CN103975082B - The manufacture method of ageing resistance and the excellent high strength cold rolled steel plate of sinter-hardened property - Google Patents
The manufacture method of ageing resistance and the excellent high strength cold rolled steel plate of sinter-hardened property Download PDFInfo
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- CN103975082B CN103975082B CN201280060602.5A CN201280060602A CN103975082B CN 103975082 B CN103975082 B CN 103975082B CN 201280060602 A CN201280060602 A CN 201280060602A CN 103975082 B CN103975082 B CN 103975082B
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Abstract
The invention provides the manufacture method of the high strength cold rolled steel plate having ageing resistance and sinter-hardened property concurrently.After former for steel material is heated to the temperature of 1000 ~ 1300 DEG C of scopes, implement the hot rolling that finish rolling end temp is set as more than 860 DEG C, batches under the coiling temperature of 550 ~ 720 DEG C of scopes, then, implement cold rolling, implement further soaking at the temperature of 760 ~ 900 DEG C of scopes, carry out the anneal that cools with the average cooling rate of more than 10 DEG C/sec.After annealing, implementing elongation is the temper rolling of 0.2 ~ 1.0%, then, implements the thermal treatment keeping 10 minutes ~ 10 hours at the temperature of 70 ~ 140 DEG C of scopes.The former material of described steel has following composition: in mass % containing C:0.0010% ~ 0.0080%, below Si:1.0%, Mn:0.1% ~ 1.8%, below P:0.100%, below S:0.03%, sol.Al:0.01% ~ 0.50%, below N:0.0050%, and to meet (Nb/92.9)/(C/12): the mode of 0.3 ~ 0.9 contains Nb, and to meet [(Co/58.9)+(Cu/63.5)+(Cr/52.0)+(Mo/95.9)]/(C/12): the mode of 0.5 ~ 5.0 regulates and containing being selected from below Co:0.05%, below Cu:0.05%, below Cr:0.05%, more than at least one or two in below Mo:0.05%.
Description
Technical field
The present invention relates to the cold-rolled steel sheet and manufacture method thereof that are suitable for car panel parts, particularly tensile strength TS is 340 ~ 440MPa level, has high strength cold rolled steel plate and the manufacture method thereof of excellent ageing resistance (anti-agingproperty) and excellent sinter-hardened property (bake-hardeningproperty) (hereinafter also referred to BH (BHproperty)) concurrently.
It should be noted that, " steel plate (steelsheet) " herein comprises steel plate (steelsheet), steel band (steelstrip).In addition, " cold-rolled steel sheet " also comprises cold-rolled steel sheet and implements the cold-rolled steel sheet after the surface treatment such as plating to this cold-rolled steel sheet.As plating, comprise pure zinc plating, with the addition of the Zn based alloy plating of alloying element or Al using zinc as principal constituent or with the addition of the Al system alloy plating process etc. of alloying element using Al as principal constituent.
Background technology
In recent years, from the view point of environment of preserving our planet, in order to reduce carbonic acid gas CO
2quantity discharged, be strongly required to improve the fuel efficiency of automobile.In addition, recently, in order to ensure the safety of passenger during Vehicular impact, require to improve security centered by the impact characteristics improving body of a motor car.
In order to tackle such requirement, actively carry out lightweight and the strengthening of body of a motor car.In order to meet lightweight and the strengthening of body of a motor car simultaneously, it is said and carry out high strength and carry out thin-walled property in the unquestioned scope of rigidity being effective to used former material, recently, as trolley part use, actively use high-tensile steel.
For the light-weighted requirement of such body of a motor car, such as, as the panel material of inner panel and outside plate, tend to use the steel plate with the intensity that tensile strength TS is more than 390MPa.On the other hand, use as the panel component such as door and car bonnet, require that dent resistance (dentresistancestrength) is excellent, therefore, the rear yield strength of application sintering raises, so-called sinter-hardened shaped steel plate (bake-hardenedsteelsheet) (BH steel plate (BHsteelsheet)) is used in.
As BH steel plate, be generally pole low-carbon (LC) system, utilize Mn, P to carry out the steel plate after solution strengthening containing carbon with the Nb of atomic ratio measuring equivalent or its following amount, by there is a small amount of solid solution C after the annealing process, the fixing dislocation waiting processing to introduce by pressurization in application sintering processes process, increase yield strength, dent resistance is improved.
As so sinter-hardened shaped steel plate (BH steel plate), such as, describe a kind of high tensile strength cold-rolled steel sheet had excellent moldability in patent documentation 1, its contain C:0.002 ~ 0.015%, below Si:1.2%, Mn:0.04 ~ 0.8%, P:0.03 ~ 0.10%, more than Al:0.02% and for more than N% × 4, Nb:C% × 3 ~ { C% × 8+0.020%}, surplus is made up of Fe in fact.The high tensile strength cold-rolled steel sheet recorded in patent documentation 1 obtains as follows: carry out to the steel billet of above-mentioned composition the hot rolling that total reduction is more than 90%, roll speed is more than 40m/ minute, batch at temperature more than 600 DEG C, then, carry out cold rolling, further enforcement keeps the continuous annealing of 10 seconds ~ 5 minutes at 700 ~ 900 DEG C, until 500 DEG C, cool with the speed of cooling of more than 60 DEG C/min.This cold-rolled steel sheet is tensile strength TS is 35 ~ 45kgf/mm
2the aging resistance (anti-agingproperty) of level and the excellent steel plate of plasticity (formability).
