CN102925812B - Hot rolling diaphragm spring steel for automobile and production method of hot rolling diaphragm spring - Google Patents
Hot rolling diaphragm spring steel for automobile and production method of hot rolling diaphragm spring Download PDFInfo
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Abstract
The invention discloses hot rolling diaphragm spring steel for an automobile and a production method of the hot rolling diaphragm spring steel. The hot rolling diaphragm spring steel comprises the following components by weight percentage: 0.40-0.60% of C, 0.15-0.35% of Si, 0.70-1.20% of Mn, less than or equal to 0.015% of P, less than or equal to 0.008% of S, less than or equal to 0.050% of Alt, 0.10-0.30% of Mo, 0.70-1.20% of Cr, 0.10-0.50% of V and less than or equal to 0.005% N. The production method comprises the processing steps of desulfurating, smelting, refining, conducting vacuum treatment, continuously casting to form a blank, conducting segmented thermal insulation according to temperature, heating the casting blank, rolling, coiling, slowly cooling, shearing a steel band, annealing, molding, quenching, tempering and waiting for application. According to the hot rolling diaphragm spring steel and the production method, the production cost is low; a load of a rolling mill can be reduced; the comprehensive mechanical property is excellent; a steel coil is heated uniformly in the annealing process; the uniformity of a metallurgical structure is ensured; a tempered sorbite structure is obtained by heat treatment of the quenching and the tempering; the steel is separated out by compound precipitation of microalloys, such as Cr, Mo and V in the steel; and high strength and good wear-proof property of the steel are ensured.
Description
Technical field
The present invention relates to spring steel, be specifically used for steel and production method thereof for automobile hot rolling diaphragm spring.
Background technology
Before the present invention proposes, the similar technical products that relates to alloy structure steel making field is more, but less for automobile diaphragm spring steel aspect.Through retrieval, Chinese patent name is called " high tough high-hardenability spring tube material ", the document that number of patent application is CN200510018800.7, its composition and mass percent C:0.48 ~ 0.55%, Si:0.17 ~ 0.37%, Mn:0.70 ~ 1.00%, Cr:0.8 ~ 1.1%, B:0.001 ~ 0.004%, Ni≤0.35%, Cu≤0.25%, P≤0.03%, S≤0.03%, all the other are Fe.It is owing to having added B, and P, S content level of control are not high, though have certain economy, post-production poor-performing, can not meet the requirement of steel for automobile diaphragm spring.And this steel is when quenching, intensity can obtain larger raising, and crack sensitivity is also higher, easily at subsequent disposal Fracture, has increased heat treated difficulty.
Japanese documentation JP19930037451 " a kind of clutch diaphragm steel " and JP19890059067 " a kind of Automobile Clutch Plate Spring steel ", these two kinds of steel in chemical composition owing to all having added more C, Si, Mn and a certain amount of Mo, cause that not only production cost is high, and production unit is had relatively high expectations, and post-production difficulty is also larger.
In automobile clutch assembly, diaphragm spring has a significant impact the performance and used life in automobile clutch assembly.At present, limit by metallurgical equipment ability level and post-production level, domestic large-scale cargo truck and high-grade car diaphragm spring major part also adopt imported materials and items.Domestic automobile diaphragm spring steel adopts the operational path of " hot rolling → annealing → shearing → thermal treatment " more, reduce the intensity of steel by anneal after, process again and thermal treatment, but product performance homogeneity is bad, but its product comprehensive mechanical property and do not reach the requirement of steel for high-grade automobile clutch work-ing life.In order further to improve automobile diaphragm spring elastic force, cold and hot working performance, work-ing life, reduce plate property fluctuation, realize the production domesticization of this steel grade, finish the history of large-scale cargo truck diaphragm spring dependence on import, project verification research and development automobile diaphragm spring steel.In order further improving automobile diaphragm spring elastic force, cold and hot working performance, work-ing life, and to reduce plate property fluctuation, to propose the present invention for this reason.
