JP5187320B2 - Cold rolled steel sheet manufacturing method - Google Patents

Description

  The present invention relates to a method for manufacturing a cold-rolled steel sheet. More specifically, the present invention relates to a method for producing a high-tensile cold-rolled steel sheet that is used after being formed into various shapes by press working or the like, and in particular, a method for producing a high-tensile cold-rolled steel sheet excellent in ductility and stretch flangeability. About.

  Now that the industrial technology field is highly divided, materials used in each technical field are required to have special and high performance. For example, even cold-rolled steel sheets used by press forming are required to have better formability with the diversification of press shapes. In addition, high strength is required, and application of high-tensile cold-rolled steel sheets is being studied. In particular, regarding automotive steel sheets, the demand for thin-walled, high-formability, high-tensile cold-rolled steel sheets has been remarkably increasing in order to reduce the weight of the vehicle body and improve fuel efficiency in consideration of the global environment. In press molding, since the thinner the steel sheet used, the easier it is to crack and wrinkle, a steel sheet with better ductility and stretch flangeability is required. However, these press formability and high strength of the steel sheet are contradictory characteristics, and it is difficult to satisfy these characteristics at the same time.

Until now, as a method for improving the press formability of a high-tensile cold-rolled steel sheet, many techniques relating to micronization of the microstructure have been proposed. For example, Patent Document 1 discloses a method for producing an ultrafine-grained high-strength hot-rolled steel sheet that performs rolling with a total rolling reduction of 80% or more in a temperature range near the Ar ₃ point in a hot rolling process. No. 2 discloses a method for producing ultrafine-grained ferritic steel in which rolling at a rolling reduction of 40% or more is continuously performed in the hot rolling step.

However, methods such as these techniques in which large rolling is performed in the hot rolling process are difficult to apply to industrial production because an excessive load is applied to the rolling mill. In addition, there is no description about a method for finely granulating a cold-rolled steel sheet, and according to the study by the present inventors, a fine-grained hot-rolled steel sheet obtained by large rolling is used as a base material, and cold rolling and When annealing is performed, crystal grains are easily coarsened, and it is difficult to obtain a cold-rolled steel sheet having excellent press formability. In particular, in the production of a dual-phase cold-rolled steel sheet having a metal structure consisting of ferrite and a low-temperature transformation generation phase that needs to be annealed in a high temperature range of Ac ₁ point or more, coarsening of crystal grains is remarkable. The advantage of the dual-phase cold-rolled steel sheet that is excellent in ductility cannot be enjoyed.

  Patent Document 3 discloses a method for producing a hot-rolled steel sheet having ultrafine grains, in which a reduction in a dynamic recrystallization region is performed by a reduction pass of 5 stands or more in a hot rolling process. However, it is necessary to extremely reduce the temperature drop during hot rolling, and it is difficult to carry out with normal hot rolling equipment. Moreover, although the example which performed cold rolling and annealing after hot rolling is shown, the balance of tensile strength and hole expansibility is bad, and press formability is inadequate.

  Regarding a method for finely granulating a cold-rolled steel sheet, Patent Document 4 discloses a technique of containing a large amount of Ti or Nb and finely pulverizing ferrite in an annealing process. A duplex steel sheet in which martensite and bainite are dispersed in fine ferrite is obtained, the yield ratio is low, the shape freezing property is improved, and the balance between strength and ductility and the balance between strength and stretch flangeability are achieved. Although it can be improved, it is difficult to ensure both ductility and stretch flangeability at the same time. In addition, the addition of Ti and Nb not only increases the production cost, but austenite grains become coarse when annealed at a high temperature, so that the appropriate temperature range for annealing is narrow and it is difficult to ensure production stability.

Patent Document 5, subjected at least once before the process of rapid cooling after heating to cold rolling after Ae ₁ point or more Ae ₃ point or less of the temperature and further maintaining the temperature below ₃ points or more ₁ point Ae Ae quenching A method is disclosed in which a two-phase high-strength steel sheet is finely granulated by annealing, and in Patent Document 6, a hot-rolled steel sheet is subjected to heat treatment at 600 ° C. or higher and Ac _one point or lower, and then cold-rolled and annealed. And a method of making a two-phase high-tensile steel sheet into a fine grain is disclosed. In these methods, since a step of performing pretreatment or heat treatment is added, productivity deterioration and production cost increase are significant.

  In Patent Document 7, immediately after hot rolling, it is rapidly cooled to 720 ° C. or less and held in a temperature range of 600 to 720 ° C. for 2 seconds or more, and the obtained hot-rolled steel sheet is subjected to cold rolling and annealing and has a small particle size distribution. A method for producing a cold-rolled steel sheet having a fine grain structure is disclosed.

JP 58-123823 A JP 59-229413 A Japanese Patent Laid-Open No. 11-152544 JP 2004-250774 A JP 2004-232022 A JP 2005-213603 A International Publication No. 2007/15541

  The technique disclosed in Patent Document 7 described above is a fine grain structure having a small particle size distribution by not subjecting the processing strain accumulated in austenite to the ferrite transformation after the hot rolling is completed, and by transforming the processing strain as a driving force. Is an excellent invention in which excellent ductility and thermal stability are obtained. However, as a result of repeated studies by the present inventors, depending on the chemical composition and production conditions of the steel, after cold rolling and annealing, high strength, good ductility and good stretch flangeability cannot be secured at the same time. Turned out to be.

