JP2016079414A - Cold rolled steel sheet and manufacturing method therefor - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a cold rolled steel sheet good in heat spot resistance and abrasion resistance.SOLUTION: A cold rolled steel sheet contains, by mass%, 0.03 to 0.12% of C, 0 to 1.0% of Si, 0.2 to 0.8% of Mn, 0.03% or less of P, 0.03% or less of S and 0.05% or less of Al. It also contains one of 0.03 to 0.4% of Nb and 0.03 to 0.3% of V. Further each element satisfies 5×C%-Si%+Mn%-1.5×Al%<1 in a range of above described contents. The balance is Fe with inevitable impurities. An average grain diameter of carbide containing any of Nb, V and Ti as a deposition is set at 20 to 100 nm. By regulating a chemical composition and homogeneously dispersing the deposition, heat spot resistance and abrasion resistance are enhanced.SELECTED DRAWING: None

Description

  The present invention relates to a cold-rolled steel sheet used for, for example, a clutch plate and a manufacturing method thereof, and provides a cold-rolled steel sheet excellent in heat resistance and wear resistance and a manufacturing method thereof.

  In a wet multi-plate clutch of an automatic transmission, a plurality of friction plates each having a friction material formed of special paper attached to a surface thereof and separate plates in contact with the friction plates are alternately arranged. Then, the transmission of power is controlled by an operation of switching between opening and connection of the friction plate and the separate plate.

  Both the friction plate and the separate plate are ring-shaped steel plate members. In general, these friction plates and separate plates constituting the wet multi-plate clutch are collectively referred to as a clutch plate.

  The main malfunctions occurring in the separate plate are wear of the spline part (hereinafter referred to as property A), rattling due to poor positional accuracy of the spline part (hereinafter referred to as property B), friction plate. There are four known variations: roughness change due to wear on the friction surface (hereinafter referred to as property C), and generation of heat spots and non-uniform shape and material (hereinafter referred to as property D). It has been. All of these are important characteristics, but it is the most difficult to deal with defects caused by heat spots.

  When connected from the neutral state to the power transmission state in the operation of the wet multi-plate clutch, the friction plate and the clutch plate are pressed with high load at a high relative speed, and the friction plate and the clutch plate The speed decreases rapidly. The frictional heat generated at this time is rapidly input to the surface of the separate plate that becomes the sliding portion, and therefore the temperature of the surface of the separate plate is raised. This temperature rise on the surface of the separate plate is the cause of the generation of heat spots.

  And the protrusion of the heat spot part derived from the heating by frictional heat, the distortion around the heat spot, and the local material change make the frictional state in the clutch operation non-uniform. In addition, the uneven friction state causes a vicious cycle of forming a new heat spot, and the performance of the wet multi-plate clutch is significantly deteriorated.

  Here, improvement in fuel efficiency of automobiles is a very important issue in modern times, and improvement in efficiency in terms of mechanism and reduction in size and weight as a unit are very important in various components constituting the automobile.

  Further, in transmissions, improvement in efficiency, reduction in friction loss, and reduction in size and weight are required. To achieve these, it is necessary to improve the efficiency of the wet multi-plate clutch. In order to improve the wet multi-plate clutch efficiency, it is conceivable to reduce the diameter of the plate, reduce the number of plates, reduce the lubricating oil, and improve the friction coefficient by changing the friction material. However, both cause an excessive temperature rise that cannot be handled by the prior art, that is, a heat spot.

  Therefore, if the material performance of the clutch plate can be improved, there is a possibility that the efficiency of the transmission can be dramatically improved. Therefore, the steel plate used for the clutch plate is required to improve heat spot resistance.

  As techniques for improving the heat spot resistance of a steel sheet, methods described in Patent Document 1 to Patent Document 3 and the like are known.

  In Patent Document 1, a low-carbon steel is used to increase the phase transformation temperature from ferrite to austenite, thereby preventing the occurrence of phase transformation even when the plate is heated by frictional heat during clutching. A method of suppressing the occurrence of is shown.

  Patent Document 2 discloses a method of suppressing the generation of heat spots by controlling the temperature rise of the plate due to frictional heat by regulating the amount of alloying elements and improving the thermal diffusivity of the steel sheet.

  Patent Document 3 discloses a method for suppressing the generation of heat spots by using austenitic stainless steel, which is unlikely to undergo phase transformation, as a material for plates.

  Patent Document 4 uses partial recrystallization to ensure release of residual stress and hardness.

JP 2005-249050 A JP 2005-249051 A JP-A-2005-249106 Japanese Patent No. 5320990

  However, the methods disclosed in Patent Documents 1 to 3 only correspond to some of the four properties A to D required for the separate plate. In addition, the methods of Patent Document 1 to Patent Document 3 have many effects such as an insufficient effect on heat spot resistance, a decrease in manufacturability, and an increase in material cost. Has a problem.

  For example, Patent Documents 1, 2, and 3 do not consider the correspondence to the property A, property B, and property C, and are insufficient for improving the transmission efficiency, reducing friction loss, and reducing the size and weight.

  In addition, the austenitic stainless steel of Patent Document 3 is not only considerably expensive compared to a steel plate generally used for a clutch plate, but also because stainless steel has low thermal conductivity, frictional heat diffusibility is low. The problem is that the temperature is low and the temperature of the steel sheet surface is likely to rise.