Summary of the invention
The object of this invention is to provide a kind of automobile hot rolling diaphragm spring steel and manufacture method thereof, can overcome the rear coil of strip tissue of annealing and mechanical property lack of homogeneity, surface quality is bad and cold-forming property not enough, obtains hot rolling diaphragm spring steel and the production method thereof for automobile of high strength, high elastic limit, high yield strength and highly anti-fatigue limiting performance.
Realize the measure of above-mentioned purpose:
Hot rolling diaphragm spring steel for a kind of automobile, its component and weight percent content are: C:0.40 ~ 0.60%, Si:0.15 ~ 0.35%, Mn:0.70 ~ 1.20%, P≤0.015%, S≤0.008%, Alt≤0.050%, Mo:0.10 ~ 0.30%, Cr:0.70 ~ 1.20%, V:0.10 ~ 0.50%, N≤0.005%, surplus is Fe and is inevitably mingled with.
Produce a kind of method of hot rolling diaphragm spring steel for automobile, its step:
1) carry out desulfurizing iron;
2) carry out converter smelting;
3) in LF stove, carry out refining;
4) in RH vacuum oven, process, control vacuum processing time and be no less than 18 minutes;
5) continuous casting becomes base: in casting process, induction stirring all the time;
6) in stay-warm case, strand is carried out to temperature section insulation: when holding temperature is greater than 600 ℃, speed of cooling is not higher than 50 ℃/h; When holding temperature is within the scope of 200～600 ℃, speed of cooling scope is at 150 ~ 250 ℃/h; When holding temperature is during lower than 200 ℃, open stay-warm case and carry out air cooling;
7) to strand heating, heating and temperature control is 1200～1300 ℃, and it is 8～14 minutes/centimetre that heating rate is controlled;
8) carry out segmentation rolling: control roughing start rolling temperature at 1050～1150 ℃, control finish rolling finishing temperature at 850～920 ℃;
9) batch, control coiling temperature at 680～780 ℃;
10) carry out slow cooling, speed of cooling is controlled to be no more than under 40 ℃/h and is cooled to and is no more than 200 ℃;
11) shear steel band;
12) anneal, annealing temperature is 700～780 ℃, annealing time: (6+0.5Q) * 60 minutes/ton of steel,
In formula, Q represents the steel plate gross weight packing into, and unit is ton;
13) machine-shaping;
14) according to profiled member different sites, quench: control quenching temperature at 820～880 ℃, profiled member inner ring adopts oil or quenching medium to carry out, and it is 120～150 ℃/sec that speed of cooling is controlled at; Profiled member outer ring adopts water to carry out, and speed of cooling is controlled at 200～300 ℃/sec;
15) carry out the tempering of two stages: the first stage, tempering temperature is in the time of 450～600 ℃, and tempering time is for take additional 30 minutes of the thickness of slab that millimeter is unit; Subordinate phase, tempering temperature is in the time of 250～400 ℃, and tempering time is for take additional 50 minutes of the thickness of slab that millimeter is unit;
16) check stand-by.
The function and mechanism of each element and main technologic parameters in the present invention:
Element aspect:
C: it is to improve the most effective element of steel strength, along with the increase of C content, Fe in steel
3c increases, and hardenability also increases, and the tensile strength of steel and yield strength improve.But along with C content increases, the unit elongation of steel, impelling strength and cold-forming property decline.Therefore, in conjunction with existing steel grade of the same type, the C content of steel of the present invention should be controlled in 0.45% ~ 0.60%, guarantees that steel plate has high strength, high hardenability, high-wearing feature etc.
Si: the avidity of itself and carbon is very weak, carburet not in steel, but can dissolve in ferrite, and produce solution strengthening effect, ferritic intensity and hardness are improved, but plasticity and toughness decline to some extent.Visible, Si has certain help to intensity, but content can not be too high, in order to avoid reduce the plasticity and toughness of steel.The Si content of steel of the present invention is controlled in 0.15% ~ 0.35% scope and can meets the demands.