  The present invention has been made to solve such problems, and more specifically, the problem is to provide a method for producing a high-tensile cold-rolled steel sheet having excellent ductility and stretch flangeability. It is.

  The present inventors conducted a detailed investigation on the influence of chemical composition and production conditions on the mechanical properties of high-tensile cold-rolled steel sheets. In this specification, “%” in the content of each element in the chemical composition means mass%.

  A series of test steels is mass%, C: less than 0.10%, Si: 2.0% or less, Mn: 1.50% or more and 3.50% or less, P: 0.10% or less, S: 0.010% or less, sol. It had a chemical composition consisting of Al: 0.10% or less, N: 0.010% or less, the balance Fe and impurities.

A slab having such a chemical composition is heated to 1200 ° C., and then hot-rolled to a sheet thickness of 2.0 mm in a temperature range of ₃ or more points of Ar. After hot rolling, it is 720 ° C. or less under various cooling conditions. After cooling to the temperature range, air cooling for 5 to 10 seconds, cooling to various temperatures at a cooling rate of 90 ° C./s or less, setting this as the coiling temperature, and charging it into an electric heating furnace maintained at the same temperature Then, after holding for 30 minutes, the furnace was cooled at a cooling rate of 20 ° C./h to simulate slow cooling after winding. The obtained hot-rolled steel sheet was pickled and cold-rolled to a sheet thickness of 1.0 mm at a rolling rate of 50%. Using the continuous annealing simulator, the obtained cold-rolled steel sheet was heated to various temperatures, subjected to soaking treatment for 95 seconds, and then annealed under various conditions.

  A specimen for structure observation was collected from the annealed cold-rolled steel sheet, and the longitudinal section parallel to the rolling direction was polished. Then, using a scanning electron microscope (SEM), 1/4 of the sheet thickness from the steel sheet surface. The metal structure was observed at the depth position. In addition, a tensile test piece was taken in parallel with the rolling direction to perform a tensile test. Furthermore, stretch flangeability was evaluated by a hole expansion test. In the hole expansion test, a punched hole with a diameter of 10 mm is formed with a clearance of 12.5%, the punched hole is expanded with a conical punch with a tip angle of 60 °, and the expansion rate of the hole when a crack that penetrates the plate thickness occurs is measured. did.

As a result of these preliminary tests, the following findings (A) to (F) were obtained.
(A) A hot-rolled steel sheet manufactured through a so-called immediate quenching process in which water quenching is performed immediately after hot rolling, specifically, quenching to a temperature range of 720 ° C. or less within 0.4 seconds from completion of hot rolling. When the hot-rolled steel sheet manufactured by cold-rolling is annealed by cold rolling, the ductility and stretch flangeability of the cold-rolled steel sheet improve as the annealing temperature rises, but if the annealing temperature is too high, the austenite grains become coarse, The ductility and stretch flangeability of cold-rolled steel sheets may deteriorate rapidly.

  (B) Immediately after the rapid cooling, if the coiling temperature is increased, austenite grain coarsening is suppressed when annealing is performed at a high temperature after cold rolling. The reason for this is not clear, but (a) the precipitation amount of iron carbide in the hot-rolled steel sheet increases as the coiling temperature rises, and (b) iron carbide undergoes transformation from ferrite to austenite during annealing. As the amount of precipitation of iron carbide increases, the frequency of nucleation increases and austenite becomes finer. (C) Undissolved iron carbide suppresses austenite grain growth. For this reason, it is estimated that the austenite is refined.

  (C) The effect of preventing coarsening of austenite grains accompanying an increase in the coiling temperature becomes stronger as the Si content in the steel increases. The reason for this is not clear, but (a) as the Si content increases, the iron carbide becomes finer and the number density increases. (B) This further increases the frequency of nucleation in the transformation from ferrite to austenite. (C) Moreover, it is estimated that it originates in that the grain growth suppression by undissolved iron carbide becomes strong.

(D) While suppressing the coarsening of austenite grains (Ac ₃ points-40 ° C) and soaking in the temperature range above and cooling, fine ferrite is the main phase and the low temperature transformation product phase is finely dispersed as the second phase To obtain a metallographic structure. The reason for this is not clear, but (a) ferrite produced through ferrite → austenite → ferrite transformation is made finer than ferrite before austenitization, and (b) undissolved iron carbide suppresses ferrite grain growth. It is estimated that

(E) A cold-rolled steel sheet having such a metal structure exhibits good ductility and good stretch flangeability while having high strength.
(F) Furthermore, by further cooling the constant temperature region after the soaking, better ductility and better stretch flangeability can be obtained.

From the above results, a steel containing a certain amount or more of Si is hot-rolled and then immediately cooled, wound into a coil at a high temperature, cold-rolled, and averaged at a temperature of (Ac ₃ point-40 ° C) or higher. By heating and cooling, a cold-rolled steel sheet having a structure in which the main phase is ferrite and the second phase includes a low-temperature transformation generation phase and excellent in ductility and stretch flangeability can be produced.