  Patent Document 4 is intended to ensure the release of residual stress and hardness by partial recrystallization. However, since the material (hardness) changes depending on the recrystallization rate, strict annealing is required to stabilize the quality. There was a problem that temperature control was necessary. It has also been found that this method does not provide the hardness level targeted by the present invention.

  Therefore, a steel plate having good heat spot resistance and wear resistance has been demanded as a material for the clutch plate.

  This invention is made | formed in view of such a point, and it aims at providing the cold spot steel plate which suppressed heat spot resistance and abrasion resistance, and heat deformation, and its manufacturing method.

The cold-rolled steel sheet according to claim 1 is mass%, C: 0.03 to 0.08%, Si: 0 to 1.0%, Mn: 0.2 to 0.8%, P: 0. 0.03% or less, S: 0.03% or less, Al: 0.05% or less, Nb: 0.03-0.4%, V: 0.01-0.3%, Ti: 0 0.01% to 0.3% of one or more, satisfy the following formulas (1) and (2), and have a chemical component consisting of the remaining Fe and inevitable impurities, and any of Nb, V and Ti This is a cold-rolled steel sheet having excellent heat-resistant deformability, in which the carbide-containing carbide has an average particle diameter of 20 to 100 nm and a hardness of 200 HV to 400 HV.
5 × C% −Si% + Mn% −1.5 × Al <1 (1)
0.04 <(Nb% ÷ 1.4) + (V% ÷ 1.1) + Ti% <0.3 (2)

The cold-rolled steel sheet according to claim 2 is further mass%, Cr: 0.10 to 2.0%, Ni: 0 to 0.5%, Mo: 0.05 to 0.5%, B: The cold-rolled steel sheet according to claim 1, comprising 0.0002 to 0.002% of one or more kinds so as to satisfy the formula (3).
5 × C% −Si% + Mn% + 1.6 × Cr + 0.8 × Ni% −1.5 × Al <1 (3)

  The cold-rolled steel sheet according to claim 3 has an average particle diameter of a carbide containing any one of Nb, V and Ti in a surface layer portion from the steel sheet surface to at least 200 μm, from 20 to 100 nm. This is a cold-rolled steel sheet.

  The method for producing a cold-rolled steel sheet according to claim 4 is a method of heating a steel slab having the chemical component according to any one of claims 1 to 3 to 1200 ° C or higher, and a coiling temperature of 500 ° C to 700 ° C. A hot rolled coil subjected to hot rolling is used as a raw material, and is subjected to cold rolling directly or after being subjected to cold rolling after being subjected to cold rolling with a cross-sectional hardness of 200 to 400 HV. It is a manufacturing method of a rolled steel sheet.

  According to the present invention, the chemical components are regulated, and the average particle diameter of the precipitated carbide is 20 to 100 nm. Therefore, heat spot resistance and wear resistance can be improved, and thermal deformation of the clutch plate can be suppressed.

It is a perspective view which shows the state before the test of the heat spot resistance test in the Example of this invention. (A) is a top view which shows the state after the test of a heat spot resistance test same as the above, (b) is AA sectional drawing of FIG. 2 (a) which shows the state after the test of a heat spot resistance test same as the above. (C) is a figure which shows a hardness measurement location.

  An embodiment of the present invention will be described.

  The cold-rolled steel sheet according to the present invention is used, for example, as a material for a clutch plate in a wet multi-plate clutch mechanism of an automatic transmission of an automobile.

  First, the cause of the heat spot in the clutch plate formed of a normal steel plate will be described.

  When the clutch is connected under a high load, the temperature of the clutch plate surface in the connected state is remarkably increased due to friction, and the steel sheet is austenitized in the metal structure. In addition, in a steel plate, the area | region which becomes austenite by the temperature rise at the time of a clutch connection is only a steel plate surface layer, and temperature does not rise so much as it phase-transforms inside a steel plate.

  The heating region on the surface of the steel sheet is rapidly cooled (self-cooled) by rapid heat conduction into the steel sheet having a low temperature, and undergoes martensitic transformation.

  When the heated part due to friction is quenched by self-cooling and martensite transformation occurs, volume expansion occurs in the generated martensite structure, and a heat spot that is a convex region protruding higher than the surroundings is formed. Is done.

  Further, the shape change during the martensitic transformation imparts a tensile residual stress to the surrounding tissue, and the flatness of the clutch plate is impaired, resulting in distortion.

  In order to suppress such a heat spot, the following countermeasures by the first to fourth countermeasures are effective.

  The first countermeasure is suppression of the temperature rise of the clutch plate due to frictional heat. That is, by improving the thermal conductivity of the steel plate forming the clutch plate, the heat from the friction part on the surface of the clutch plate is rapidly diffused to the surroundings, and a local abnormal temperature rise on the outermost surface is suppressed.

  The thermal conductivity in steel is highest for pure iron and decreases as the amount of alloying elements increases. Further, when the volume fraction of the second phase such as pearlite increases, the thermal conductivity decreases. However, the addition of alloying elements in steel is necessary to ensure appropriate strength and wear resistance as a clutch plate.

  Therefore, in order to ensure the strength and wear resistance required for the clutch plate and maintain high thermal conductivity, the metal structure is a dispersed structure in which fine precipitates are uniformly dispersed in the ferrite structure. Is effective.