Prior art document
Patent documentation
Patent documentation 1: Japanese Laid Open Patent JP56-139654 publication
Summary of the invention
Invent problem to be solved
But, in the technology recorded in patent documentation 1, in order to improve sinter-hardened property, there is the problem reducing Nb amount or occur elongation at yield due to timeliness.That is, in the manufacture method in the past always studied, there is the problem that can not have ageing resistance and sinter-hardened property concurrently.
In the present invention, its object is to, solve the problem of such prior art, provide tensile strength TS to be 340 ~ 440MPa level, have concurrently the manufacture method of the high strength cold rolled steel plate of ageing resistance and sinter-hardened property (BH).
It should be noted that, after " ageing resistance is excellent " herein refers to timeliness at normal temperatures, elongation at yield is few, is less than 0.8%.In addition, " sinter-hardened property (BH) is excellent " herein refer to imparting 2% prestrain, implement the thermal treatment (application sintering processes) of 170 DEG C × 20 minutes afterwards, the yielding stress situation that is more than 30MPa relative to the most heavily stressed increasing amount (BH amount) under prestrain.
For the method for dealing with problems
The present inventor to achieve these goals, is studied in detail the impact that various factors brings to BH, ageing resistance.Its result obtains following opinion: in order to have ageing resistance and sinter-hardened property concurrently, the control of the solid solution C under normal temperature and application sintering temperature is important.And find, in order to suitably carry out the control of solid solution C, be important by the two combination following, that is: except Nb, suitably select the trace additives that Cr, Cu, Co, Mo etc. are different with Nb from the interaction of C, make and be adjusted to proper content and the composition that contains; And the thermal treatment implemented after temper rolling under low temperature, thereby, it is possible to obtain cold-rolled steel sheet that little, the sinter-hardened amount of the elongation at yield after room temperature ageing (BH amount) improves, that have ageing resistance and sinter-hardened property concurrently.
Then, about the impact that the thermal treatment temp after temper rolling produces elongation at yield, the experimental result that the present inventor carries out is described.
To there is the former material of the steel formed that is made up of iron and inevitable impurity for 0.0026%C-0.01%Si-0.4%Mn-0.051%P-0.003%S-0.037%Al-0.0030% N-0.011%Nb-0.018%Cr-surplus in mass % at finish rolling end temp: 900 DEG C, coiling temperature: implement hot rolling under the condition of 650 DEG C and make hot-rolled sheet, then, pickling and cold rolling and make cold-reduced sheet is implemented to obtained hot-rolled sheet.Then, to obtained cold-reduced sheet implement be heated to annealing temperature 840 DEG C carry out soaking after, make until the average cooling rate of 300 DEG C is that 15 DEG C/sec of anneal cooled make cold rolled annealed plate.
Implement to make skin-pass amount (elongation) carry out the temper rolling of various change to obtained cold rolled annealed plate, then, implement to make thermal treatment temp Temp in the scope of RT (25 DEG C) ~ 170 DEG C, carry out the low-temperature heat treatment of various change.It should be noted that, the hold-time under thermal treatment temp Temp is set as 1 hour.After implementing temper rolling and low-temperature heat treatment, implement tension test, investigate elongation at yield rate.Obtained result is shown in Fig. 1 with the relation of elongation at yield rate Y-El and thermal treatment temp Temp.
As shown in Figure 1, in skin-pass amount (elongation) up under the elongation condition of 1.8%, the thermal treatment temp Temp of low-temperature heat treatment is until about 120 DEG C, and elongation at yield rate Y-El is little, but produces elongation at yield rate Y-El when thermal treatment temp Temp increases further.This tendency is the tendency all the time known.In addition, elongation condition (the such as skin-pass amount (elongation): 0.5%) of elongation at yield rate Y-El is slightly observed at once after temper rolling, when thermal treatment temp Temp is about 70 DEG C ~ about 140 DEG C, elongation at yield rate Y-El reduces.About the reason that elongation at yield rate reduces, be still not clear at present, but can think by carbon and the interaction of the dislocation introduced when temper rolling and elongation at yield rate is reduced.
The present invention carries out having studied based on such opinion further.That is, purport of the present invention is as described below.