Mn: the avidity of itself and carbon is stronger, it is the effective element that expands austenite phase region, crystal grain thinning, spheroidized carbide and assurance over-all properties and improve hardening capacity, and it does not worsen the deformability of steel, 1.00% Mn approximately can be tensile strength contribution 100MPa.Consider the strength range of steel of the present invention, therefore Mn is controlled to 0.70% ~ 1.20%.
Al: it is the main deoxidant element in steel, maxima solubility in austenite is about 0.6%, and it only faintly increases hardening capacity after dissolving in austenite.But when Al too high levels, easily cause being mingled with and increasing in steel, unfavorable to the toughness of steel, therefore Alt content in steel is controlled in 0.050%.
Mo: in the higher steel of carbon content, Mo is mainly in order to improve the hardening capacity of steel, improves the secondary hardening ability of steel, and can improve the obdurability of steel, suppresses temper brittleness.Meanwhile, can also improve cementite stability and hardness in steel, to improving elasticity, wear resistance and the ultimate strength of steel, play an important role, but content can increase decarburizing tendency when more.Therefore, Mo content is controlled to 0.10% ~ 0.30%.
Cr: the effect that it can improve the hardening capacity of steel and have secondary hardening is effectively to improve the particularly element of hot strength of steel strength, can also improve cementite stability and hardness in steel, plays an important role to improving elasticity, wear resistance and the ultimate strength of steel.Can improve steel anti-hydrogen embrittlement ability and temper resistance.Meanwhile, Cr can also improve coil of strip surface quality, is convenient to cold rolling processing of later stage.Consider above-mentioned analytical results, and the contents level of Mo in steel, Cr content is controlled to 0.70% ~ 1.20%.
V: it is one of carbide forming element effectively improving armor plate strength, the effect in steel is only second to Nb, Ti.After adding V in steel, will form VC, improve fusing point, hardness and the wear resistance of cementite.But the content of V can not be too high, there is disperse state and distribute in V, produce secondary hardening when average tempering, is unfavorable for the inspection during manufacture of steel.Therefore, design V content time V is controlled to 0.10% ~ 0.50%.
Although impurity element P, S in steel content in steel is very few, larger to cold and hot working performance impact, strictly controls its content and can obviously reduce the phenomenon of rupture in the course of processing.The brittle failure position occurring at the coils of hot-rolled steel often segregation of P goes out, and also easily causes that layering is torn etc. containing the segregation of the inclusion of S, and the processing characteristics of steel is had to considerable influence.Therefore, for this steel, P should be controlled in 0.015%, S is controlled in 0.008%.
In addition, this steel is had relatively high expectations at continuous casting and annealing process, should reduce gas content in steel as far as possible, reduces the segregation of steel.Meanwhile, in order to reduce the influence of time effect of steel, the content of N is controlled in 0.005%.
Process aspect:
Process for making
The present invention limits the vacuum processing time in process for making to be no less than 18min, its objective is by increasing vacuum processing time and can reduce preferably impurity in steel, gas content.
Why the present invention will control vacuum processing time for being not less than 18min, can reduce preferably impurity in steel, gas content.
While being defined in continuous casting in addition, must carry out induction stirring, be because Carbon Content Of Steel, alloying element content are higher, to reduce element segregation.
Also require strand to take different slow cooling speed according to temperature section difference, object is avoided high-temperature embrittlement region exactly, prevents disconnected base, reduces strand crackle, improves slab quality.