  The second measure is to suppress the γ-ization of the metal structure in the clutch plate surface layer even when the clutch plate temperature rises due to frictional heat. That is, even in a situation where a temperature increase on the surface of the steel sheet due to frictional heat is inevitable, the austenite formation due to the temperature increase due to friction is suppressed by making the steel sheet itself difficult to undergo austenite transformation.

  In order to suppress the austenite transformation, it is effective to increase the transformation point or delay the solution of the carbide.

  In order to raise the transformation point, it is effective to add an element that raises the α → γ transformation point (A3 transformation point) or to reduce the amount of an element that lowers the A3 transformation point.

  In order to delay solution, it is effective to make carbides exist in steel with a stable property that makes it hard to dissolve as much as possible.

  In carbon steel, the α → γ transformation starts from the solid solution of carbide at the interface between the carbide and the parent phase. If the solid solution of carbide in the α phase or γ phase is easy, the α → γ transformation proceeds rapidly. On the other hand, if the carbide is not easily dissolved, the progression of the α → γ transformation is suppressed.

  C, Mn, and Ni lower the transformation point, and Si and Cr raise the transformation point. Therefore, it is important to reduce the addition amount of C, Mn, and Ni as much as possible, and the addition amount of Si and Cr may be increased as necessary in consideration of other conditions.

  Further, the Fe3C (cementite: θ) system that is a carbide has a property of being easily dissolved, but in the case of Cr-added steel, Cr tends to concentrate in Fe3C. Fe3C is stabilized by the concentration of Cr. In addition, Nb-based carbides, V-based carbides, and Ti-based carbides have very high stability and low solubility in the γ phase compared to Fe3C.

  That is, fine and uniform dispersion of Nb carbide, V carbide and Ti carbide is a very excellent method for securing the strength and wear resistance of the steel sheet. Therefore, the use of Nb-based carbides, V-based carbides, and Ti-based carbides is suitable as a method for suppressing γ conversion. Further, addition of Nb, V, or Ti is also effective as a method of reducing C, which is the element with the most remarkable transformation point decrease.

  Therefore, in order to ensure strength and wear resistance, it is effective to add Nb, V, or Ti to form a hard carbide. Further, in order to reduce the amount of surplus C that does not bind to Nb, V, or Ti, the Nb addition amount, the V addition amount, the Ti addition amount, and the C amount are related to each other to obtain an optimum addition amount. The amount of dissolved C in can be reduced, and γ-ization can be further suppressed.

  The third countermeasure is to suppress martensitic transformation due to self-cooling of the clutch plate even if the metal structure of the clutch plate surface layer becomes γ due to a temperature rise due to frictional heat. That is, even in a situation where temperature rise and gamma formation on the steel sheet surface cannot be avoided, the martensitic transformation due to self-cooling is suppressed by reducing the hardenability of the steel sheet.

  In order to reduce the hardenability, it is effective to reduce the amount of elements added to improve the hardenability and to refine the γ crystal grain size.

  In order to reduce (or not improve) the hardenability, it is important to reduce the addition amount of Si, Mn, Ni, Cr, Mo, B, and the like as much as possible.

  In order to refine the γ crystal grain size, it is effective to use the grain boundary pinning effect by fine precipitates. That is, by finely dispersing the Nb-based carbide, V-based carbide, Ti-based carbide and nitride to refine the γ particle size, the nucleation of the α phase is promoted during cooling from the γ phase, Hardenability decreases. Further, the use of such Nb, V, and Ti is very effective because it not only improves the thermal conductivity and suppresses the γ-formation, but also improves the strength and wear resistance.

  The fourth countermeasure is to suppress the deformation of the clutch plate due to transformation stress even if the metal structure of the clutch plate surface layer becomes γ due to temperature rise due to frictional heat and becomes martensite due to self-cooling. In other words, even when the martensite (heat spot) of the heating part on the steel sheet surface is inevitable, the clutch plate resulting from the heat spot is ensured by sufficiently ensuring the strength of the metal structure around the heat spot. Suppresses distortion.

  As described above, the heat spot itself is considered to be a martensite region formed by heating and rapid cooling of the friction part. The temperature around the heat spot is not as high as the heat spot, but the temperature rises due to frictional heat, and the metal structure is affected. In addition, the heat spot undergoes a phase transformation of α → γ → martensite, but the heat spot is not heated so much as to be γ, and in many cases, becomes softer than the material structure. Specifically, a steel plate adjusted to about 220 to 320 HV by work hardening by cold rolling is usually used as the clutch plate. Around the heat spot, the work caused by frictional heat is recovered and recrystallized in the work structure by cold rolling, and the hardness decreases.

  Therefore, if recovery and recrystallization of the cold rolled structure can be suppressed, softening around the heat spot can be suppressed. Specifically, recrystallization can be suppressed by adding Nb, V and Ti to a structure in which Nb carbide, V carbide and Ti carbide having high thermal stability are uniformly dispersed in the structure. , The decrease in hardness can be effectively suppressed.