[1] manufacture method for ageing resistance and the excellent high strength cold rolled steel plate of sinter-hardened property, it comprises:
Prepare the former material of steel,
The former material of this steel is implemented that finish rolling end temp is set as more than 860 DEG C, the hot rolling of batching under the coiling temperature of 550 ~ 720 DEG C of scopes and make hot-rolled sheet,
Implement cold rolling to this hot-rolled sheet and make cold-reduced sheet,
This cold-reduced sheet is implemented under annealing temperature is the temperature of 760 ~ 900 DEG C of scopes after soaking, is made until the average cooling rate of 300 DEG C is that cold rolled annealed plate is made in more than the 10 DEG C/sec annealing cooled,
To this cold rolled annealed plate with 0.2 ~ 1.0% elongation implement temper rolling or leveling processing,
Implement the thermal treatment keeping 10 minutes ~ 10 hours at the temperature of 70 ~ 140 DEG C of scopes,
The former material of described steel has following composition: in mass % containing more than C:0.0010% and less than 0.0080%, below Si:1.0%, more than Mn:0.1% and less than 1.8%, below P:0.100%, below S:0.03%, more than sol.Al:0.01% and less than 0.50%, below N:0.0050%, more than Nb:0.005% and less than 0.050%, Nb content and C content meet following (1) formula, and be selected from by below Co:0.05%, below Cu:0.05%, below Cr:0.05%, at least one in the group that below Mo:0.05% forms meets following (2) formula, surplus comprises Fe and inevitable impurity,
0.3≤(Nb/92.9)/(C/12)≤0.9…(1)
0.5≤[(Co/58.9)+(Cu/63.5)+(Cr/52.0)+(Mo/95.9)]/(C/12)≤5.0…(2)
Wherein, Nb, C, Co, Cu, Cr, Mo: the quality % content of each element.
The manufacture method of the high strength cold rolled steel plate [2] as described in [1], wherein, the former material of above-mentioned steel, on the basis of above-mentioned composition, contains below B:0.0050% in mass % further.
The manufacture method of the high strength cold rolled steel plate [3] as described in [1] or [2], wherein, above-mentioned cold rolling be with more than 50% and the draft of less than 85% implement cold rolling.
The manufacture method of the high strength cold rolled steel plate [4] as described in [1] ~ [3], wherein, above-mentioned cold rolled annealed plate has ferrite single phase structure.
The manufacture method of the high strength cold rolled steel plate [5] as described in [1] ~ [4], wherein, implements plating to above-mentioned cold rolled annealed plate.
The manufacture method of the high strength cold rolled steel plate [6] as described in [1] ~ [5], wherein, above-mentioned cold-rolled steel sheet is the elongation at yield rate after the timeliness under normal temperature is the cold-rolled steel sheet of less than 0.8%.
The manufacture method of the high strength cold rolled steel plate [7] as described in [1] ~ [6], wherein, above-mentioned cold-rolled steel sheet be sinter-hardened after yielding stress increasing amount be the cold-rolled steel sheet of more than 30MPa.
The manufacture method of the high strength cold rolled steel plate [8] as described in [1] ~ [7], wherein, the cold-rolled steel sheet of above-mentioned cold-rolled steel sheet to be tensile strength be 340 ~ 440MPa.
Invention effect
According to the present invention, can manufacture easily and at an easy rate that the panel component, the tensile strength TS that are suitable for body of a motor car are 340 ~ 440MPa level, yield ratio is low, elongation also high, have excellent moldability and have the high strength cold rolled steel plate of excellent ageing resistance and excellent sinter-hardened property concurrently, industrially play special effect.In addition, high strength cold rolled steel plate of the present invention also can be applied as the inner and outer plates purposes of body of a motor car, also has the effect fully can made contributions to the raising of the lightweight of body of a motor car, crash safety.In addition, high strength cold rolled steel plate of the present invention also can be applied as family's electrical article or the former material of pipeline.
Accompanying drawing explanation
Fig. 1 is the figure representing the impact that skin-pass amount (skin-pass elongation) relation on elongation at yield rate Y-El and thermal treatment temp Temp produces.
Embodiment
The present invention is a kind of manufacture method of high strength cold rolled steel plate, wherein, implement successively to the former material of steel carry out heating implement hot rolling and make hot-rolled sheet hot-rolled process, to this hot-rolled sheet implement cold rolling and make cold-reduced sheet cold rolling process, this cold-reduced sheet implemented to anneal and make the annealing operation of cold rolled annealed plate and this cold rolled annealed plate implemented to the temper rolling operation of temper rolling or leveling processing, obtain the high strength cold rolled steel plate having excellent ageing resistance and excellent sinter-hardened property (BH) concurrently.
First, limit reason to the composition of the former material of steel used as initial former material to be described.Below, unless otherwise specified, then only represent with % about the quality % of composition.
More than C:0.0010% and less than 0.0080%
C is for having excellent ageing resistance and the important element of excellent BH concurrently, in the BH guaranteeing to expect, needs containing more than 0.0010%.On the other hand, a large amount of containing sometimes more than 0.0080%, from the view point of guaranteeing ageing resistance, needing to improve Nb content, causing the surging of material cost, and in the poor situation of Nb, sometimes room temperature ageing occurs.Therefore, C is defined as more than 0.0010% and the scope of less than 0.0080%.In addition, be preferably less than 0.0080%, more preferably less than 0.0060%, further preferably less than 0.0040%.
Below Si:1.0%
Si makes the intensity of steel plate increase and improve the element of processing ability to cure by solution strengthening.In order to obtain such effect, preferably containing more than 0.01%, further preferably containing more than 0.1%.On the other hand, more than 1.0% in a large number containing sometimes, produce red oxide skin when hot rolling, easily reduce the appearance of steel plate, and when zinc-plated, encourage the generation of not plating.In addition, Si's as above is a large amount of containing also chemical convertibility being made to reduce.Therefore, Si is defined as less than 1.0%.In addition, preferably less than 0.5%.
