CN101348882A - High stress, high plasticity and high hardenability large cross section spring steel - Google Patents
High stress, high plasticity and high hardenability large cross section spring steel Download PDFInfo
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Abstract
The invention relates to a large-section spring steel with high stress, high plasticity and high hardenability, which belongs to the alloy steel technical field. The compositions (in weight percent) of the steel are 0.37 to 0.43 percent of carbon, 0.80 to 1.40 percent of silicon, 1.30 to 2.20 percent of manganese, 0.08 to 0.14 percent of vanadium, 0.04 to 0.12 percent of titanium, 0.0015 to 0.004 percent of boron, less than 1.00 percent of chromium, less than 0.008 percent of nitrogen, 0.015 percent of sulfur, less than 20 parts per million of oxygen, and the balance being iron and impurities, wherein the gross amount of (Mn+Cr+Mo+w+0.2Ni) alloy is controlled to between 1.60 and 2.60 and B refers to the boron content analyzed by a 5N (equivalent weight) phosphate-sulfate solution sample. The spring steel with high strength and high plasticity can make the fatigue life of a large-section spring flat steel platform reach 0.25 million times under the high stress of 930 MPa and make the fatigue life of a large-section circular spring reach 0.8 million times under the high shear stress of 1,000 MPa. The steel is particularly suitable for manufacturing a damper spring for a moderate and heavy duty technical vehicle, a buffer for a rail vehicle and a spring for a bogie.
Description
(1) technical field:
The invention belongs to the technical field of steel alloy, is the large cross section spring steel of a kind of heavily stressed, high-ductility, high-hardenability.
(2) background technology:
At present, automobile self loss of weight requires the weight of motor spring to reduce.Adopt high strength, high-toughness spring steel; Be processed into the tapered spring band steel; Constitute the total journey of spring with one to three tapered spring band steel; Replacing the total journey of multi-disc plane spring band steel is the direction of current automobile technology technical development.The speed of train running is improving constantly, and present speed per hour has reached 250～500 kilometers; In order to ensure the safety of high-speed cruising, the bogie of train, the snubber spring steel, desired strength reaches 1800～2300Mpa, and reduction of area reaches more than 45～55%; Current, to press the intensity of spring steel and divide, intensity has 55Si2MnB at the steel grade of 1000～1300Mpa, 60Si2Mn, 55CrMn, 60CrMn, 50CrV, 60CrMnB; Intensity has 55SiMnVB at the steel grade of 1300～1500Mpa, 30W4Cr2V, 60CrMnMo; Intensity has 60Si2Cr at the steel grade of 1800～2000Mpa, 60Si2CrV, but the unit elongation of these two high-strength spring steels has only 6%, and reduction of area has only 20%.The characteristics that do not possess high-plasticity.The 38SiMnVB sedan suspension spring high strength that patent ZL98113532.3 proposes, high-ductility spring steel intensity is at 1800～2033Mpa, and reduction of area has 44～54%.This steel is applied to the tapered spring steel plate of thickness less than 12mm, diameter is less than the round spring of 20mm, obtained satisfied effect: for example car is taken advantage of the variable cross-section flat spring of 80mm, stand examination fatigue lifetime with 7mm, adopt 930Mpa heavily stressed, stand fatigue lifetime is all above 250,000 times.The round spring of 8～14mm diameter is used for the sedan suspension spring, adopts 1030Mpa heavily stressed, and stand fatigue lifetime is above 400,000 times.But, medium-sized and motorbus, medium and heavy engineering is big with the cross section specification of the used variable cross-section flat spring of automobile; The cross section specification of the round spring that train, subway are used is big.The trial effect of 38SiMnVB is bad.For example, the variable cross-section flat spring of 7 tons of trucies is of a size of 24mm and takes advantage of 100mm, adopts that 900Mpa is heavily stressed to carry out stand examination fatigue lifetime, and stand fatigue lifetime is 8～100,000 times.Do not reach 150,000 times requirement.Take advantage of 90mm and 38mm to take advantage of the variable cross-section flat spring of 81mm to 28mm, stand is lower fatigue lifetime, even when before the tired official test of stand the variable cross-section flat spring being applied prestress, brittle rupture repeatedly occurs.The 32mm circle spring that the train snubber is used, under the 1000Mpa shearing force, be 160,000 fatigue lifetime, do not reach 800,000 times requirement.