Steel rolling process
Because hardness of steel of the present invention is high, be rolled and batch by high-strength steel technique.Before rolling, slab heating temperature is 1200 ~ 1300 ℃, and heating rate is 8 ~ 14min/cm, guarantees the even steel of strand temperature.When roughing and finish rolling, design temperature is higher than conventional low alloy steel, reduces milling equipment load.Meanwhile, consider the critical point temperature of steel, avoid occurring mixed crystal phenomenon.Therefore, the roughing start rolling temperature of steel is 1050 ~ 1150 ℃, and finish rolling finishing temperature is 850 ~ 920 ℃, and coiling temperature is 680 ~ 780 ℃.
Processing, thermal treatment process
Machining process route of the present invention: shear → annealing (carbon atmosphere) → processing → quenching → tempering → check delivery.Why before annealing, shear, it is the substance for less annealing coil, thermal treatment is heated evenly, avoid coil of strip top layer and heart portion be heated and speed of cooling inhomogeneous and cause the inhomogeneous of annealed structure, processing below of impact and the performance after thermal treatment.When annealing, in annealing furnace, add carbon dust, can effectively avoid coil of strip superficial decarbonization phenomenon, Decarburized layer is dropped in 20 μ m, reduce decarburization position coil of strip performance ununiformity.Annealing temperature is controlled to 700 ~ 780 ℃, is in order significantly to reduce coil of strip intensity, and makes the nodularization of organizing of steel, to be easy to shearing.
Quenching temperature is controlled to 820 ~ 880 ℃, and adopts different cooling systems according to different sites, object is exactly for according to the requirement of parts different sites use properties, accurately controls tissue and the mechanical property of different sites, makes parts meet service requirements completely.
Adopt the tempering of two stages, first stage tempering temperature is controlled at 450 ~ 600, and adopt the different mode of the different tempering times of temperature section and temperature section, in order to allow steel complete austenitizing, after quenching+tempering, obtain stable tempered martensite, obtain high strength, snappiness, high yield strength and the highly anti-fatigue limit.Subordinate phase, tempering temperature is controlled at 250～400 ℃, is in order to reduce the internal stress of parts, prevents from use deforming and rupturing, and guarantees to use safety.
The present invention compared with prior art, not only has high strength, snappiness, high yield strength and the highly anti-fatigue limit, can be used for manufacturing various types of vehicles clutch assembly, particularly large-scale cargo truck and high-grade car.And carbon in adopting on Composition Design, and add a certain amount of Mn, Cr, Mo, V, strict P, the S content controlled, reduces production cost simultaneously, utilizes rational rolling and batches system, has reduced mill load and infringement; In post-production, designed the operational path of hot rolled coil → cutting → annealing → processing → quenching → tempering, by reducing annealing coil substance, being heated evenly property of coil of strip while having improved annealing, guaranteed homogeneity of structure, and by quenching+tempering thermal treatment, obtain tempered sorbite and organize, utilize the composite precipitation of the microalloies such as Cr in steel, Mo, V to separate out and guaranteed that steel obtain enough intensity and wear resistance.
Accompanying drawing explanation
Fig. 1 is As rolled metallographic structure figure of the present invention
Fig. 2 is As rolled cross section metallographic structure figure of the present invention.
Embodiment
Below the present invention is described in detail:
Table 1 is the value list of various embodiments of the present invention and comparative example;
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example;
Table 3 is various embodiments of the present invention and comparative example mechanical properties test the results list.