More than Mn:0.1% and less than 1.8%
Mn has generation solid solution and makes the intensity of steel plate increase and fixed with the form of MnS by S thus prevent the effect of the thermal crack caused by S.In order to obtain such effect, need containing more than 0.1%.On the other hand, excessive in sometimes more than 1.8%, ductility, r value are reduced.Therefore, Mn is defined as the scope of 0.1 ~ 1.8%.In addition, preferably less than 1.2%.
Below P:0.100%
The effect that P has generation solid solution and steel plate is strengthened, but in crystal boundary generation segregation, make the embrittlement of resistance to secondary processing, weldability reduction.The detrimentally affect of such P becomes remarkable sometimes in excessive the containing more than 0.100%.Therefore, P is defined as less than 0.100%.In addition, preferably less than 0.080%.
Below S:0.03%
S can produce thermal crack, and exists as sulfide-based inclusion, makes the reductions such as ductility.Therefore, in the present invention, preferably reduce as far as possible, but can allow to 0.03%.For the foregoing reasons, S is defined as less than 0.03%.In addition, preferably less than 0.01%.
More than sol.Al:0.01% and less than 0.50%
Al plays a role as reductor, and forms nitride and fixed by solid solution N, and ageing resistance is improved.In order to obtain such effect, need containing more than 0.01%.On the other hand, a large amount of the containing more than 0.50% can make material cost (cost of alloy) surging, and causes the multiple of surface imperfection.Therefore, sol.Al is defined as the scope of 0.01 ~ 0.50%.In addition, less than 0.30% is preferably.
Below N:0.0050%
There is solid solution and make the element that the intensity of steel increases in N, but containing more than 0.0050% can make ageing resistance reduce.Therefore, in the present invention, N is defined as less than 0.0050%.
More than Nb:0.005% and less than 0.050%
The carbide Forming ability of Nb is high, has fixation of C and makes hot rolling microstructure miniaturization thus the effect of raising r value, contributing to improving plasticity.In order to obtain such effect, need containing more than 0.005%.On the other hand, excessive the containing more than 0.050% can make thermal distortion resistance increase, and rolling load during hot rolling is increased.Therefore, Nb is defined as the scope of 0.005 ~ 0.050%.
It should be noted that, Nb to regulate in the mode meeting following (1) formula and contains in above-mentioned scope and for the implication of fixation of C.
0.3≤(Nb/92.9)/(C/12)≤0.9…(1)
(wherein, Nb, C: the content (quality %) of each element)
(Nb/92.9) atomic ratio that/(C/12) is Nb and C, when (Nb/92.9)/(C/12) is less than 0.3, C's is fixing insufficient, when shape components, tensile deformation occurs, and surface quality reduces.On the other hand, during more than 0.9, solid solution C is not enough, and BH reduces.Therefore, (Nb/92.9)/(C/12) is defined as the scope of 0.3 ~ 0.9.In addition, 0.5 ~ 0.8 is preferably.
One or more in below Co:0.05%, below Cu:0.05%, below Cr:0.05%, below Mo:0.05%
Although Co, Cu, Cr, Mo are all so strong unlike Nb, are have interactional element with C, select containing one or more.Co, Cu, Cr, Mo catch C at normal temperatures, postpone its diffusion, on the other hand, are separated when application sintering processes with C, contribute to improving BH.In order to obtain such effect, Co, Cu, Cr, Mo are respectively preferably containing more than 0.01%.On the other hand, Co, Cu, Cr, Mo are a large amount of containing sometimes more than 0.05% respectively, and C is excessively fixing, and BH reduces.Therefore, limit that Co is less than 0.05%, Cu is less than 0.05%, Cr is less than 0.05%, Mo is less than 0.05% respectively.It should be noted that, such effect becomes more remarkable by the thermal treatment implemented under low temperature after temper rolling.
It should be noted that, in the present invention, Co, Cu, Cr, Mo regulate and contain in above-mentioned scope and in the mode meeting following (2) formula.
0.5≤{(Co/58.9)+(Cu/63.5)+(Cr/52.0)+(Mo/95.9)}/(C/12)≤5.0…(2)
(Co, Cu, Cr, Mo, C: the content (quality %) of each element)
(Co/58.9)+(Cu/63.5)+(Cr/52.0)+(Mo/95.9) } atomic ratio of/total amount that (C/12) is Co, Cu, Cr, Mo and C, (Co/58.9)+(Cu/63.5)+(Cr/52.0)+(Mo/95.9) }/(C/12) when being less than 0.5, catching of C is insufficient, easily there is tensile deformation when shape components, likely make surface quality reduce.On the other hand, during more than 5.0, solid solution C is not enough, and BH reduces.Therefore, { (Co/58.9)+(Cu/63.5)+(Cr/52.0)+(Mo/95.9) }/(C/12) is defined as the scope of 0.5 ~ 5.0.In addition, 1.0 ~ 3.0 are preferably.
Mentioned component is basic composition, but except basal component, can also containing below B:0.0050% as selecting element.
Below B:0.0050%
B is the element degradation property of resistance to secondary processing being improved in crystal boundary generation segregation, in order to ensure such effect, preferably containing more than 0.0003%, even if but contain more than 0.0050%, effect is also saturated, cannot expect the effect matched with content, therefore, become unfavorable economically.Therefore, when containing, B is preferably defined as less than 0.0050%.In addition, less than 0.0030% is more preferably.