When heating at about 300 ° C., no significant structural change such as recrystallization or phase transformation occurs, but recovery proceeds and the residual stress is released. If an imbalance occurs in the progress of this recovery, it will lead to deformation of the plate. The following principle is used as means for preventing deformation caused by heating at about 300 ° C.
1) Suppression of local temperature rise of plate If the thermal conductivity of the steel plate is high, heat diffuses rapidly from the friction part on the plate surface to the surroundings, and local abnormal temperature rise on the outermost surface is suppressed. As a result, the imbalance in the progress of recovery is reduced.
The thermal conductivity of steel (iron) is highest for pure iron, and decreases as the amount of alloying elements increases. Further, when the area ratio of the second phase such as pearlite increases, the thermal conductivity decreases. The addition of alloying elements to steel is necessary to ensure strength and wear resistance.
As a result of the study by the inventors, the optimum structure morphology that combines the strength and wear resistance required for the clutch plate and the maintenance of high thermal conductivity is obtained by uniformly dispersing fine precipitates in the ferrite structure. It turned out to be a dispersion-strengthened organization.

2) Coping with local temperature rise of the plate Even if the local temperature rise on the surface of the steel plate is unavoidable, if the progress of recovery can be suppressed, the release of residual stress at the temperature rising portion can be suppressed. .
The concept of suppression of recovery is as follows. That is, by suppressing the movement of dislocations with fine precipitates, the recovery is suppressed and the residual stress is maintained. Of the precipitates, Fe ₃ C (θ, cementite) -based carbides are easily coarsened. Therefore, it is effective to suppress the movement of dislocations with these fine carbides by adding Nb, V, and Ti that generate fine carbides. In addition, these fine carbides can ensure the strength and wear resistance of the steel sheet.

And based on the said countermeasure, the chemical component of the cold-rolled steel plate was prescribed | regulated as follows. The content of each element is mass% unless otherwise specified.

  That is, the chemical composition of the cold-rolled steel sheet is 0.03 to 0.12% C, 0 to 1.0% Si (including no addition), 0.2 to 0.8% Mn, and 0.0. 03% or less of P (not including no addition), 0.03% or less of S (not including no addition), 0.03 to 0.4% of Nb and 0.05% or less of Al (no addition) Not added)), the balance being composed of Fe and inevitable impurities. Moreover, in the range of content of each said element, each element is contained so that 5 * C% -Si% + Mn% -1.5 * Al% <1 which is Formula (1) may be satisfy | filled. In the formula (1), C% is the C content (%), Si% is the Si content (%), Mn% is the Mn content (%), and Al% is the Al content. Amount (%).

  Further, not only the above chemical components but also V may be contained instead of Nb as described below.

  That is, 0.03 to 0.12% C, 0 to 1.0% Si (including no addition), 0.2 to 0.8% Mn, 0.03% or less P (no addition) ), 0.03% or less of S (not including additive), 0.03 to 0.3% V and 0.05% or less of Al (not including additive). The remainder may be composed of Fe and unavoidable impurities, and the chemical component may be configured to satisfy the formula (1).

  Furthermore, you may make it the structure which contained not only each said chemical component but multiple types of Nb, V, and Ti as follows.

  That is, 0.03 to 0.12% C, 0 to 1.0% Si (including no addition), 0.2 to 0.8% Mn, 0.03% or less P (no addition) ), 0.03% or less of S (not including no addition) and 0.05% or less of Al (not including no addition) so as to satisfy the formula (1), and , 0.01 to 0.4% of Nb, 0.01 to 0.3% of V, and 0.01 to 0.3% of Ti of 0.04 <( Nb% ÷ 1.4) + (V% ÷ 1.1) + Ti% <0.3 may be included, and the balance may be a chemical component composed of Fe and inevitable impurities. In the formula (2), Nb% is the Nb content (%), V% is the V content (%), and Ti% is the Ti content (%).

  Moreover, you may make it the structure which contained not only each said chemical component but at least 1 sort (s) of Cr, Ni, Mo, and B as needed as follows.

  That is, in addition to the above chemical components, 0.10 to 2.0% Cr, 0.05 to 0.5% Ni, 0.05 to 0.5% Mo, and 0.0002 to 0.002% And at least one kind of B is contained so as to satisfy the formula (3): 5 × C% −Si% + Mn% + 1.6 × Cr% + 0.8 × Ni% −1.5 × Al% <1 It may be a chemical component. In the formula (3), C% is the C content (%), Si% is the Si content (%), Mn% is the Mn content (%), and Cr% is the Cr content. In the amount (%), Ni% is the Ni content (%), and Al% is the Al content (%).

  Here, each element and content of each element in the cold-rolled steel sheet will be described.

  When the content of C (carbon) is less than 0.03%, it becomes difficult to form hard carbide particles that contribute to wear resistance. On the other hand, as the C content increases, the α → γ transformation point decreases, the hardness and the amount of expansion deformation when the martensite structure is formed in the heated portion by frictional heat, and the thermal conductivity. Decreases. Therefore, considering the balance with other characteristics within a range satisfying the relationship of the expression (1) or (3), the upper limit of the C content is 0.12%. Accordingly, the C content is preferably 0.03% or more and 0.12% or less, and when priority is given to improving the heat spot resistance, it is preferably less than 0.10%.

  When Si (silicon) is contained for a normal deoxidation purpose, a content of less than 0.4% is sufficient. However, since Si has the effect of increasing the α → γ transformation point, it may be contained in excess of 0.4%. On the other hand, when Si is excessively contained exceeding 1.0%, brittle fracture is likely to occur during rolling of the steel sheet. Therefore, the content of Si is set to 0% (including no addition) or more and 1.0% or less.