Various embodiments of the present invention are produced according to following steps:
Its step:
1) carry out desulfurizing iron;
2) carry out converter smelting;
3) in LF stove, carry out refining;
4) in RH vacuum oven, process, control vacuum processing time and be no less than 18 minutes;
5) continuous casting becomes base: in casting process, induction stirring all the time;
6) in stay-warm case, strand is carried out to temperature section insulation: when holding temperature is greater than 600 ℃, speed of cooling is not higher than 50 ℃/h; When holding temperature is within the scope of 200～600 ℃, speed of cooling scope is at 150 ~ 250 ℃/h; When holding temperature is during lower than 200 ℃, open stay-warm case and carry out air cooling;
7) to strand heating, heating and temperature control is 1200～1300 ℃, and it is 8～14 minutes/centimetre that heating rate is controlled;
8) carry out segmentation rolling: control roughing start rolling temperature at 1050～1150 ℃, control finish rolling finishing temperature at 850～920 ℃;
9) batch, control coiling temperature at 680～780 ℃;
10) carry out slow cooling, speed of cooling is controlled to be no more than under 40 ℃/h and is cooled to and is no more than 200 ℃;
11) shear steel band;
12) anneal, annealing temperature is 700～780 ℃, annealing time: (6+0.5Q) * 60 minutes/ton of steel,
In formula, Q represents the steel plate gross weight packing into, and unit is ton;
13) machine-shaping;
14) according to profiled member different sites, quench: control quenching temperature at 820～880 ℃, profiled member inner ring adopts oil or quenching medium to carry out, and it is 120～150 ℃/sec that speed of cooling is controlled at; Profiled member outer ring adopts water to carry out, and speed of cooling is controlled at 200～300 ℃/sec;
15) carry out the tempering of two stages: the first stage, tempering temperature is in the time of 450～600 ℃, and tempering time is for take additional 30 minutes of the thickness of slab that millimeter is unit; Subordinate phase, tempering temperature is in the time of 250～400 ℃, and tempering time is for take additional 50 minutes of the thickness of slab that millimeter is unit;
16) check stand-by.
Table 1 various embodiments of the present invention and contrast steel grade chemical composition (wt%)
Table 2 various embodiments of the present invention and the main processes () that contrasts steel grade
Table 2 various embodiments of the present invention and the heat treatment process (two) that contrasts steel grade
Table 3 various embodiments of the present invention and the mechanical properties test the results list that contrasts steel grade
As can be seen from Table 3, steel grade of the present invention has good cold and hot working performance, and has high strength (R
m: 1500 ~ 2000MPa), snappiness, high yield strength and the highly anti-fatigue limit, can be used for manufacturing various types of vehicles clutch assembly, particularly large-scale cargo truck and high-grade car.
Above-described embodiment only exemplifies for the best, and is not the restriction to embodiments of the present invention.
Claims (1)
1. a production method for hot rolling diaphragm spring steel for automobile, its step:
1) carry out desulfurizing iron;
2) carry out converter smelting;
3) in LF stove, carry out refining;
4) in RH vacuum oven, process, control vacuum processing time and be no less than 18 minutes;
5) continuous casting becomes base: in casting process, induction stirring all the time; Strand component and weight percent content are: C:0.40 ~ 0.60%, Si:0.15 ~ 0.35%, Mn:0.70 ~ 1.20%, P≤0.015%, S≤0.008%, Alt≤0.050%, Mo:0.10 ~ 0.30%, Cr:0.70 ~ 1.20%, V:0.10 ~ 0.50%, N≤0.005%, surplus is Fe and is inevitably mingled with;
6) in stay-warm case, strand is carried out to temperature section insulation: when holding temperature is greater than 600 ℃, speed of cooling is not higher than 50 ℃/h; When holding temperature is within the scope of 200～600 ℃, speed of cooling scope is at 150 ~ 250 ℃/h; When holding temperature is during lower than 200 ℃, open stay-warm case and carry out air cooling;
7) to strand heating, heating and temperature control is 1200～1300 ℃, and it is 8～14 minutes/centimetre that heating rate is controlled;
8) carry out segmentation rolling: control roughing start rolling temperature at 1050～1150 ℃, control finish rolling finishing temperature at 850～920 ℃;
9) batch, control coiling temperature at 680～780 ℃;
10) carry out slow cooling, speed of cooling is controlled to be no more than under 40 ℃/h and is cooled to and is no more than 200 ℃;
11) shear steel band;
12) anneal, annealing temperature is 700～780 ℃, annealing time: (6+0.5Q) * 60 minutes/ton of steel,
In formula, Q represents the steel plate gross weight packing into, and unit is ton;
13) machine-shaping;
14) according to profiled member different sites, quench: control quenching temperature at 820～880 ℃, profiled member inner ring adopts oil or quenching medium to carry out, and it is 120～150 ℃/sec that speed of cooling is controlled at; Profiled member outer ring adopts water to carry out, and speed of cooling is controlled at 200～300 ℃/sec;
15) carry out the tempering of two stages: the first stage, tempering temperature is in the time of 450～600 ℃, and tempering time is for take additional 30 minutes of the thickness of slab that millimeter is unit; Subordinate phase, tempering temperature is in the time of 250～400 ℃, and tempering time is for take additional 50 minutes of the thickness of slab that millimeter is unit;
16) check stand-by.