(3) summary of the invention:
Purpose of the present invention will solve the prior art steel grade exactly and make medium and heavy engineering truck anti-vibrating spring, train bogie, buffer spring weak point in work-ing life, performance is unreliable, particularly can not satisfy the problem that train speed-raising requires, the large cross section spring steel of a kind of heavily stressed, high-ductility, high-hardenability is provided.
The chemical ingredients of steel of the present invention is (weight percent): C 0.37～0.43, and Si 0.80～1.40, and Mn 1.30～2.20, V 0.08～0.14, Ti 0.04～0.12, and B 0.0015～0.004, Cr＜1.00, N＜0.008, S＜0.015, O＜20ppm, surplus is Fe and unavoidable impurities, wherein the overall control of (Mn+Cr+Mo+w+0.2Ni) alloy is 1.60～2.60, and B is the boron content with the molten sample analysis of 5N (equivalent) sulphur phosphoric acid.
When Mn=1.30～1.60, Cr gets 0.14～1.00 among the present invention, and other component (weight percent) of steel: C 0.37～0.43, and Si 0.80～1.40, V 0.08～0.14, and Ti 0.04～0.12, and B 0.0015～0.004, N＜0.008, S＜0.015, O＜20ppm.
When Mn=1.60～2.20, Cr adds element among the present invention, and other component (weight percent) of steel: C 0.37～0.43, and Si 0.80～1.40, V 0.08～0.14, and Ti 0.04～0.12, and B 0.0015～0.004, N＜0.008, S＜0.015, O＜20ppm.
The high strength that the present invention proposes, the stand that high-toughness spring steel can make the large cross section spring band steel are issued to 250,000 times the heavily stressed of 930Mpa fatigue lifetime, and large section circle spring reaches 800,000 times requirement fatigue lifetime under the 1000Mpa shearing force.The present invention is specially adapted to make the thick flat spring of 24-60mm, the round spring of diameter 25-100mm.
The relative prior art of the present invention has following progress:
1. the hardening capacity height of steel of the present invention can ensure that large cross section spring band steel and round steel have high strength, high-ductility, high fatigue life with the through hardening of large cross section spring steel during quenching.
The 38SiMnVB steel that patent ZL98113532.3 proposes is to be the sedan suspension spring of the small cross-section composition with the steel design, and the spring cross section is little, and heart portion speed of cooling is fast; Steel does not need too high hardening capacity, and the heart portion quenching hardness of steel just can reach the optimum value of 55-57HRC; After the tempering, have high-strength, high-ductility is tough, the characteristic of high fatigue life.Patent ZL98113532.3 emphasizes that the composition of steel does not contain noble elements such as Cr, Mn content 1.1～1.6%.When adopting remaining Cr, Ni is when the steel scrap that Mo content is very low is made steel; When the employing molten iron, when making steel with converter-vacuum refinement-continuous casting process, Cr, Ni, Mo, the W residual content in this case, is pressed the center line composition of steel and is calculated usually near zero; (Mn+Cr+Mo+W+0.2Ni) approximate 1.35%, the terminal distance of half martensite offset quenching of steel is 12mm; Can only be applicable to the round steel (for example: the round spring of 8～14mm diameter be used for sedan suspension spring) of diameter less than 20mm, thickness is less than the band steel (for example: car is taken advantage of the variable cross-section flat spring of 80mm with 7mm) of 12mm.Both just Mn worked as Cr by the Composition Control of reaching the standard grade in 1.3～1.6%, Mo, and the Ni residual element content is near zero the time; (Mn+Cr+Mo+w+0.2Ni)=1.45%; The terminal distance of half martensite offset quenching of steel is 15mm.Also can only be applicable to the round steel of diameter less than 23mm, thickness is less than the band steel of 16mm.When the light-duty engineering truck of production is taken advantage of the variable cross-section flat spring of 70mm with 19mm, (Mn+Cr+Mo+W+0.2Ni) total amount is brought up to 1.62% by 1.35% and (is added Cr to 0.13%, remaining alloying element is by middle upper limit control), the terminal distance of half martensite offset quenching of steel is 