  Mn (manganese) is an element necessary for improving the strength of the material steel plate, and in order to improve the strength, it is necessary to contain 0.2% or more. On the other hand, Mn has the effect of lowering the α → γ transformation point, so if it is contained in excess of 0.8%, the α → γ transformation point is lowered. Therefore, the Mn content is set to 0.2% or more and 0.8% or less. As the Mn content increases, the hot-rolled steel sheet tends to have a band-like structure, and the properties of the punched section by punching tend to deteriorate, so the Mn content is more preferably 0.6% or less.

  When P (phosphorus) and S (sulfur) are contained in an amount exceeding 0.03%, punchability and toughness are reduced. Therefore, the content of P is set to 0.03% or less (excluding no addition), and the content of S is set to 0.03% or less (excluding no addition).

  Al (aluminum) is an element having a deoxidizing effect. A content of less than 0.01% is sufficient for deoxidation purposes only. However, Al has an effect of increasing the α → γ transformation point, so Al may be contained in excess of 0.01%. Further, if the steel contains Nb, V, or Ti at a predetermined concentration, there is no merit regarding the effect of increasing the transformation point even if Al is contained in a large amount exceeding 0.05%. Therefore, the content of Al is set to 0.05% or less (excluding no addition).

  Here, the α → γ transformation point and the hardenability in the cold-rolled steel sheet are affected by the action of each element of C, Si, Mn, and Al. Therefore, it is necessary to comprehensively consider the contents of these elements. And in order to raise (alpha)-> gamma transformation point and to reduce hardenability, content of each element is 5 * C% -Si% + Mn% -1.5 * Al% <1 (1 ) It is necessary to satisfy the relationship shown by the formula.

  Nb (niobium), V (vanadium), and Ti (titanium) combine with C in the steel to form a hard carbide and contribute to an improvement in wear resistance. Moreover, Nb, V, and Ti have the effect | action which fixes carbon in steel as NbC, VC, and TiC with low solubility, and suppresses the alpha-> gamma transformation in the heating part by frictional heat. Furthermore, Nb, V, and Ti effectively suppress the coarsening and softening of the ferrite crystal grain size in the temperature rising portion due to friction. That is, heat spot resistance and wear resistance can be improved by containing Nb, V, and Ti.

  When Nb is contained alone among Nb, V, and Ti, it is necessary to contain Nb in an amount of 0.03% or more in order to achieve the effects related to the heat spot resistance and wear resistance. On the other hand, if Nb exceeds 0.4%, the hardness of the hot-rolled steel sheet will increase, making it impossible to produce plate steel having the desired product thickness and hardness. Therefore, the content of Nb when Nb is contained alone among Nb, V, and Ti is set to 0.03% or more and 0.4% or less.

  Further, in the case where V is contained alone among Nb, V and Ti, in order to achieve the effects related to the heat spot resistance and wear resistance, it is necessary to contain V by 0.03% or more. On the other hand, if V is contained in excess of 0.3%, the hardness of the hot-rolled steel sheet will increase, making it impossible to produce plate steel having the desired product thickness and hardness. Therefore, the content of V when N is contained alone among Nb, V and Ti is set to 0.01% or more and 0.3% or less.

  In the case where Ti is contained alone among Nb, V, and Ti, in order to exhibit the effects related to the heat spot resistance and wear resistance, it is necessary to contain 0.03% or more of Ti. On the other hand, if Ti is contained in excess of 0.3%, the hardness of the hot-rolled steel sheet is increased, so that it is impossible to produce plate steel having the target product thickness and hardness. Therefore, the content of Ti when Ti is contained alone among Nb, V and Ti is set to 0.01% or more and 0.3% or less.

  Furthermore, in the case where a plurality of Nb, V, and Ti are contained in combination, Nb is 0.01% or more, and V is 0.01% in order to achieve the effects related to the heat spot resistance and wear resistance. % Or more and Ti must be contained by 0.01% or more. On the other hand, when Nb is contained more than 0.4%, V is contained more than 0.3%, and Ti is contained more than 0.3%, the hardness of the hot-rolled steel sheet is increased and aimed. It becomes impossible to produce plate steel having the product thickness and hardness. Therefore, when Nb, V and Ti are contained in combination, the Nb content is 0.01% or more and 0.4% or less, and the V content is 0.01% or more and 0.3% or less. Ti content is set to 0.01% or more and 0.3% or less.

  In addition, when Nb, V, and Ti are added together in this way, heat spot resistance, wear resistance, and other side effects are affected by the action of each element added. Therefore, the contents of these elements need to be comprehensively considered, and the contents of Nb, V and Ti are 0.04 <(Nb% ÷ 1.4) + (V% ÷ 1.1) + Ti% It is necessary to satisfy the relationship represented by the expression (2) where <0.3.

  Cr (chromium), Ni (nickel), Mo (molybdenum), and B (boron) have the effect of improving wear resistance and toughness. Therefore, when the counterpart spline with which the spline portion of the separate plate is engaged is hard by surface hardening treatment such as carburizing or nitriding, it is preferable to add these elements.

  When Cr is contained, the content of Cr is set to 0.10% or more and 2.0% or less in consideration of the effect of improving wear resistance and side effects.

  When Ni is contained, the Ni content is set to 0.05% or more and 0.5% or less in consideration of the toughness improving action and side effects.

  When Mo is contained, the Mo content is set to 0.05% or more and 0.5% or less in consideration of the toughness improving effect and side effects.