Surplus beyond mentioned component comprises Fe and inevitable impurity.As inevitable impurity, can Ca, REM, Sb, Sn, Zn be enumerated, can below Ca:0.01%, below REM:0.01%, below Sb:0.01%, below Sn:0.1%, below Zn:0.01% be allowed.
In the present invention, hot-rolled process, cold rolling process, annealing operation and temper rolling operation are implemented successively to the former material of the steel of above-mentioned composition and makes cold-rolled steel sheet.
It should be noted that, the molten steel of above-mentioned composition without the need to being particularly limited to, but is carried out melting preferably by the melting method that converter process, electric furnace process etc. are conventional by the manufacture method of the former material of steel, makes the former material of the steel such as steel billet by conventional castmethods such as continuous metal cast processs.For the castmethod of the former material of steel, be set as continuous metal cast process preferably in preventing the macrosegregation of composition, but by ingot casting method, thin slab casting also without any problem.
In hot-rolled process, for the heating of hot rolling except former for steel material (steel billet) being temporarily cooled to room temperature, then carrying out except the method that reheats, also can adopt without any problems and not be cooled to room temperature and the energy-saving technique such as direct sending rolling/Direct Rolling being encased under the state of warm sheet in process furnace or being rolled at once after carrying out thermal protection slightly.
Hot-rolled process preferably heats the former material of steel, implement the hot rolling be made up of roughing and finish rolling and the operation made hot-rolled sheet, then batch.
The Heating temperature of the former material of steel is preferably set to 1000 ~ 1300 DEG C.When Heating temperature is lower than 1000 DEG C, resistance to deformation is high, and rolling loads increases, and the risk level broken down during hot rolling increases.On the other hand, under the high temperature more than 1300 DEG C, along with the increase of oxidative weight, scale loss increases.
The former material of steel after heating is laminated by roughing base.The condition of roughing, without the need to being particularly limited to, can be carried out according to conventional methods.It should be noted that, from the view point of reducing the former material Heating temperature of steel and fault when preventing hot rolling, combinationally using the so-called thin slab well heater heated thin slab is effective means.
Then, finish rolling carried out to thin slab and make hot-rolled sheet.Now, finish rolling end temp is set as more than 860 DEG C.This is to obtain fine hot-rolled sheet tissue to obtain excellent deep drawability after cold rolling and recrystallization annealing.When finish rolling end temp is lower than 860 DEG C, skin section reaches below transformation temperature and forms oversize particle, or fully flourishing from the phase transformation texture that non-recrystallization γ phase transformation is next, undeveloped in cold rolled annealed rear texture, and then rolling load during hot rolling increases.For the foregoing reasons, finish rolling end temp is defined as more than 860 DEG C.On the other hand, when finish rolling end temp reaches a high temperature more than 980 DEG C, organize greatly thicker, hinder cold rolled annealed after the formation of recrystallization texture and prosperity, sometimes can not get high r value, therefore, be preferably set to less than 980 DEG C.Therefore, preferred finish rolling end temp is 880 ~ 940 DEG C.
It should be noted that, in order to reduce rolling loads during hot rolling, lubrication and rolling can be set between the passage of part or all of finish rolling.It is also effective for carrying out lubrication and rolling from the homogenizing of plate profile and the viewpoint homogenized of material.It should be noted that, frictional coefficient during lubrication and rolling is preferably set to the scope of 0.10 ~ 0.25.In addition, also preferably set the thin slab be close to front and back to be engaged with each other and the technique for continuous rolling carrying out finish rolling continuously.From the view point of the job stabilization of hot rolling, preferred technique for continuous rolling.
After finish rolling terminates, hot-rolled sheet is batched.Coiling temperature is set as the temperature of 550 ~ 720 DEG C of scopes.When coiling temperature is lower than 550 DEG C, the precipitation of NbC becomes insufficient.On the other hand, under the high temperature more than 720 DEG C, grain coarsening is large, causes the reduction of armor plate strength.In addition, if coiling temperature to be set as the high temperature more than 720 DEG C, then can hinder cold rolled annealed after high r value, plasticity reduces sometimes.Therefore, coiling temperature is defined as the scope of 550 ~ 720 DEG C.In addition, less than 660 DEG C are preferably.
Then, cold rolling process is implemented to the hot-rolled sheet terminated after hot-rolled process.
It should be noted that, before cold rolling process, preferably suitably implement pickling.Acid washing method can adopt arbitrary common method.
In cold rolling process, as long as can make the cold-reduced sheet of desired size, its condition is without the need to being particularly limited to, and cold rolling draft is preferably set to more than 50%.In order to obtain the steel plate that r value is high, plasticity is good, be set as that high cold rolling draft is effective, when draft is less than 50%, { 111} recrystallization texture can not be flourishing, and deep drawability reduces sometimes.On the other hand, improve cold rolling draft, r value more raises, but cold rolling draft more than 85% time, its effect is saturated, and in addition, the rolling load of pair roller increases.Therefore, cold rolling draft is preferably set to more than 50% and less than 85%.