24.3mm; Adopt 930Mpa heavily stressed, stand fatigue lifetime is all above 250,000 times.If do not break through the restriction of patent ZL98113532.3 technical scheme; Take to improve alloy content, improve the measure of hardening capacity; Can not reach such level.For the large section circle spring of diameter 32～90mm, the large section variable cross-section spring that 24～60mm is thick, the alloy ratio of requirement is higher, and the hardening capacity of steel is higher.Because the alloy ratio of this patent design steel is too low, the hardening capacity of steel is too low; When being used to produce large cross section spring, steel heart portion quenching metallographic microstructure in regular meeting a large amount of upper bainites is arranged; Quenching hardness is low.At this moment, not only the intensity of steel does not reach the level of 1800～2033Mpa, the also non-constant of the plasticity of steel, toughness, and the fatigue lifetime of spring can be very low.For example: 81mm is wide, and the large cross section spring steel that 38mm is thick adopts oil quenching, and the heart portion quenching hardness of steel has only 43HRC; Adopt water quenching, the heart portion quenching hardness of steel has only 47HRC; Quenching hardness far below small cross-section spring heart portion.This is the basic reason that this technical scheme can not be applied to large cross section spring.Make large cross section spring also as the sedan suspension spring of small cross-section, the heart portion quenching hardness of steel reaches the optimum value of 55-57HRC; After the tempering, have high-strength, high-ductility is tough, the characteristic of high fatigue life; The essential restriction that breaks through patent ZL98113532.3 technical scheme takes to improve alloy content, improves the measure of hardening capacity: the one, and keep former patent Mn=1.10～1.60% constant, improve Cr, Mo, w, the content of Ni element; Perhaps only manganese content is brought up to Mn=1.6～2.3%, do not consider to add Cr, Mo, w, Ni element; The 3rd, summarize this two kinds of methods, be main added elements with control manganese content, be to replenish with other alloying element contents; Control (Mn+Cr+Mo+w+0.2Ni)=1.60～2.60%; The alloy total amount.
The technical scheme that the present invention proposes with the center line of C (carbon) content from 0.38%; Bring up to 0.40%; (lower limit is from 0.34%; Bring up to 0.37%; ); With Mn content from 1.10～1.60%; Bring up to 1.3～2.2%; , the Cr upper content limit brings up to 1.0%; The inventive point of the technical program is: special stipulation: (Mn+Cr+Mo+w+0.2Ni)=1.60～2.60%; Stipulate like this, when being requirement steel-making, if the Cr in the steel, Mo, w, the Ni residual content is too high; Can the corresponding add-on that reduces the Mn alloy.If considering Cr, Mo, w, the Hou of Ni residual content, the alloy total amount is still low than expected value, only improves the add-on of manganese alloy.Compare with patent ZL98113532.3 technical scheme, the technical program brings up to 1.60～2.60% with the alloy total amount by 1.10～1.60%.Metallographicobservation shows: when spring heart portion quenching hardness was lower than 53HRC, bainite structure began to occur.The raising of C and alloy ratio improves the hardening capacity of steel.The end quenching experiment of steel, by the center line composition measuring and calculating of the technical program, the terminal distance of half martensite offset quenching is 77.4mm.The technical scheme that the present invention proposes is brought up to 53～57HRC with the heart portion quenching hardness of the large section band steel of diameter 25mm～100mm large cross section spring round steel and thickness 20mm～60mm from 43HRC.The martensite content of heart portion is not less than 80%.Eliminate the upper bainite tissue that steel is become fragile, obtained desired martensitic stucture.C content be 0.40 martensitic stucture through 280～380 ℃ of tempering, have very high intensity and plasticity and toughness, stand height fatigue lifetime of large cross section spring.Overcome the existing defective of patent ZL98113532.3 technical scheme.