The present invention completed based on the above knowledge is as follows.
(1) A method for producing a cold-rolled steel sheet comprising a metallographic structure in which the main phase is ferrite and the second phase includes a low-temperature transformation generation phase, which includes the following steps (A) to (C):
(A) By mass%, C: more than 0.010% and less than 0.10%, Si: more than 0.10% and 2.0% or less, Mn: 1.50% or more and 3.50% or less, P: 0.00. 10% or less, S: 0.010% or less, sol. A slab having a chemical composition containing Al: 0.10% or less and N: 0.010% or less is subjected to hot rolling to complete rolling in a temperature range of Ar ₃ points or more to obtain a hot-rolled steel sheet, A hot rolling step in which the hot-rolled steel sheet is cooled to a temperature range of 720 ° C. or lower within 0.4 seconds after completion of the rolling and wound in a temperature range of 400 ° C. or higher;
(B) a cold rolling process in which the hot-rolled steel sheet is cold-rolled to obtain a cold-rolled steel sheet; and (C) the cold-rolled steel sheet is subjected to a soaking process in a temperature range of (Ac ₃ points-40 ° C) or higher. Annealing process.

  (2) The method for producing a cold-rolled steel sheet according to (1), wherein, in the step (C), after the soaking, cooling is performed at 50 ° C. or more at a cooling rate of less than 10 ° C./s.

  (3) The chemical composition is one or more selected from the group consisting of Ti: less than 0.040%, Nb: less than 0.030%, and V: 0.50% or less in terms of mass%. The method for producing a cold-rolled steel sheet according to (1) or (2) above, characterized in that

  (4) The chemical composition is one or more selected from the group consisting of Cr: 1.0% or less, Mo: 0.50% or less, and B: 0.010% or less in terms of mass%. The method for producing a cold-rolled steel sheet according to any one of (1) to (3) above, wherein

  (5) The chemical composition is further selected from the group consisting of Ca: 0.010% or less, Mg: 0.010% or less, REM: 0.050% or less, and Bi: 0.050% or less in terms of mass%. The method for producing a cold-rolled steel sheet according to any one of (1) to (4) above, wherein the method comprises one or more kinds.

  According to the present invention, a high-tensile cold-rolled steel sheet having sufficient ductility and stretch flangeability that can be applied to processing such as press forming can be obtained. The present invention greatly contributes to the development of industries, such as contributing to the solution of global environmental problems through weight reduction of automobile bodies.

  The metallographic structure and chemical composition of the high-tensile cold-rolled steel sheet according to the present invention and the rolling and annealing conditions in the production method capable of producing the steel sheet efficiently, stably and economically will be described in detail below.

1. Metal structure The high-tensile cold-rolled steel sheet of the present embodiment has a composite structure in which the main phase is fine ferrite and the second phase includes a low-temperature transformation generation phase. This is because it is suitable for increasing the strength without impairing the ductility. Here, the low temperature transformation generation phase refers to a phase and structure produced by low temperature transformation such as martensite and bainite. Other than these, acicular ferrite, bainitic ferrite and tempered martensite are exemplified. This low temperature transformation product phase may contain two or more phases and structures, such as martensite and bainite. The main phase means a phase or structure having the maximum volume fraction, and the second phase means a phase and structure other than the main phase. When the low temperature transformation product phase includes two or more phases and structures, the sum of the volume fractions of these phases and tissues is defined as the volume fraction of the low temperature transformation product phase.

  In order to improve ductility and stretch flangeability, the ferrite volume fraction is preferably 80.0% or more. More preferably, it is 85.0% or more, and particularly preferably 90.0% or more. On the other hand, if the volume fraction of ferrite is excessive, the tensile strength decreases. Therefore, the volume fraction of ferrite is preferably less than 98.0%. More preferably it is less than 95.0%, particularly preferably less than 92.0%. In order to further improve the ductility and stretch flangeability, the average crystal grain size of ferrite is preferably less than 5.0 μm. More preferably, it is less than 4.0 micrometers, Most preferably, it is less than 3.0 micrometers.

  In order to increase the tensile strength, the volume ratio of the low temperature transformation product phase is preferably more than 2.0%. More preferably, it is more than 4.0%, particularly preferably more than 6.0%. On the other hand, when the volume ratio of the low-temperature transformation generation phase is excessive, the ductility and stretch flangeability deteriorate significantly. Therefore, the volume fraction of the low temperature transformation product phase is preferably less than 20.0%. More preferably, it is less than 15.0%, particularly preferably less than 10.0%.

  In order to improve ductility and shape freezing property, the low-temperature transformation generation phase preferably contains martensite. In this case, the volume ratio of martensite in the entire structure is preferably more than 1.0%, more preferably more than 2.0%, and particularly preferably more than 3.0%. On the other hand, when the volume ratio of martensite becomes excessive, stretch flangeability deteriorates. For this reason, the volume ratio of the martensite phase in the entire structure is preferably less than 15.0%, and more preferably less than 10.0%.

  In order to improve stretch flangeability, the low temperature transformation generation phase preferably contains bainite. In this case, the volume fraction of bainite in the entire structure is preferably more than 1.0%, more preferably more than 2.0%, and particularly preferably more than 3.0%. On the other hand, when the volume fraction of bainite becomes excessive, ductility and shape freezing property deteriorate. For this reason, the volume fraction of bainite in the entire structure is preferably less than 15.0%, more preferably less than 10.0%.