  When B is contained, the content of B is set to 0.0002% or more and 0.002% or less in consideration of toughness improving action and side effects.

  Further, when Cr or Ni is contained as required, the α → γ transformation point and hardenability of the cold-rolled steel sheet are also affected by the action of Cr and Ni. Therefore, in order to increase the α → γ transformation point and decrease the hardenability, it is necessary to comprehensively consider the contents of C, Si, Mn and Al, Cr and Ni, and 5 × C% It is necessary to satisfy the relationship represented by the formula (3) where −Si% + Mn% + 1.6 × Cr% + 0.8 × Ni% −1.5 × Al% <1.

  And as mentioned above, in order to improve heat spot resistance and wear resistance, very important elements are Nb carbide, V carbide and Ti carbide. That is, Nb-based carbides, V-based carbides, and Ti-based carbides on the steel plate surface are effective for improving the heat spot resistance and the wear resistance on the friction surface with the mating spline in the spline portion. Therefore, the Nb carbide, V carbide and Ti carbide need to be finely and uniformly dispersed.

Specifically, when Nb is contained alone, it is necessary that the average particle size of Nb-based carbides, which are precipitates in the steel sheet, be in the range of 20 nm to 100 nm.

  In addition, when V is contained alone, it is necessary that the average particle diameter of the V-based carbide which is a precipitate in the steel sheet is in the range of 20 nm to 100 nm.

  In addition, when Ti is contained alone, the average particle size of the Ti-based carbide that is a precipitate in the steel sheet needs to be in the range of 20 nm to 100 nm.

  Further, when a plurality of Nb, V, and Ti are contained in combination, the average particle size of precipitates in the steel sheet, that is, carbides including any of Nb, V, and Ti is 20 nm to 100 nm. Must be within the range.

  In particular, Nb-based carbides, V-based carbides, and Ti-based carbides present on the surface of the steel sheet and in the vicinity of the surface layer have a large effect on heat spot resistance and wear resistance. Therefore, it is preferable that the average particle size of the carbide containing any one of Nb, V, and Ti present in the surface layer portion that is at least 200 μm from the steel plate surface is 20 nm or more and 100 nm or less.

  On the other hand, Nb-based carbides, V-based carbides, and Ti-based carbides that are deeper than the surface layer portion such as the central portion in the cross-sectional direction of the steel sheet do not contribute much to the heat spot resistance and have excellent wear resistance. On the contrary, there is a possibility of hurting the opponent material. Therefore, the average particle diameters of the Nb-based carbide, V-based carbide, and Ti-based carbide at the center in the cross-sectional direction of the steel plate may be approximately the same as those of the surface layer portion. Conversely, if Nb-based carbides, V-based carbides, and Ti-based carbides are excessively present in the center in the cross-sectional direction with respect to the surface layer portion, it is not preferable when using a cold-rolled steel sheet as a clutch plate. Therefore, the average particle diameter of the carbide containing any one of Nb, V, and Ti in a layer deeper than 200 μm from the surface of the steel sheet in the cross-sectional direction is preferably 20 nm or more and 100 nm or less, as in the surface layer part.

  Next, the manufacturing method of this invention is demonstrated.

  First, 0.03-0.12% C, 0-1.0% Si (including no addition), 0.2-0.8% Mn, 0.03% or less P (no addition) 0.03% or less of S (not including additive), 0.03 to 0.4% of Nb and 0.05% or less of Al (not including additive). Then, a steel slab having a chemical component that is composed of Fe and inevitable impurities and that satisfies the relationship represented by the formula (1) is melted.

  When V is contained instead of Nb, 0.03 to 0.12% C, 0 to 1.0% Si (including no addition), 0.2 to 0.8% Mn 0.03% or less of P (not including no addition), 0.03% or less of S (not including no addition), 0.01 to 0.3% V, and 0.05% or less of Al A steel slab having a chemical composition that contains (the additive is not included) and the balance is composed of Fe and inevitable impurities and satisfies the relationship represented by the formula (1) is melted.

  When Ti is contained instead of Nb, 0.03 to 0.12% C, 0 to 1.0% Si (including no addition), 0.2 to 0.8% Mn 0.03% or less of P (excluding no addition), 0.03% or less of S (not including no addition), 0.01 to 0.3% Ti and 0.05% or less of Al A steel slab having a chemical composition that contains (the additive is not included) and the balance is composed of Fe and inevitable impurities and satisfies the relationship represented by the formula (1) is melted.

  Further, when a plurality of Nb, V, and Ti are contained in combination, 0.03 to 0.12% C, 0 to 1.0% Si (including no addition), 0 .2 to 0.8% Mn, 0.03% or less P (without addition), 0.03% or less S (without addition) and 0.05% or less Al (without addition) Is added so as to satisfy the relationship represented by the formula (1), and 0.01 to 0.4% Nb, 0.01 to 0.3% V, and 0.01 to A steel slab having a chemical composition in which a plurality of kinds of 0.3% Ti are contained so as to satisfy the relationship represented by the formula (2) and the balance is composed of Fe and inevitable impurities is melted.

  Further, in the case of containing at least one of Cr, Ni, Mo and B, in addition to the above chemical components, 0.10 to 2.0% Cr, 0.05 to 0.5% Ni, 0 A steel slab having a chemical composition containing at least one of 0.05 to 0.5% Mo and 0.0002 to 0.002% B so as to satisfy the relationship represented by the formula (3) is melted.