2. the technical scheme that proposes by the present invention is produced motor spring in enormous quantities, the stable performance of product:
Produce in enormous quantities and contain B boron steel, hardening capacity instability; Machine commandment unstable properties is ubiquitous problem; For example: the automobile of the contrast U.S. is with H steel standard, and the width of the hardenability band that contains the B steel of the U.S. is generally than the hardenability band of the steel that does not contain B.The present invention draws through studying for a long period of time: the carbon compound of boron and solid solution attitude boron are effective to the hardening capacity of steel, and the nitride of boron and oxide compound are invalid to the hardening capacity of steel.Adopt the molten sample of sulphur phosphoric acid of 5N concentration, the boron of analysis wherein has 95% to be effective boron, and 5% is invalid boron.If the employing spectroscopic analysis, then effective the and invalid element to boron can not selectively show.When the content of effective boron greater than 0.0015% the time, boron is a constant to the useful magnification of the hardening capacity of steel.When the content of effective boron less than 0.0015% the time, boron is a parameter to the useful magnification of the hardening capacity of steel; The speed of its variation very greatly.Therefore, when the content of effective boron less than 0.0015% the time, the hardening capacity of steel and machine commandment performance are extremely unstable.At present, with the steel-making of spectrum boron analysis and guidance, boron following is limited to 0.0005% produces in enormous quantities just and contain the B steel, the reason place of hardening capacity, machine commandment unstable properties.Second inventive point of the technical scheme that the present invention proposes is that regulation is analyzed boron with the molten sample of the sulphur phosphoric acid of 5N concentration, and also the following of regulation boron is limited to 0.0015%, eliminated the labile factor of boron; Therefore the technical scheme that proposes by the present invention is produced motor spring, the stable performance of product in enormous quantities.If the technical scheme that the B of containing steel produced in USA also adopts this patent to propose contains the B steel and will not have any difference with the width that does not contain the hardenability band of B steel.Patent ZL98113532.3 had not both stipulated the analytical procedure of effective boron, again too low with the following qualification of boron content; Mechanical performance of products, the fatigue property instability.For example: as the C=0.40 of steel, Mn=1.47, Cr=0.13, Si=1.00,, Ni=0.01, Mo=0.01, w=0.01 is during Cu=0.15; If the effective B content in the steel more than or equal to 0.0015 o'clock, is used to produce diameter when being the railway circle spring of 32mm, use water quenching, the heart portion quenching hardness of steel can reach 53～54HRC, through 330 ℃ of tempering, tempered-hardness 51HRC; The shearing stress of employing 1000Mpa carries out the fatigue experiment of spring, can reach 800,000 times.If the B in the steel is invalid boron, spring heart portion quenching hardness will be reduced to 45HRC, and characteristic high-strength after the tempering, high-ductility is lost, and also can descend significantly fatigue lifetime.Boron alloy is joined in the molten steel, is the boron in the last steel effective content, still invalid content? the operant level that depends on steelworker's reducing process fully.Must adopt to show that the detection method of effective boron monitors production process, could guarantee to produce in enormous quantities quality of stability.Patent ZL98113532.3 does not stipulate the analytical procedure of effective boron, and present many steel mills still adopt spectrometer analysis B; Can not carry out effective prosecution to production process, the quality of product can not be stablized.
3. the technical scheme that proposes by the present invention is produced motor spring in enormous quantities, the thick and mixed crystal problem of crystal grain can not occur:
Crystal grain is thick can to cause brittle rupture equally with mixed crystal problem, reduces fatigue lifetime.Remaining titanium content in steel is greater than 0.04%, steel roll (forging) temperature when being higher than 1250 ℃, the inherent grain size of steel is stabilized in the level of 6-8 level, two conditions are indispensable.The present invention stipulates Ti=0.04-0.12%.Patent ZL98113532.3 does not clearly stipulate titanium content; Produce motor spring, the thick and mixed crystal problem of crystal grain often occurs; Fatigue lifetime is low.For example: by the present invention, the C=0.40 of steel, Mn=1.47, Cr=0.13, Si=1.00,, Ni=0.01, Mo=0.01, w=0.01, during Cu=0.15, Ti=0.063%, V=0.10.Be used to produce the railway circle spring that diameter is 32mm, 1100 ℃ of induction heating are directly used water quenching behind spring, through 330 ℃ of tempering, the shearing stress of employing 1000Mpa carries out the fatigue experiment of spring, can reach 800,000 times, and fatigue fracture is rendered as significantly thin brilliant tough break.The grain fineness number of spring is 5～7 grades.By the one heat steel that patent ZL98113532.3 produces, other composition and steel fairly similar of the present invention, the C=0.40 of steel, Mn=1.46, Cr=0.14, Si=0.98,, Ni=0, Mo=0, w=0.01, Cu=0.12; Just the titanium content in the steel is less than 0.02%, V=0.08%; When being the railway circle spring of 32mm with identical explained hereafter diameter, the shearing stress of employing 1000Mpa carries out the fatigue experiment of spring, and the life-span drops to 160,000 times.Fatigue fracture is rendered as tangible coarse-grain rock-candy structure.The grain fineness number of spring is the 3-4 level.In order to eliminate coarse grain, with this stove steel induction heating air cooling behind spring, the air cooling of annealing again, reheat shrend; With the method crystal grain thinning of recrystallization repeatedly, reach after 6 grades; Carry out the fatigue experiment of spring again under the shearing stress of 950Mpa, the life-span returns to 930,000 times.Produce the train spring in enormous quantities by the technical scheme that the present invention proposes, production technique is simpler than patent ZL98113532.3; 1100 ℃ of induction heating can directly be used water quenching behind spring, the thick and mixed crystal problem of crystal grain can not occur, fatigue lifetime height.