  As the second phase, residual austenite may be included in addition to the low-temperature transformation generation phase. When residual austenite is included, ductility is improved. However, when the volume ratio of retained austenite becomes excessive, stretch flangeability deteriorates. For this reason, the volume fraction of retained austenite is preferably less than 15.0%, more preferably less than 10.0%, and particularly preferably less than 8.0%. In order to more reliably obtain the effect of improving ductility due to retained austenite, the volume ratio of retained austenite is preferably more than 1.0%, more preferably more than 2.0%, and more than 3.0%. It is particularly preferred.

  In the present embodiment, in the case of a cold-rolled steel sheet, the position of a quarter depth of the sheet thickness from the surface of the steel sheet, and in the case of a plated steel sheet, the steel sheet that is the base material from the boundary between the steel sheet that is the base material and the plating layer. The above-described metal structure is defined at a position of a quarter depth of the plate thickness.

As a mechanical property that can be realized based on the above-described features on the metal structure, the steel sheet of the present embodiment preferably has a tensile strength (TS) of 590 MPa or more, and 780 MPa or more in order to ensure shock absorption. More preferably. In order to ensure ductility, TS is preferably less than 1180 MPa, more preferably less than 980 MPa. From the viewpoint of press formability, when the total elongation of the steel sheet is El and the hole expansion ratio measured according to the Japan Iron and Steel Federation Standard JFST1001 is λ, the value of TS ² × E1 × λ is 9.0 ×. It is preferably 10 ⁸ MPa ² % ² or more, more preferably 1.0 × 10 ⁹ MPa ² % ² or more, and particularly preferably 1.1 × 10 ⁹ MPa ² % ² or more. From the viewpoint of shape freezeability, the yield ratio is preferably less than 80%, more preferably less than 75%, and particularly preferably less than 70%.

2. Chemical composition of steel C: more than 0.010% and less than 0.10% When the C content is 0.010% or less, it is difficult to obtain the above metal structure. Therefore, the C content is more than 0.010%. Preferably it is more than 0.020%, more preferably more than 0.030%, particularly preferably more than 0.04%. On the other hand, when the C content is 0.10% or more, not only the metal structure is hardly obtained, but also the stretch flangeability of the steel sheet is impaired and the weldability is also deteriorated. Therefore, the C content is less than 0.10%. Preferably it is less than 0.08%, more preferably less than 0.06%, particularly preferably less than 0.05%.

Si: more than 0.10% and not more than 2.0% Si has an effect of improving ductility and stretch flangeability through suppression of austenite grain growth during annealing. When the Si content is 0.10% or less, it is difficult to obtain the effect by the above-described action. Therefore, the Si content is more than 0.10%. Preferably it is more than 0.25%, more preferably more than 0.50%, particularly preferably more than 0.60%. On the other hand, if the Si content exceeds 2.0%, the surface properties of the steel sheet deteriorate. Furthermore, chemical conversion property and plating property are remarkably deteriorated. Therefore, the Si content is 2.0% or less. Preferably it is 1.50% or less, More preferably, it is 1.25% or less, Most preferably, it is less than 1.00%.

Mn: 1.50% or more and 3.50% or less Mn has an effect of improving the hardenability of steel and is an effective element for obtaining the above metal structure. If the Mn content is less than 1.50%, it is difficult to obtain the above metal structure. Therefore, the Mn content is 1.50% or more. Preferably it is more than 2.10%, more preferably more than 2.20%, particularly preferably more than 2.30%. On the other hand, if the Mn content exceeds 3.50%, the volume fraction of ferrite is too small and ductility deteriorates, and the bendability is impaired due to segregation of Mn, and further, the material cost increases. Therefore, the Mn content is 3.50% or less. Preferably it is less than 3.00%, more preferably less than 2.70%, particularly preferably less than 2.50%.

P: 0.10% or less P is an element contained in steel as an impurity, and segregates at grain boundaries to embrittle the steel. For this reason, the smaller the P content, the better. Therefore, the P content is 0.10% or less. Preferably it is less than 0.020%, more preferably less than 0.015%.

S: 0.010% or less S is an element contained in steel as an impurity, and forms sulfide inclusions to deteriorate stretch flangeability. For this reason, the smaller the S content, the better. Therefore, the S content is 0.010% or less. Preferably it is 0.005% or less, More preferably, it is less than 0.003%, Most preferably, it is 0.001% or less.

sol. Al: 0.10% or less Al has a function of deoxidizing molten steel. In the present invention, since Si having a deoxidizing action is contained in the same manner as Al, Al is not necessarily contained. When it is contained for the purpose of deoxidation, sol. Even if the content of Al exceeds 0.10%, the effect is saturated and uneconomical. The Al content is 0.10% or less. Preferably it is 0.05% or less, More preferably, it is 0.02% or less. In order to obtain the effect of deoxidation by Al more reliably, sol. The Al content is preferably 0.005% or more.

N: 0.010% or less N is an element contained in steel as an impurity, and deteriorates ductility. For this reason, the smaller the N content, the better. Therefore, the N content is 0.010% or less. Preferably it is 0.006% or less, More preferably, it is 0.005% or less.