Anneal is carried out to the cold-reduced sheet enforcement after end cold rolling process and makes the annealing operation of cold rolled annealed plate.In the present invention, anneal is preferably set to following process: in continuous annealing production line, by cold-reduced sheet at the temperature of annealing temperature 760 ~ 900 DEG C of scopes after soaking, by until the average cooling rate of 300 DEG C is set as that more than 10 DEG C/sec cool.
When annealing temperature is lower than 760 DEG C, non-recrystallization tissue residue, ductility reduces.On the other hand, under the high temperature more than 900 DEG C, generating austenite phase when annealing, generating cooled low-temperature phase covert or solid solution C is measured increase, ageing resistance is reduced.Therefore, annealing temperature is defined as the temperature of 760 ~ 900 DEG C of scopes.In addition, more than 800 DEG C are preferably.
In addition, the speed of cooling after soaking is in until when the average cooling rate of 300 DEG C is less than 10 DEG C/sec, slowly cooled, and solid solution C separates out with the form of cementite again, and BH reduces.Therefore, the speed of cooling after soaking is in until the average cooling rate of 300 DEG C is defined as more than 10 DEG C/sec.In addition, less than 40 DEG C/sec are preferably.
It should be noted that, the tissue terminating the cold rolled annealed plate after annealing operation becomes ferrite single phase structure.When there is the equal second-phase of beyond ferritic phase, such as martensite, ageing resistance changes, and therefore, temper rolling afterwards and the manufacturing condition of low-temperature heat treatment depart from the top condition in the present invention.
The platings such as plating can be implemented to terminating the cold rolled annealed plate after annealing operation.As plating, can enumerate: pure zinc plating, the Zn based alloy plating that with the addition of alloying element using zinc as principal constituent or Al or with the addition of the Al system alloy plating process etc. of alloying element using Al as principal constituent.
Then, temper rolling operation is implemented to the cold rolled annealed plate (plating plate) terminating the cold rolled annealed plate after annealing operation or implement plating further.
In temper rolling operation, the temper rolling for the purpose of shape correction, surfaceness adjustment etc. is implemented to cold rolled annealed plate or plating plate or flattens processing.Temper rolling or the elongation flattened in processing are set as the scope of 0.2 ~ 1.0%.When elongation is less than 0.2%, shape correction cannot be realized, surfaceness regulates such expectation object.On the other hand, elongation increase and more than 1.0% time, yield-point increases, and when being configured as such as outer plate panel, the surface quality such as facial disfigurement reduces.Therefore, the elongation in temper rolling is defined as 0.2 ~ 1.0%.It should be noted that, during temper rolling and leveling are processed, form processing is different, but confirms that its effect is significantly not different.
Cold rolled annealed plate after temper rolling operation or plating plate are implemented further to the thermal treatment under low temperature.In order to have ageing resistance and sinter-hardened property concurrently, the low-temperature heat treatment importantly implemented after temper rolling operation.
In the present invention, low-temperature heat treatment is set as the thermal treatment keeping 10 minutes ~ 10 hours at the temperature of 70 ~ 140 DEG C of scopes.
When thermal treatment temp is lower than 70 DEG C, the reduction of elongation at yield rate is few, on the other hand, during more than 140 DEG C, again produces elongation at yield rate.By the temper rolling of above-mentioned scope, after just carrying out temper rolling, there is a little elongation at yield rate, but by implementing thermal treatment in the temperature range of 70 ~ 140 DEG C, elongation at yield rate reduces.About the detailed mechanism of this phenomenon, be still not clear at present, but the present inventor infer be dislocation by introducing when C and temper rolling interaction and elongation at yield rate is reduced.
In the present invention, at the temperature in above-mentioned scope, when the hold-time is less than 10 minutes, the interaction of the dislocation of C and introducing does not give full play to, and elongation at yield rate remains, and therefore, the surface quality after processing reduces.On the other hand, when keeping for a long time more than 10 hours, the dislocation of introducing and C fix strongly, and therefore, elongation at yield rate increases again.In addition, long maintenance can hinder productivity.For the foregoing reasons, the thermal treatment after temper rolling operation is set as the process keeping 10 minutes ~ 10 hours at the temperature of 70 ~ 140 DEG C of scopes.
Below, further the present invention is specifically described based on embodiment.
Embodiment
Utilize conventional smelting furnace and converter to carry out melting on the molten steel of the composition shown in table 1, make steel billet (the former material of steel: wall thickness 250mm) by conventional continuous metal cast process.By these heating steel billets to 1250 DEG C, carry out roughing and the base that laminates.Then, under the conditions shown in Table 2 finish rolling implemented to these thin slabs and makes hot-rolled sheet, coiling into web-like.Then, cleanup acid treatment is implemented to the hot-rolled sheet coiling into web-like, after removing surface scale, the cold rolling process of the condition shown in further enforcement table 2 and make cold-reduced sheet.
Implement under the conditions shown in Table 2 further to utilize the anneal of continuous annealing production line to these cold-reduced sheets and make the annealing operation of cold rolled annealed plate.Then, the temper rolling operation of carrying out temper rolling is implemented under the conditions shown in Table 2 to these cold rolled annealed plates, implements thermal treatment under the conditions shown in Table 2 further.
Cut test film from obtained cold rolled annealed plate, implement structure observation, tension test, sinter-hardened test, aging test, investigate microtexture, tensile properties, sinter-hardened property, ageing resistance.Test method is as described below.