4. the invention steel is compared notch sensitivity with the high-carbon spring steel and is obviously reduced:
Current, the main product of spring steel is that carbon content is 0.60% and 0.50% spring steel both at home and abroad.Carbon content is 0.60% and 0.50% spring steel, and maximum problem is when the intensity of steel reaches 1800～2300Mpa, and the plasticity of spring steel is low, and under high like this intensity, reduction of area has only 20-30%; Because the plasticity of high-carbon quantity spring steel is low, spring is when carrying out fatigue test, and the rate of expansion of fatigue cracking is very fast, and to the surface imperfection of steel, the crisp type slag inclusion in the steel is very responsive; The fine crack of steel surface is exposed to the fragility slag inclusion thing of steel surface, all may become tired source, causes the early fatigue fracture of spring; The notch sensitivity of steel is very high.Because like this, the production of spring steel requires oxygen level (the oxide compound slag inclusion is the fragility slag inclusion) in the steel less than 15ppm usually, and the cleaning of steel surface defective will reach bright as silver degree.Therefore the manufacturing cost of the spring steel of important use is very high, the costing an arm and a leg of steel.Both just quality of so strict control steel to the passenger train from goods train bogie, when the buffer spring quality is inspected by random samples, still has many products can not be qualified at national quality testing department.The technical program and carbon content are 0.60% to compare with 0.50% spring steel, and biggest advantage is when the intensity of steel reaches 1800～2300Mpa, and spring steel still has the characteristic of high-ductility, and reduction of area has 40～50%.Spring steel is when carrying out fatigue test, and the rate of expansion of crackle is slow, and to the surface imperfection of steel, the crisp type slag inclusion in the steel is insensitive.Therefore, both be that the oxygen level in the steel is not too low, the steel surface defective is cleared up not too thoroughly, also can not produce obviously influence to the fatigue lifetime of spring.For example: 32mm circle 38SiMnVB steel (bright as silver cleaning is not carried out on the surface) 1000Mpa shearing stress, 800,000 fatigue experiments, fatigue fracture are plastic fracture, 60Si2CrVA (bright as silver cleaning is carried out on the surface) 889Mpa shearing stress, 620,000 fatigue experiments, fatigue fracture are rock-candy structure.Steel of the present invention is compared notch sensitivity with the high-carbon spring steel and is obviously reduced; Increase substantially fatigue lifetime.
5. though the technical program is stipulated (Mn+Cr+Mo+w+0.2Ni)=1.60～2.60%; But not Mo, w, Ni considers as adding element; Just take in as residual element.Therefore, the UHS1900 of the technical program and 40Si2CrNiMoV steel and Japan, UHS2000, ND120S, RK360 (ND) 250S etc. contains higher Mo, w, the steel grade of Ni constituent content is compared, and has advantage cheaply in the application of alloying element.For example: the terminal hardening capacity experiment of RK360 (NC) 250S steel, the terminal distance of half martensite offset quenching is 72.3mm, performance and this programme are suitable.But this steel contains Cr 0.85%, and Ni 2.00%, and Mo 0.40%, and it is high a lot of that the material cost of steel-making is obviously wanted.
Do not require that steel have high cleanliness, can shorten the vacuum refinement time of steel-making greatly; Do not require that the steel surface peeling reaches bright as silver degree; Can reduce the surface-conditioning cost of steel greatly; The material cost of steel-making is much lower.Steel of the present invention has bigger low-cost advantage than existing spring steel.