The steel plate according to the present embodiment may contain the elements listed below as optional elements.
One or more selected from the group consisting of Ti: less than 0.040%, Nb: less than 0.030% and V: 0.50% or less Ti, Nb and V precipitate as carbides or nitrides. , Has the effect of suppressing the austenite coarsening during annealing and improving ductility and stretch flangeability. Therefore, you may contain 1 type, or 2 or more types of these elements. However, even if it contains excessively, the effect by the said effect | action will be saturated and it will become uneconomical. In addition, the recrystallization temperature increases, the metal structure of the cold-rolled steel sheet becomes non-uniform, and the stretch flangeability is also impaired. Furthermore, the precipitation amount of carbide or nitride increases, the yield ratio increases, and the shape freezing property also deteriorates. Therefore, the Ti content is less than 0.040%, the Nb content is less than 0.030%, and the V content is 0.50% or less. The Ti content is preferably less than 0.025%, more preferably less than 0.020%, the Nb content is preferably less than 0.020%, more preferably 0.015% or less, and the V content is Preferably it is 0.30% or less. In order to more reliably obtain the effect of the above action, it is preferable to satisfy any of Ti: 0.005% or more, Nb: 0.005% or more, and V: 0.010% or more. When Ti is contained, the Ti content is more preferably 0.010% or more, and when Nb is contained, the Nb content is more preferably 0.010% or more.

One or more selected from the group consisting of Cr: 1.0% or less, Mo: 0.50% or less, and B: 0.010% or less Cr, Mo, and B improve the hardenability of steel. It is an element effective in obtaining the above metal structure. Therefore, you may contain 1 type, or 2 or more types of these elements. However, even if it contains excessively, the effect by the said effect | action will be saturated and it will become uneconomical. Therefore, the Cr content is 1.0% or less, the Mo content is 0.50% or less, and the B content is 0.010% or less. The Cr content is preferably 0.50% or less, the Mo content is preferably 0.20% or less, and the B content is preferably 0.0030% or less. In order to more reliably obtain the effect of the above action, it is preferable to satisfy any of Cr: 0.20% or more, Mo: 0.05% or more, and B: 0.0010% or more.

Ca, Mg and REM selected from the group consisting of Ca: 0.010% or less, Mg: 0.010% or less, REM: 0.050% or less, and Bi: 0.050% or less By adjusting the shape of the inclusions, Bi has the effect of improving stretch flangeability by refining the solidified structure. Therefore, you may contain 1 type, or 2 or more types of these elements. However, even if it contains excessively, the effect by the said effect | action will be saturated and it will become uneconomical. Therefore, the Ca content is 0.010% or less, the Mg content is 0.010% or less, the REM content is 0.050% or less, and the Bi content is 0.050% or less. Preferably, the Ca content is 0.0020% or less, the Mg content is 0.0020% or less, the REM content is 0.0020% or less, and the Bi content is 0.010% or less. In order to obtain the above action more reliably, it is preferable to satisfy any of Ca: 0.0005% or more, Mg: 0.0005% or more, REM: 0.0005% or more, and Bi: 0.0010% or more. . Note that REM means a rare earth element and is a generic name for a total of 17 elements of Sc, Y and lanthanoid, and the REM content is the total content of these elements.

3. Manufacturing conditions The steel having the above-mentioned chemical composition is melted by a known means and then made into a steel ingot by a continuous casting method, or a method of rolling into pieces after making it into an ingot by any casting method, etc. It is made into a billet. In the continuous casting process, in order to suppress the occurrence of surface defects due to inclusions, it is preferable to cause an external additional flow such as electromagnetic stirring in the molten steel in the mold. The steel ingot or steel slab may be reheated once it has been cooled and subjected to hot rolling. The steel ingot in the high temperature state after continuous casting or the steel slab in the high temperature state after partial rolling is used as it is. Alternatively, it may be kept hot or subjected to auxiliary heating for hot rolling. In the present specification, such steel ingots and steel slabs are collectively referred to as “slabs” as materials for hot rolling. The temperature of the slab to be subjected to hot rolling is preferably less than 1250 ° C. and more preferably 1200 ° C. or less in order to prevent coarsening of austenite. The lower limit of the temperature of the slab to be subjected to hot rolling is not particularly limited as long as it is a temperature at which hot rolling can be completed at Ar ₃ points or more as described later.

Hot rolling is completed in a temperature range of Ar ₃ or more in order to refine the structure of the hot-rolled steel sheet by transforming austenite after completion of rolling. When the temperature at the completion of rolling is low, the texture of the hot-rolled steel sheet develops, and the stretch flangeability after cold rolling and annealing deteriorates. For this reason, it is preferable that the hot rolling is completed at a temperature of (Ar ₃ points + 20 ° C.) or higher. It is more preferable to complete at a temperature of (Ar ₃ points + 30 ° C.) or higher. Moreover, when the temperature of hot rolling is too low, the rolling load increases and rolling becomes difficult. Therefore, it is preferable to complete hot rolling at 780 ° C. or higher, and more preferably at 800 ° C. or higher.