  After this steel slab is heated to 1200 ° C. or higher, hot rolling is performed. In addition, when heating temperature is lower than 1200 degreeC, solutionization of a carbide | carbonized_material may become inadequate.

  In the hot rolling, it is preferable to adjust the hot rolling finishing temperature to a temperature above the Ar3 transformation point from the viewpoint of the quality of the hot rolled steel sheet, the hot rolling efficiency, and the like. That is, the finishing temperature is 850 ° C. or higher and 950 ° C. or lower, and the hot rolled coil wound in the temperature range where the winding temperature is 500 ° C. or higher and 700 ° C. or lower is used as the material. In addition, the precipitation amount of a carbide | carbonized_material reduces that winding-up temperature is less than 500 degreeC. On the other hand, when the coiling temperature exceeds 700 ° C., the surface decarburization of the steel sheet becomes remarkable, the amount of carbide precipitation in the outermost layer portion decreases, and the particle size of the precipitated carbide decreases. Further, when the average cooling rate from the finishing temperature to the winding temperature is less than 20 ° C./second, the precipitated carbides are coarsened, and therefore the average cooling rate is preferably 20 ° C./second or more.

  The hot-rolled steel sheet is made into a product by cold rolling after removing the surface scale by pickling treatment. Specifically, in order to obtain a hardness of 200 HV or more and 400 HV or less, which is necessary as a steel plate for a clutch plate, particularly a separate plate, it is necessary to perform cold rolling at a cold rolling rate of 20% to 70%. The hardness is adjusted by adjusting the rolling rate.

  Here, since the friction plate is required to have hardness and flatness of 200 HV or more and 400 HV or less from the viewpoint of punchability, a hot rolled steel sheet is cold-rolled to produce a product. In order to ensure flatness, it is preferable to adjust the cold rolling rate within a range of 20% to 70%. On the other hand, if the hardness is less than 200 HV, the punched product has a large sag and burrs, a secondary shear surface is generated, and the properties of the spline portion are deteriorated. On the other hand, when the hardness exceeds 400 HV, wear and damage of the punching die increase, and a shearing surface is not formed on the punching surface, which is not preferable as the shape of the spline portion.

  Moreover, you may anneal a hot-rolled steel plate directly as needed, or may anneal a cold-rolled steel plate as intermediate annealing. In any case, it is preferable to perform cold rolling after annealing. In addition, when intermediate annealing is performed during the cold rolling process, appropriate annealing conditions can be appropriately selected in consideration of the product sheet thickness and the cold rolling rate. However, annealing conditions that cause surface decarburization are not preferred.

  And according to the said cold rolled steel sheet, while regulating a chemical component based on the said 1st countermeasure thru | or a 4th countermeasure, the average particle diameter of the precipitated Nb type carbide, V type carbide, and Ti type carbide is 20 nm. Since the thickness is 100 nm or less, heat spot resistance and wear resistance can be improved.

  That is, in the conventional technique, it is necessary to reduce the addition amount of the alloy element in order to improve the heat spot resistance, but to improve the strength by adding a necessary alloy element to improve the wear resistance. Since it is necessary, the heat spot resistance and the wear resistance could not be improved in a well-balanced manner. However, the cold-rolled steel sheet can improve the heat spot resistance and the wear resistance in a well-balanced manner. Therefore, it is suitable as a material for clutch plates and the like.

  Hereinafter, this example and a comparative example will be described.

  First, steel slabs having chemical components shown in Table 1 were melted. In Table 1, when not containing at least one of Cr, Ni, Mo and B, the value of the left side of the formula (1) is shown as the Q value, and at least of Cr, Ni, Mo and B When it contains 1 type, the value of the left side of (3) Formula is shown as Q value.

  Each steel slab was subjected to hot rolling and cold rolling under the conditions shown in Table 2 to prepare each specimen.

  In the hot rolling, the heating temperature was 1250 ° C., and the winding temperature was 450 ° C., 520 ° C., 570 ° C., 600 ° C., 630 ° C. or 725 ° C.

  Further, the hot-rolled steel sheet was finished with a plate thickness of 1.8 mm at various cold rolling rates after hydrochloric acid pickling. The cross-sectional hardness at the time after cold rolling was set to 250 HV. In addition, about 2 types of a present Example, it cold-rolled, after annealing a hot-rolled steel plate at 690 degreeC.

  About each of these test materials, measurement of thermal conductivity, measurement of cross-sectional hardness, precipitated carbides (Nb carbide (NbC), V carbide (hereinafter referred to as VC or V4C3 as VC)) and Ti carbide (TiC)). The average particle size was measured and the volume fraction of the hard tissue in the cross-sectional structure was measured.

  Further, a test piece was collected from each test material and subjected to a punching test, a pin-on-disk friction and wear test, and a heat spot resistance test.

  In the thermal conductivity measurement, the thermal conductivity at 100 to 200 ° C. was measured using a laser flash method. And the thing whose measured thermal conductivity was 50 W / m * K or more was made into good evaluation, and was set as (circle) in Table 2.

  In the cross-sectional hardness measurement, a part of each test material was cut out, embedded in resin, polished, and then measured for Vickers hardness at the center of the cross-sectional thickness. The measurement load was 50 gf.