(4) embodiment:
Embodiment 1-1:32mm circle spring (rail buffer) and 20mm take advantage of the composition of 90mm flat spring (Light-duty Vehicle) with steel:
C=0.40 Mn=1.45 Cr=0.20 B=0.002 (the boron content of B) Ti=0.04 V=0.08 Si=1.10 S=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
Mo＝0.01 w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.67
Embodiment 1-2:32mm circle spring (rail buffer) and 20mm take advantage of the composition of 90mm flat spring (Light-duty Vehicle) with steel:
C=0.37 Mn=1.40 Cr=0.35 B=0.0015 (the boron content of B) Ti=0.07 V=0.14 Si=0.8 S=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
Mo＝0.01 w＝0.01 Ni＝0.01 N＝0.006 O＝20PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.77
Embodiment 1-3:32mm circle spring (rail buffer) and 20mm take advantage of the composition of 90mm flat spring (Light-duty Vehicle) with steel:
C=0.43 Mn=1.47 Cr=0.18 B=0.004 (the boron content of B) Ti=0.09 V=0.12 Si=1.2 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.005 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.67
Embodiment 1-4:32mm circle spring (rail buffer) and 20mm take advantage of the composition of 90mm flat spring (Light-duty Vehicle) with steel:
C=0.40 Mn=1.61 Cr=0.01 B=0.003 (the boron content of B) Ti=0.10 V=0.13 Si=1.30 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.005 O＝15PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.64
Embodiment 2-1:40mm circle spring (heavy-load automobile) and 24mm take advantage of the composition of 100mm flat spring (heavy-duty car) with steel:
C=0.40 Mn=1.45 Cr=0.32 B=0.002 (the boron content of B) Ti=0.12 V=0.12 Si=1.4 S=0.012 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.79
Embodiment 2-2:40mm circle spring (heavy-load automobile) and 24mm take advantage of the composition of 100mm flat spring (heavy-duty car) with steel:
C=0.37 Mn=1.30 Cr=0.57 B=0.003 (the boron content of B) Ti=0.11 V=0.10 Si=1.10 S=0.01 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.89
Embodiment 2-3:40mm circle spring (heavy-load automobile) and 24mm take advantage of the composition of 100mm flat spring (heavy-duty car) with steel:
C=0.43 Mn=1.46 Cr=0.31 B=0.004 (the boron content of B) Ti=0.07 V=0.13 Si=1.10 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.79
Embodiment 2-4:40mm circle spring (heavy-load automobile) and 24mm take advantage of the composition of 100mm flat spring (heavy-duty car) with steel:
C=0.40 Mn=1.70 Cr=0.01 B=0.002 (the boron content of B) Ti=0.09 V=0.14 Si=1.10 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.73
Embodiment 3-1:56mm circle spring (subway) and 38mm take advantage of the composition of 81mm flat spring (heavy-duty car) with steel:
C=0.40 Mn=1.45 Cr=0.50 B=0.0015 (the boron content of B) Ti=0.08 V=0.08 Si=1.20 S=0.016 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.97
Embodiment 3-2:56mm circle spring (subway) and 38mm take advantage of the composition of 81mm flat spring (heavy-duty car) with steel:
C=0.37 Mn=1.44 Cr=0.61 B=0.003 (the boron content of B) Ti=0.06 V=0.10 Si=1.10 S=0.01 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.07
Embodiment 3-3:56mm circle spring (subway) and 38mm take advantage of the composition of 81mm flat spring (heavy-duty car) with steel:
C=0.43 Mn=1.46 Cr=0.49 B=0.002 (the boron content of B) Ti=0.04 V=0.12 Si=1.4 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.97
Embodiment 3-4:56mm circle spring (subway) and 38mm take advantage of the composition of 81mm flat spring (heavy-duty car) with steel:
C=0.40 Mn=1.74 Cr=0.05 B=0.004 (the boron content of B) Ti=0.05 V=0.13 Si=1.10 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.81
Embodiment 4-1:70mm circle spring (torsion bar) and 48mm take advantage of the composition of 100mm flat spring (traction engine) with steel:
C=0.40 Mn=1.45 Cr=0.64 B=0.002 (the boron content of B) Ti=0.09 V=0.10 Si=1.10 S=0.01 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.11
Embodiment 4-2:70mm circle spring (torsion bar) and 48mm take advantage of the composition of 100mm flat spring (traction engine) with steel:
C=0.37 Mn=1.44 Cr=0.75 B=0.002 (the boron content of B) Ti=0.10 V=0.10 Si=1.10 S=0.01 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.21