(1) structure observation
Structure observation test film is cut from obtained cold rolled annealed plate, the section (L section) parallel with rolling direction is ground, carry out nital corrosion, by opticmicroscope (multiplying power: 400 times) tissues observed, shooting, by image analysis, obtain the area occupation ratio of ferritic phase, as volume fraction.In optical texture photo, the intragranular of ferritic phase is not corroded and presents white.When there is the second-phase of the corrosion blackening beyond ferritic phase, by scanning electronic microscope (multiplying power: 3000 times) tissues observed, shooting, by image analysis, obtains the volume fraction of second-phase.In scanning electronic microscope macrograph, ferritic phase presents the contrast of slightly black, and martensitic phase forms the particle of the contrast presenting white, in addition, carbide is generated as the region of stratiform or some column-shaped as perlite and Bainite Phases of Some.But, do not comprise the tiny second-phase of diameter less than 0.2 μm.
(2) tension test
To make the draw direction of test film be that the mode in the direction (C direction) of 90 ° cuts JIS5 test film (GL:50mm) relative to rolling direction from obtained cold rolled annealed plate, based on the regulation of JISZ2241, implement tension test with the pinblock speed of 10mm/ minute, obtain tensile properties (tensile strength TS, elongation El).
(3) sinter-hardened test
To make the draw direction of test film be that the mode in the direction (C direction) of 90 ° cuts JIS5 test film (GL:50mm) relative to rolling direction from obtained cold rolled annealed plate, after this test film being given to the prestrain of 2%, implement the process being equivalent to application sintering of 170 DEG C × 20 minutes.Then, redraw, obtain the upper yield point after thermal treatment (yielding stress).Obtain the most heavily stressed difference under the upper yield point after obtained thermal treatment and prestrain, as sinter-hardened amount (BH amount).
(4) aging test
To make the draw direction of test film be that the mode in the direction (C direction) of 90 ° cuts JIS5 test film (GL:50mm) relative to rolling direction from obtained cold rolled annealed plate, keep 6 months under aging temp (38 DEG C).After maintenance, implement tension test in the same manner as (2) tension test, obtain elongation at yield rate.Using elongation at yield rate be less than 0.8% situation be evaluated as zero as ageing resistance is excellent.Situation is in addition designated as ×.
Obtained result is shown in table 3.
The present invention's example all become there is ferrite single phase structure, tensile strength TS is 340 ~ 440MPa level, have the elongation El of more than 40%, excellent processability and BH amount are more than 30MPa and elongation at yield rate after demonstrating excellent sinter-hardened property and then ageing treatment are low to moderate less than 0.8%, ageing resistance is excellent high strength cold rolled steel plate.It should be noted that, about the present invention's example, carried out the investigation of r value in addition, confirmed the high level can guaranteeing more than 1.6 in average r value.On the other hand, depart from the comparative example of scope of the present invention, tissue is containing the second-phase beyond amount of ferrite phase, elongation El is low, plasticity reduces, or BH amount is less than 30MPa, and sinter-hardened property reduces, or the elongation at yield rate produced after ageing treatment more than 0.8%, ageing resistance reduces.
Claims (12)
1. a manufacture method for ageing resistance and the excellent high strength cold rolled steel plate of sinter-hardened property, it comprises:
Prepare the former material of steel,
The former material of this steel is implemented that finish rolling end temp is set as more than 860 DEG C, the hot rolling of batching under the coiling temperature of 550 ~ 720 DEG C of scopes and make hot-rolled sheet,
Implement cold rolling to this hot-rolled sheet and make cold-reduced sheet,
This cold-reduced sheet is implemented under annealing temperature is the temperature of 760 ~ 900 DEG C of scopes after soaking, is made until the average cooling rate of 300 DEG C is that cold rolled annealed plate is made in more than the 10 DEG C/sec annealing cooled,
To this cold rolled annealed plate with 0.2 ~ 1.0% elongation implement temper rolling or leveling processing,
Implement the thermal treatment keeping 10 minutes ~ 10 hours at the temperature of 70 ~ 140 DEG C of scopes,
The former material of described steel has following composition: in mass % containing more than C:0.0010% and less than 0.0080%, below Si:1.0%, more than Mn:0.1% and less than 1.8%, below P:0.100%, below S:0.03%, more than sol.Al:0.01% and less than 0.50%, below N:0.0050%, more than Nb:0.005% and less than 0.050%, Nb content and C content meet following (1) formula, and be selected from by below Co:0.05%, below Cu:0.05%, below Cr:0.05%, at least one in the group that below Mo:0.05% forms meets following (2) formula, surplus comprises Fe and inevitable impurity,
0.3≤(Nb/92.9)/(C/12)≤0.9…(1)
0.5≤[(Co/58.9)+(Cu/63.5)+(Cr/52.0)+(Mo/95.9)]/(C/12)≤5.0…(2)
Wherein, Nb, C, Co, Cu, Cr, Mo: the quality % content of each element.
2. the manufacture method of high strength cold rolled steel plate as claimed in claim 1, wherein, the former material of described steel, on the basis of described composition, contains below B:0.0050% in mass % further.