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| CN103898412B (en) * | 2014-03-14 | 2016-08-17 | 山西太钢不锈钢股份有限公司 | A kind of Automobile Clutch Plate Spring hot-strip and manufacture method thereof |
| CN104313472B (en) * | 2014-10-31 | 2016-06-22 | 武汉钢铁(集团)公司 | A kind of high-carbon Hot Rolling Automobile diaphragm spring steel and production method thereof |
| CN104668907A (en) * | 2015-01-30 | 2015-06-03 | 南通弘峰机电有限公司 | Machining process for large spring pieces |
| CN105316591A (en) * | 2015-03-14 | 2016-02-10 | 洛阳辰祥机械科技有限公司 | Preparation method for high-performance spring |
| CN106311789B (en) * | 2015-06-19 | 2018-05-11 | 常熟宝升精冲材料有限公司 | A kind of 51CrV4 spring steel fine processing method |
| CN105039657A (en) * | 2015-06-29 | 2015-11-11 | 江苏金基特钢有限公司 | Method for improving wear-resisting performance of carbon steel |
| CN105886930B (en) * | 2016-04-26 | 2017-12-26 | 宝山钢铁股份有限公司 | A kind of high-strength corrosion-resistant spring steel and its manufacture method |
| CN106222553B (en) * | 2016-08-19 | 2018-11-02 | 武汉钢铁有限公司 | A kind of manufacturing method for the cold rolling medium high carbon alloy structural steel that thickness is 0.1-0.4mm |
| CN106222572B (en) * | 2016-08-19 | 2018-07-13 | 武汉钢铁有限公司 | A kind of manufacturing method for the cold rolling medium high carbon alloy structural steel that thickness is 0.4-0.8mm |
| CN107177782B (en) * | 2017-06-30 | 2019-05-24 | 武汉钢铁有限公司 | A kind of corrosion-resistant spring steel and preparation method thereof |
| CN107385330A (en) * | 2017-07-05 | 2017-11-24 | 南京钢铁股份有限公司 | A kind of production technology of car belt wind spring SK5 spring steel |
| CN109881117B (en) * | 2019-03-20 | 2021-07-20 | 包头钢铁（集团）有限责任公司 | Hot-rolled coil for high-carbon spring and production method thereof |
| CN112063816B (en) * | 2019-06-10 | 2021-11-19 | 育材堂（苏州）材料科技有限公司 | Heat treatment method of high-strength steel and product obtained thereby |
| CN110295271A (en) * | 2019-06-19 | 2019-10-01 | 东莞市卓蓝自动化设备有限公司 | A kind of flexbile gear heat treatment process |
| CN110699528B (en) * | 2019-11-12 | 2021-07-23 | 山东汽车弹簧厂淄博有限公司 | Preparation method of spring steel plate |
| CN111304413A (en) * | 2020-03-13 | 2020-06-19 | 大冶特殊钢有限公司 | Spring flat steel and preparation method thereof |
| CN115786799A (en) * | 2022-11-03 | 2023-03-14 | 山东钢铁股份有限公司 | Production method of medium carbon structural steel without mixed crystal and widmannstatten structure |
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