Embodiment 4-3:70mm circle spring (torsion bar) and 48mm take advantage of the composition of 100mm flat spring (traction engine) with steel:
C=0.43 Mn=1.46 Cr=0.63 B=0.002 (the boron content of B) Ti=0.11 V=0.10 Si=1.10 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.11
Embodiment 4-4:70mm circle spring (torsion bar) and 48mm take advantage of the composition of 100mm flat spring (traction engine) with steel:
C=0.40 Mn=1.84 Cr=0.01 B=0.003 (the boron content of B) Ti=0.07 V=0.10 Si=1.30 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.87
Embodiment 5-190mm circle spring (torsion bar) and 60mm take advantage of the composition of 160mm flat spring (traction engine) with steel:
C=0.40 Mn=1.45 Cr=0.78 B=0.004 (the boron content of B) Ti=0.09 V=0.10 Si=1.30 Mo=0.01 w=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.25
Embodiment 5-2:90mm circle spring (torsion bar) and 60mm take advantage of the composition of 160mm flat spring (traction engine) with steel:
C=0.37 Mn=1.44 Cr=0.89 B=0.002 (the boron content of B) Ti=0.08 V=0.10 Si=1.10 S=0.01 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.35
Embodiment 5-3:90mm circle spring (torsion bar) and 60mm take advantage of the composition of 160mm flat spring (traction engine) with steel:
C=0.43 Mn=1.46 Cr=0.77 B=0.002 (the boron content of B) Ti=0.04 V=0.10 Si=1.10 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.25
Embodiment 5-4:90mm circle spring (torsion bar) and 60mm take advantage of the composition of 160mm flat spring (traction engine) with steel:
C=0.40 Mn=1.88 Cr=0.01, B=0.002 (the boron content of B) Ti=0.07 V=0.10 Si=1.10 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=1.91
Embodiment 6-1:100mm circle spring (torsion bar) composition of steel:
C=0.40 Mn=1.45 Cr=0.95 B=0.002 (the boron content of B) Ti=0.07 V=0.10 Si=1.10 S=0.012 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.42
Embodiment 6-2:100mm circle spring (torsion bar) composition of steel:
C=0.37 Mn=1.58 Cr=1.00 B=0.002 (the boron content of B) Ti=0.07 V=0.10 Si=1.10 S=0.01 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.60
Embodiment 6-3:100mm circle spring (torsion bar) composition of steel:
C=0.43 Mn=1.46 Cr=0.94 B=0.002 (the boron content of B) Ti=0.07 V=0.10 Si=1.10 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.42
Embodiment 6-4:100mm circle spring (torsion bar) composition of steel:
C=0.40 Mn=2.20 Cr=0.01 B=0.002 (the boron content of B) Ti=0.07 V=0.10 Si=1.10 S=0.014 Mo=0.01 for analyzing with the molten sample of 5N sulphur phosphoric acid
w＝0.01 Ni＝0.01 N＝0.008 O＝10PPm
Surplus is Fe and impurity, wherein: (Mn+Cr+Mo+w+0.2Ni)=2.23
By the spring steel of above embodiment composition smelting, through 1250～1300 ℃ of heat, cold soon after edging is become a useful person (cold scattering in the air), the cleaning of steel surface defective reaches 3.2 grades; Justify spring through 1000～1050 ℃ of induction heating, direct water hardening behind spring; Through 280～380 ℃ of tempering.Spring part heart portion quenching hardness can reach 53～57HRC, tempered-hardness 50～52HRC.Spring in addition part after cold shot peening.Under 1000Mpa shearing stress, can reach fatigue lifetime 800,000 times.To tapered spring, 1150～1100 ℃ of heat, edging becomes cold soon (cold scattering in the air) behind the variable cross-section spring with spring flat steel, spring direct water hardening after 860～880 ℃ of heating; Through 280～380 ℃ of tempering.Spring part heart portion quenching hardness in addition can reach 53～57HRC, tempered-hardness 50～52HRC.Spring in addition part after cold shot peening.Under 930Mpa shearing stress, can reach fatigue lifetime 250,000 times.
Claims (3)
1. the large cross section spring steel of heavily stressed a, high-ductility, high-hardenability, it is characterized in that: the component of steel is (weight percent): C 0.37～0.43, Si 0.80～1.40, Mn 1.30～2.20, V 0.08～0.14, Ti 0.04～0.12, B 0.0015～0.004, Cr＜1.00, N＜0.008, S＜0.015,0＜20ppm, surplus is Fe and unavoidable impurities, and wherein the overall control of (Mn+Cr+Mo+w+0.2Ni) alloy is 1.60～2.60, and B is the boron content with the molten sample analysis of 5N (equivalent) sulphur phosphoric acid.