  In addition, when hot rolling consists of rough rolling and finish rolling, in order to complete finish rolling at the said temperature, you may heat a rough rolling material between rough rolling and finish rolling. At this time, it is desirable to suppress the temperature fluctuation over the entire length of the rough rolled material at the start of finish rolling to 140 ° C. or lower by heating so that the rear end of the rough rolled material is higher than the front end. Thereby, the uniformity of the product characteristic in a coil improves.

  The heating method of the rough rolled material may be performed using a known means. For example, a solenoid induction heating device is provided between the rough rolling mill and the finish rolling mill, and the heating temperature rise is controlled based on the temperature distribution in the longitudinal direction of the rough rolled material on the upstream side of the induction heating device. May be.

  The amount of hot rolling reduction is preferably as high as possible in order to increase the amount of processing strain introduced into austenite and promote the refinement of the structure of the hot-rolled steel sheet. However, if the reduction amount becomes too high, the rolling load increases and rolling becomes difficult. Therefore, it is preferable that the reduction amount of the final one pass of hot rolling is more than 15% and less than 50% in terms of sheet thickness reduction rate, and more preferably more than 20% and less than 40%.

  After hot rolling, it is rapidly cooled to a temperature range of 720 ° C. or less within 0.4 seconds after completion of rolling. This suppresses the release of processing strain introduced into austenite by rolling, transforms austenite using processing strain as a driving force, refines the structure of hot-rolled steel sheet, ductility and stretch flangeability after cold rolling and annealing It is for improving. Preferably, it is rapid cooling to a temperature range of 720 ° C. or less within 0.3 seconds after completion of rolling, and more preferably, it is rapidly cooled to a temperature range of 720 ° C. or less within 0.2 seconds after completion of rolling. . In addition, since release of processing strain is suppressed as the average cooling rate during rapid cooling increases, the average cooling rate during rapid cooling is preferably set to 400 ° C./s or more, thereby further increasing the structure of the hot-rolled steel sheet. It can be miniaturized. The average cooling rate during the rapid cooling is more preferably 500 ° C./s or more, and particularly preferably 700 ° C./s or more. Note that the time from the completion of rolling to the start of rapid cooling and the cooling rate during that time do not need to be specified.

  The equipment for rapid cooling is not particularly defined, but industrially, it is preferable to use a water spray device with a high water density, and a water spray header is disposed between the rolling plate conveyance rollers, and sufficient from above and below the rolling plate. A method of injecting high-pressure water having a water density is exemplified.

  After the rapid cooling stop, the steel plate is wound in a temperature range of 400 ° C. or higher. This is because when the coiling temperature is lower than 400 ° C., iron carbide is not sufficiently precipitated in the hot-rolled steel sheet, austenite is coarsened in the annealing process, and ductility and stretch flangeability after cold rolling and annealing are impaired. Because. The winding temperature is preferably higher than 500 ° C, more preferably higher than 550 ° C, and particularly preferably higher than 600 ° C. On the other hand, when the coiling temperature is too high, the yield decreases due to scale generation. For this reason, it is preferable that winding temperature shall be less than 700 degreeC.

  The conditions from the rapid cooling stop to the winding are not particularly defined, but after the rapid cooling stop, it is preferable to hold at a temperature range of 720 to 600 ° C. for 1 second or more. Thereby, the production | generation of a fine ferrite is accelerated | stimulated. On the other hand, if the holding time becomes too long, the productivity is impaired. Therefore, the holding time in the temperature range of 720 to 600 ° C. is preferably within 10 seconds. After holding in the temperature range of 720 to 600 ° C., it is preferable to cool to the coiling temperature at a cooling rate of 20 ° C./s or more in order to prevent the generated ferrite from becoming coarse.

  The hot-rolled steel sheet produced as described above has a metal structure mainly composed of fine ferrite and containing iron carbide. In order to further suppress the coarsening of austenite during annealing and further improve the ductility and stretch flangeability of the cold-rolled steel sheet, it is preferable that the average crystal grain size of ferrite in the hot-rolled steel sheet is 3.0 μm or less, More preferably, it is 2.0 μm or less.

  The hot-rolled steel sheet is descaled by pickling or the like and then cold-rolled according to a conventional method. In cold rolling, in order to promote recrystallization to make the metal structure of the cold-rolled steel sheet uniform and improve stretch flangeability, the cold pressure ratio is preferably set to 40% or more. If the cold pressure ratio is too high, the rolling load increases and rolling becomes difficult. Therefore, the cold pressure ratio is preferably less than 70%, and more preferably less than 60%.

The steel sheet after cold rolling is annealed after being subjected to a treatment such as degreasing according to a known method, if necessary. The soaking temperature in annealing is set to (Ac ₃ points−40 ° C.) or higher. This is to refine the ferrite of the cold-rolled steel sheet and improve ductility and stretch flangeability. The soaking temperature is preferably more than (Ac ₃ points−20 ° C.), more preferably more than Ac ₃ points. However, if the soaking temperature becomes too high, austenite becomes excessively coarse during soaking, and ductility and stretch flangeability deteriorate. Therefore, the soaking temperature is preferably less than (Ac ₃ points + 100 ° C.), and more preferably less than (Ac ₃ points + 50 ° C.).