3. the manufacture method of high strength cold rolled steel plate as claimed in claim 1, wherein, described cold rolling be with more than 50% and the draft of less than 85% enforcement cold rolling.
4. the manufacture method of high strength cold rolled steel plate as claimed in claim 2, wherein, described cold rolling be with more than 50% and the draft of less than 85% enforcement cold rolling.
5. the manufacture method of high strength cold rolled steel plate as claimed in claim 1, wherein, described cold rolled annealed plate has ferrite single phase structure.
6. the manufacture method of high strength cold rolled steel plate as claimed in claim 2, wherein, described cold rolled annealed plate has ferrite single phase structure.
7. the manufacture method of high strength cold rolled steel plate as claimed in claim 3, wherein, described cold rolled annealed plate has ferrite single phase structure.
8. the manufacture method of high strength cold rolled steel plate as claimed in claim 4, wherein, described cold rolled annealed plate has ferrite single phase structure.
9. the manufacture method of the high strength cold rolled steel plate according to any one of claim 1 ~ 8, wherein, implements plating to described cold rolled annealed plate.
10. the manufacture method of the high strength cold rolled steel plate according to any one of claim 1 ~ 8, wherein, described cold-rolled steel sheet is the elongation at yield rate after the timeliness under normal temperature is the cold-rolled steel sheet of less than 0.8%.
The manufacture method of 11. high strength cold rolled steel plates according to any one of claim 1 ~ 8, wherein, described cold-rolled steel sheet be sinter-hardened after yielding stress increasing amount be the cold-rolled steel sheet of more than 30MPa.
The manufacture method of 12. high strength cold rolled steel plates according to any one of claim 1 ~ 8, wherein, the cold-rolled steel sheet of described cold-rolled steel sheet to be tensile strength be 340 ~ 440MPa.
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| JP2011268799 | 2011-12-08 | ||
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| JP2012211625A JP5310919B2 (en) | 2011-12-08 | 2012-09-26 | Method for producing high-strength cold-rolled steel sheets with excellent aging resistance and seizure curability |
| JP2012-211625 | 2012-09-26 | ||
| PCT/JP2012/007772 WO2013084478A1 (en) | 2011-12-08 | 2012-12-04 | Method for manufacturing high-strength cold-rolled steel sheet having excellent aging resistance and bake hardenability |
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| KR101607011B1 (en) * | 2014-09-26 | 2016-03-28 | 현대제철 주식회사 | Steel sheet and method of manufacturing the same |
| CN106906418A (en) * | 2015-12-23 | 2017-06-30 | 本钢板材股份有限公司 | The processing method that a kind of automobile hardens high-strength steel with 180BH cold rolling bakings |
| CN106906419A (en) * | 2015-12-23 | 2017-06-30 | 本钢板材股份有限公司 | A kind of automobile 220BH cold rolling bakings harden high-strength steel |
| CN106906417A (en) * | 2015-12-23 | 2017-06-30 | 本钢板材股份有限公司 | The processing method that a kind of automobile hardens high-strength steel with 220BH cold rolling bakings |
| CN106906416A (en) * | 2015-12-23 | 2017-06-30 | 本钢板材股份有限公司 | A kind of automobile 180BH cold rolling bakings harden high-strength steel |
| CN106756554A (en) * | 2016-12-19 | 2017-05-31 | 本钢板材股份有限公司 | A kind of cold rolling baking hardened steel of resistance to timeliness 180BH and its production method |
| CN106702266A (en) * | 2016-12-19 | 2017-05-24 | 本钢板材股份有限公司 | Ageing-resistant cold-rolled bake-hardening steel 220 BH and production method thereof |
| KR102031449B1 (en) * | 2017-12-24 | 2019-10-11 | 주식회사 포스코 | Zinc-based metal plated steel sheet having excellent anti-aging property at room temperature and bake hardenability, and manufacturing method for the same |
| KR102064962B1 (en) * | 2017-12-24 | 2020-02-11 | 주식회사 포스코 | Cold rolled steel sheet and hot dip zinc-based plated steel sheet having excellent bake hardenability and corrosion resistance, and method for manufacturing the same |
| KR101988773B1 (en) * | 2017-12-26 | 2019-06-12 | 주식회사 포스코 | Cold-rolled steel sheet having excellent anti-aging properties and workability, and manufacturing method thereof |
| TWI655294B (en) * | 2018-02-07 | 2019-04-01 | 中國鋼鐵股份有限公司 | Method for decreasing arc value of slit steel sheet |
| CN110643894B (en) * | 2018-06-27 | 2021-05-14 | 宝山钢铁股份有限公司 | Ultra-high strength hot rolled steel sheet and steel strip having good fatigue and hole expansion properties, and method for manufacturing same |
| CN109161814B (en) * | 2018-08-30 | 2020-10-02 | 唐山钢铁集团有限责任公司 | Ultra-low carbon baking hardened steel plate and production method thereof |
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| KR20140098192A (en) | 2014-08-07 |
| WO2013084478A1 (en) | 2013-06-13 |
| JP2013139624A (en) | 2013-07-18 |
| CN103975082A (en) | 2014-08-06 |
| KR101607041B1 (en) | 2016-03-28 |
| JP5310919B2 (en) | 2013-10-09 |
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