2. the large cross section spring steel of a kind of heavily stressed, high-ductility according to claim 1, high-hardenability, it is characterized in that: when Mn=1.30～1.60, Cr gets 0.14～1.00, and other component (weight percent) of steel: C 0.37～0.43, and Si 0.80～1.40, V 0.08～0.14, Ti 0.04～0.12, and B 0.0015～0.004, N＜0.008, S＜0.015,0＜20ppm.
3. the large cross section spring steel of a kind of heavily stressed, high-ductility according to claim 1, high-hardenability, it is characterized in that: when Mn=1.60～2.20, Cr adds element, and other component (weight percent) of steel: C 0.37～0.43, and Si 0.80～1.40, V 0.08～0.14, Ti 0.04～0.12, and B 0.0015～0.004, N＜0.008, S＜0.015,0＜20ppm.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101693980B (en) * | 2009-09-30 | 2011-06-01 | 山西太钢不锈钢股份有限公司 | Flat steel and manufacture method thereof |
| CN102803537A (en) * | 2009-12-18 | 2012-11-28 | 爱知制钢株式会社 | Steel for leaf spring with high fatigue strength, and leaf spring component |
| CN103014517A (en) * | 2013-01-11 | 2013-04-03 | 方大特钢科技股份有限公司 | Multicomponent alloy integrated spring flat steel |
| CN104114732A (en) * | 2012-02-14 | 2014-10-22 | 杰富意钢铁株式会社 | Spring steel |
| CN111118398A (en) * | 2020-01-19 | 2020-05-08 | 石家庄钢铁有限责任公司 | High-hardenability high-strength low-temperature-toughness spring steel and production method thereof |
| CN111893377A (en) * | 2020-07-13 | 2020-11-06 | 首钢集团有限公司 | Aluminum-silicon plated steel plate for 1900 MPa-grade high-strength and high-toughness hot stamping and preparation method thereof |
| CN112375970A (en) * | 2020-10-20 | 2021-02-19 | 东风汽车底盘系统有限公司 | Spring steel and processing method thereof |
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2007
- 2007-07-20 CN CN200710052805A patent/CN100591791C/en not_active Expired - Fee Related
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101693980B (en) * | 2009-09-30 | 2011-06-01 | 山西太钢不锈钢股份有限公司 | Flat steel and manufacture method thereof |
| CN102803537A (en) * | 2009-12-18 | 2012-11-28 | 爱知制钢株式会社 | Steel for leaf spring with high fatigue strength, and leaf spring component |
| US8741216B2 (en) | 2009-12-18 | 2014-06-03 | Nhk Spring Co., Ltd. | Steel for leaf spring with high fatigue strength, and leaf spring parts |
| CN106381450A (en) * | 2009-12-18 | 2017-02-08 | 爱知制钢株式会社 | Steel for leaf spring with high fatigue strength, and leaf spring parts |
| CN104114732A (en) * | 2012-02-14 | 2014-10-22 | 杰富意钢铁株式会社 | Spring steel |
| CN103014517A (en) * | 2013-01-11 | 2013-04-03 | 方大特钢科技股份有限公司 | Multicomponent alloy integrated spring flat steel |
| CN111118398A (en) * | 2020-01-19 | 2020-05-08 | 石家庄钢铁有限责任公司 | High-hardenability high-strength low-temperature-toughness spring steel and production method thereof |
| CN111893377A (en) * | 2020-07-13 | 2020-11-06 | 首钢集团有限公司 | Aluminum-silicon plated steel plate for 1900 MPa-grade high-strength and high-toughness hot stamping and preparation method thereof |
| CN111893377B (en) * | 2020-07-13 | 2021-10-26 | 首钢集团有限公司 | Aluminum-silicon plated steel plate for 1900 MPa-grade high-strength and high-toughness hot stamping and preparation method thereof |
| CN112375970A (en) * | 2020-10-20 | 2021-02-19 | 东风汽车底盘系统有限公司 | Spring steel and processing method thereof |
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| CN100591791C (en) | 2010-02-24 |
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