  In order to increase the volume fraction of ferrite and further improve the ductility and stretch flangeability, it is preferable to cool 50 ° C. or more from the soaking temperature at a cooling rate of less than 10 ° C./s after soaking. The cooling rate after soaking is preferably less than 5.0 ° C./s, more preferably less than 3.0 ° C./s, and particularly preferably less than 2.0 ° C./s.

  In order to further increase the volume fraction of ferrite, after soaking, it is preferable to cool at 80 ° C. or higher from the soaking temperature at a cooling rate of less than 10 ° C./s, more preferably to cool at 100 ° C. or higher. It is particularly preferable to cool at a temperature of at least ° C.

  In order to obtain a low temperature transformation generation phase, it is preferable to cool a temperature range of 650 to 450 ° C. at a cooling rate of 15 ° C./s or more and 200 ° C./s or less. A more preferable cooling rate is more than 30 ° C./s and less than 150 ° C./s, and a particularly preferable cooling rate is more than 50 ° C./s and less than 130 ° C./s. Moreover, in order to adjust the metal structure of the cold rolled steel sheet, it may be held for 60 seconds or more in a temperature range of 450 to 200 ° C. In order to increase the tensile strength, the holding temperature is preferably 400 ° C. or lower. On the other hand, in order to reduce the hardness difference between the low-temperature transformation generation phase and ferrite and improve stretch flangeability, the holding temperature is preferably 300 ° C. or higher, and more preferably 350 ° C. or higher.

  Moreover, as for the heating rate to the soaking | uniform-heating temperature in annealing, it is preferable that the temperature range of 700 degreeC or more shall be less than 10 degrees C / s. If the heating rate to reach the soaking temperature is too high, the metal structure of the cold-rolled steel sheet becomes non-uniform, and there is a possibility that the stretch flangeability is deteriorated.

  When manufacturing a plated steel sheet, the cold-rolled steel sheet manufactured by the above-described method may be electroplated or hot-plated according to a conventional method. The plating method, the chemical composition of the plating film, and the alloying treatment after plating are performed. It is not limited to the presence or absence. Examples of electroplating include electrogalvanizing and electro-Zn-Ni alloy plating. Examples of the hot dip plating include hot dip galvanizing, alloyed hot dip galvanizing, hot dip aluminum plating, hot dip Zn-Al alloy plating, hot dip Zn-Al-Mg alloy plating, hot dip Zn-Al-Mg-Si alloy plating and the like. .

In the case of producing a hot-dip galvanized steel sheet, cold rolling is performed by the above-described method, soaking at a temperature of (Ac ₃ points−40 ° C.) or higher, and then at a cooling rate of less than 10 ° C./s. It is preferable to cool at a temperature of at least ° C., then cool to a temperature in the temperature range of 600 to 460 ° C. at a cooling rate of at least 4 ° C./s, hold at this temperature range for at least 10 seconds, and then apply hot dip galvanization. Thereby, it becomes easy to obtain a low temperature transformation production phase. Moreover, in order to improve the corrosion resistance after coating, it is preferable to reheat after hot dip galvanizing and alloying treatment.

  The cold-rolled steel sheet and the plated steel sheet thus obtained may be subjected to temper rolling according to a conventional method. However, when the elongation rate of temper rolling is high, ductility is deteriorated. Therefore, the elongation of temper rolling is preferably 1.0% or less. A more preferable elongation is 0.5% or less.

The present invention will be described more specifically with reference to examples.
Steel having the chemical composition shown in Table 1 was melted and cast using a laboratory vacuum melting furnace. These steel ingots were made into steel pieces having a thickness of 30 mm by hot forging. The steel slab was heated to 1200 ° C. using an electric heating furnace and held for 60 minutes, and then hot rolled under the conditions shown in Table 2.

Specifically, using an experimental hot rolling mill, 6-pass rolling was performed in a temperature range of ₃ or more points of Ar, and finished to a thickness of 2 mm. The rolling reduction rate for the final pass was 22% in terms of sheet thickness reduction rate. After hot rolling, it is cooled to 650 to 680 ° C. under various cooling conditions using a water spray, allowed to cool for 6 to 10 seconds, and then cooled to various temperatures at a cooling rate of 60 ° C./s. The coiling temperature was set at an electric heating furnace maintained at the same temperature, held for 30 minutes, and then cooled to room temperature at a cooling rate of 20 ° C./h to simulate slow cooling after winding. .

  The obtained steel plate was pickled and used as a cold-rolled base material, and cold-rolled at a reduction rate of 50% to obtain a cold-rolled steel plate having a thickness of 1.0 mm. Using the continuous annealing simulator, the obtained cold rolled steel sheet was heated to 550 ° C. at a heating rate of 10 ° C./s, and then heated to various temperatures shown in Table 2 at a heating rate of 2 ° C./s. A soaking process is performed for 95 seconds, followed by primary cooling to various temperatures shown in Table 2, and secondary cooling to various temperatures shown in Table 2 with an average cooling rate from 700 ° C. being 60 ° C./s. Then, after maintaining at that temperature for 330 seconds, annealing was performed to cool to room temperature.

