017-08-01 | 2019-02-12 | 宝钢特钢长材有限公司 | Carburizing steel and preparation method thereof for atomizer valve body |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03258445A (en) * | 1990-03-09 | 1991-11-18 | Kawasaki Steel Corp | Production of raw material for bearing having long service life and high strength |
| CN101082101A (en) * | 2006-05-29 | 2007-12-05 | 宝山钢铁股份有限公司 | Chromic-nickel-free high-strength high ductility structural steel and manufacturing method thereof |
| CN101186995A (en) * | 2007-10-15 | 2008-05-28 | 莱芜钢铁集团有限公司 | Medium carbon bearing steel and its preparation method |
-
2014
- 2014-10-17 CN CN201410554526.4A patent/CN105568158B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03258445A (en) * | 1990-03-09 | 1991-11-18 | Kawasaki Steel Corp | Production of raw material for bearing having long service life and high strength |
| CN101082101A (en) * | 2006-05-29 | 2007-12-05 | 宝山钢铁股份有限公司 | Chromic-nickel-free high-strength high ductility structural steel and manufacturing method thereof |
| CN101186995A (en) * | 2007-10-15 | 2008-05-28 | 莱芜钢铁集团有限公司 | Medium carbon bearing steel and its preparation method |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106591697A (en) * | 2016-11-09 | 2017-04-26 | 安徽千禧精密轴承制造有限公司 | Bearing alloy steel and heat treatment method thereof |
| CN106636922A (en) * | 2016-12-28 | 2017-05-10 | 内蒙古包钢钢联股份有限公司 | Steel for high-strength microalloying wear-resistant ball material and production method of steel |
| CN109321837A (en) * | 2017-08-01 | 2019-02-12 | 宝钢特钢长材有限公司 | Carburizing steel and preparation method thereof for atomizer valve body |
| CN107761003A (en) * | 2017-09-20 | 2018-03-06 | 上海汽车粉末冶金有限公司 | The powder metallurgy sintered method of bearing cap |
Also Published As
| Publication number | Publication date |
|---|---|
| CN105568158B (en) | 2017-05-24 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105525226B (en) | A kind of martensitic stain less steel wire rod and its manufacture method | |
| CN106661705B (en) | carburized alloy steel and preparation method and application thereof | |
| CN103266287B (en) | Carbon ferritic in one-pearlite type non-hardened and tempered steel and manufacture method thereof | |
| CN104328353B (en) | A kind of rare-earth type 0Cr17Ni4Cu4Nb martensitic precipitations and preparation method thereof | |
| WO2021098208A1 (en) | 690 mpa-grade medium manganese steel medium thick steel with high strength and low yield ratio and manufacturing method therefor | |
| CN111394639B (en) | Manufacturing method of high-wear-resistance gear steel | |
| CN108950432B (en) | Manufacturing method of high-strength and high-toughness low-alloy wear-resistant steel | |
| CN103397272B (en) | There is wear-resisting steel plate of low crack-sensitivity exponential sum high strength and preparation method thereof | |
| CN109023119A (en) | A kind of abrasion-resistant stee and its manufacturing method with excellent plasticity and toughness | |
| CN107881417B (en) | A kind of low yield strength ratio martensite-ferrite-austenite multi-phase wear-resistant steel plate and its manufacturing method | |
| CN105779867B (en) | A kind of Cutting free wear-resisting steel plate and preparation method thereof | |
| CN107130172B (en) | 400HBW grades of Brinell hardness whole constrictive type high tenacity easily weld special thick wear-resisting steel plate and its manufacturing method | |
| CN103114245A (en) | Wear-resistant lining board and preparation method thereof | |
| CN105112782A (en) | Low-temperature ferrite LT-FH40 steel plate applied to hot-rolled ships and production method thereof | |
| CN105543703A (en) | Multi-microalloyed antifatigue carburized gear steel and manufacturing method thereof | |
| CN102424936A (en) | Low temperature impact resistance allay structure steel and manufacture method thereof | |
| JP2024515134A (en) | Steel for high temperature carburizing gear shaft and manufacturing method of the steel | |
| CN109695001B (en) | Novel rare earth hot work die steel and preparation method thereof | |
| CN104451436A (en) | Bainite-martensite-austenite multi-phase wear-resistant steel plate and manufacturing method thereof | |
| CN105568158B (en) | Nickel-chromium-free impact-resistant bearing steel and producing method thereof | |
| CN109778068A (en) | The abrasion resistant cast steel and preparation method thereof of niobium vanadium complex intensifying | |
| CN111850399A (en) | Corrosion-resistant plastic die steel with good wear resistance and preparation method thereof | |
| WO2019029533A1 (en) | Cast steel, preparation method for cast steel and use of cast steel | |
| WO2021208181A1 (en) | Low-temperature, high-toughness, high-temperature, high-intensity and high-hardenability hot mold steel and preparation method therefor | |
| CN109182673B (en) | Low-cost high-strength wear-resistant stainless steel and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20210428 Address after: 200940 No. 1269, Fisheries Road, Shanghai, Baoshan District Patentee after: BAOSTEEL SPECIAL STEEL LONG PRODUCTS Co.,Ltd. Address before: 200940 No. 1269, Fisheries Road, Shanghai, Baoshan District Patentee before: BAOSTEEL SPECIAL STEEL Co.,Ltd. |