  From the obtained hot-rolled steel sheet, a specimen for SEM observation was collected, and after polishing a longitudinal section parallel to the rolling direction, the metal structure at the 1/4 depth position of the sheet thickness was observed from the steel sheet surface, and image processing was performed. Thus, the average crystal grain size of ferrite was measured.

  In addition, a specimen for SEM observation was collected from the annealed cold-rolled steel sheet, and after polishing the longitudinal section parallel to the rolling direction, the metal structure at the 1/4 depth position of the plate thickness was observed from the steel sheet surface. Then, the volume fraction of the ferrite and the low-temperature transformation generation phase and the average crystal grain size of the ferrite were measured by image processing. Moreover, the test piece for X-ray diffraction was extract | collected and the amount of retained austenite in the 1/4 depth position of plate | board thickness from the steel plate surface was measured by X-ray diffraction.

  Yield stress (YS), tensile strength (TS), and total elongation (El) are obtained by taking a JIS No. 5 tensile specimen along the rolling direction from the annealed cold-rolled steel sheet and conducting a tensile test. It was.

  Stretch flangeability was evaluated by measuring the hole expansion rate (λ) by the following method. A 100 mm square plate is collected from the annealed cold rolled steel sheet, a punched hole with a diameter of 10 mm is formed with a clearance of 12.5%, and the punched hole is expanded from the sag side with a conical punch with a tip angle of 60 °. The expansion rate of the hole when a crack penetrating the plate thickness was measured, and this was defined as the hole expansion rate.

  Table 3 shows the metal structure observation results and performance evaluation results of the cold-rolled steel sheet.

As for the test results (trial numbers 1, ^2, 5, ⁸ , 9, 11 to 15) for the steel sheets within the range defined by the present invention, the value of TS ² × E1 × λ is 8.7 × 10 ^8. MPa ² % ² or more, showing good ductility and stretch flangeability. All of the test results (trial numbers 1, 5, 8, 9, 13 to 15) cooled at a cooling rate of less than 10 ° C. after soaking had a value of TS ² × E1 × λ of 9.5 ×. 10 ⁸ MPa ² % ² or more, and particularly good ductility and stretch flangeability were exhibited.

As for the test results (trial numbers 3, 4, 6, 7, and 10) for steel plates whose steel composition or manufacturing method deviates from the range specified by the present invention, the value of TS ² × El × λ is 6.8. × 10 ⁸ MPa ² % ² or less, and the ductility and stretch flangeability were inferior.

  Specifically, in the test using Steel A (Trial No. 3) and the test using Steel B (Trial No. 6), the time from the completion of hot rolling to the rapid cooling stop is too long. Ferrite is coarse and ductility and stretch flangeability are poor. In the test using steel A (Trial No. 4), since the soaking temperature during annealing is too low, the ferrite of the cold-rolled steel sheet is coarse, and the ductility and stretch flangeability are poor. In the test using Steel B (Trial No. 7), since the coiling temperature is too low, the ferrite of the cold-rolled steel sheet is coarse and the ductility and stretch flangeability are poor. In the test using steel E (trial number 10), since the Si content in the steel is small, the ferrite of the cold-rolled steel sheet is coarse and the ductility and stretch flangeability are poor.

Claims (5)

A method for producing a cold-rolled steel sheet having a metal structure in which the main phase is ferrite and the second phase includes a low-temperature transformation generation phase, which includes the following steps (A) to (C):
(A) By mass%, C: more than 0.010% and less than 0.10%, Si: more than 0.10% and 2.0% or less, Mn: 1.50% or more and 3.50% or less, P: 0.00. 10% or less, S: 0.010% or less, sol. A slab having a chemical composition containing Al: 0.10% or less and N: 0.010% or less is subjected to hot rolling to complete rolling in a temperature range of Ar ₃ points or more to obtain a hot-rolled steel sheet, A hot rolling step in which the hot-rolled steel sheet is cooled to a temperature range of 720 ° C. or lower within 0.4 seconds after completion of the rolling and wound in a temperature range of 400 ° C. or higher;
(B) a cold rolling process in which the hot-rolled steel sheet is cold-rolled to obtain a cold-rolled steel sheet; and (C) the cold-rolled steel sheet is subjected to a soaking process in a temperature range of (Ac ₃ points-40 ° C) or higher. Annealing process.   In the said process (C), it cools 50 degreeC or more with the cooling rate of less than 10 degrees C / s after the soaking process, The manufacturing method of the cold-rolled steel plate of Claim 1 characterized by the above-mentioned.   The chemical composition further contains one or more selected from the group consisting of Ti: less than 0.040%, Nb: less than 0.030%, and V: 0.50% or less by mass%. The method for producing a cold-rolled steel sheet according to claim 1 or 2, wherein the method is a thing.   The chemical composition further contains, in mass%, one or more selected from the group consisting of Cr: 1.0% or less, Mo: 0.50% or less, and B: 0.010% or less. The method for producing a cold-rolled steel sheet according to any one of claims 1 to 3, wherein the method is a thing.   The chemical composition is further selected from the group consisting of Ca: 0.010% or less, Mg: 0.010% or less, REM: 0.050% or less, and Bi: 0.050% or less in terms of mass%. The method for producing a cold-rolled steel sheet according to any one of claims 1 to 4, comprising seeds or two or more kinds.