  In the measurement of the average particle size of the carbide of the surface layer, a part of each test material was cut and embedded in the resin so that one surface of the cold-rolled steel sheet was an observation surface. And after polishing and etching in parallel with the surface of the cold-rolled steel sheet so that the position of the depth of 50 to 150 μm in the thickness direction from the surface of the cold-rolled steel sheet becomes the observation surface, an extraction replica is prepared and deposited. Things were observed. Among Nb, V and Ti, Nb added alone observed NbC, V added alone observed VC, Ti added alone observed TiC, and composite added Corresponding precipitates were observed among NbC, VC and TiC. For observation, a transmission electron microscope (TEM) was used, and the size of the precipitate was converted into a circle with an image analyzer, and the diameter of each precipitate was calculated. The photographing magnification was 50,000 times and 10 fields of view were observed. Then, the sum of the calculated particle diameters of the precipitates was divided by the number of precipitates to obtain an average particle diameter. Regarding the average particle size of the precipitates of the test materials thus measured, in Table 2, A is the case where the average particle size is less than 20 nm, and B is the case where the average particle size is 20 to 100 nm. The case where the particle size exceeded 100 nm was defined as C.

  In the punching test, a circular hole having a thickness of 1.8 mm and a diameter of 10 mm was punched from each test piece using a 300 kN universal testing machine. As the punching die, SKD11 of JIS standard mainly for cold die tempered to 60HRC for both punch and die was used. The test conditions were a punching speed of 1.7 mm / second and a clearance of 5%. Punched processed products having 20 to 30 shots were collected and evaluated for sagging amount and shear surface ratio on the shear plane. Specifically, each index was measured and the average value was calculated for the rolling direction of the material steel plate and the direction perpendicular thereto. The pass / fail threshold values were 0.2 mm and 70%, respectively. Then, each index satisfying the threshold value was evaluated as good evaluation, and in Table 2, it was evaluated as “good”.

  In the pin-on-disk friction and wear test, a wear test was performed while dripping mission oil using a pin-on-disk friction and wear tester. Specifically, the pin was 1.8 mm in thickness and 10 mm × 2 mm in a rectangular plate shape, and was fixed to the sample holder so that the contact surface with the disk had a thickness of 1.8 mm × 2 mm. In addition, a non-woven fabric (buff) is applied to the disc, and a paste containing alumina having a particle size of 0.1 μm is applied, while pressing a pin with a test load of 50 N, a friction speed of 1.0 m / sec and a friction distance of 3600 m. A wear test was conducted under the conditions. And, the friction surface of the pin before the friction test was adjusted to Ra = 0.2 μm, and the roughness of the pin friction surface after the friction test was Ra = 0.1 μm or more was evaluated as good evaluation. Then, it was set as ○.

  In the heat spot resistance test (rapid heating / cooling test), the surface layer portion was locally heated by irradiating the surface of the test piece with a strong laser beam for a short time. In other words, after heating the surface of the steel sheet with laser light, the laser irradiation is stopped, and the heated part is rapidly cooled by the self-cooling action of the steel sheet, and a characteristic altered layer in the heat spot (structure change layer including martensite) Produced. Even when a martensite phase is not formed, the material steel plate hardened by cold rolling may be recrystallized into coarse crystal grains due to a temperature rise caused by laser irradiation, which may reduce the hardness. Thus, if a deteriorated layer is formed including hardening and softening, a difference will arise in the cross-sectional hardness inside a raw steel plate, and the hardness of a laser irradiation part. Therefore, heat spot resistance can be evaluated by measuring the cross-sectional hardness between the surface layer portion and the inside.

  Such a heat spot resistance test was specifically performed as follows. As shown in FIG. 1, a 25 mm × 25 mm test piece 1 collected from each specimen was fixed to the center of the surface of a steel block 2 having a thickness of 20 mm and a thickness of 60 mm × 60 mm with a bolt (not shown). And the laser beam was irradiated to the center part of the test piece 1 surface. The irradiation conditions were a CO2 laser, an effective output of 1080 W, a beam shape of 6 mmφ, and an irradiation time of 0.75 seconds.

  Further, as shown in FIGS. 2 (a) to 2 (c), in the cross section of the test piece 1 after laser irradiation, a laser irradiation measuring unit 3a, which is a position 100 μm from the surface of the laser irradiation unit 3 irradiated with laser, and Measure the Vickers hardness of the thickness center 4 which is the center of the thickness direction, and evaluate the degree of hardening or softening of the surface layer (laser irradiation measurement part 3a) with respect to the hardness of the inside (sheet thickness center 4) did. In Table 2, when the difference in hardness between the surface layer and the inside is within ± 50 HV, the evaluation is “Good”, the case where it is 50 HV or more and less than 100 HV is Δ, the case where it is 100 HV or more is Δ, and −50HV The following cases were marked with ▼.

A low temperature heating test for evaluation of thermal deformation was performed according to the following procedure.
The test piece was sampled from a cold-rolled sheet having a thickness of 1.8 t into a 30 × 120 mm strip. The test piece was placed on a surface plate without being fixed, and laser irradiation was performed. The conditions of laser irradiation are a CO ₂ laser (output 400 W), a beam diameter of 15 mmφ, and an irradiation time of 60 seconds. The amount of warpage per 100 mm length before and after heating was measured, and the amount of change was evaluated. The results are shown in Table 2. The evaluation was OK when the amount of change was 20 μm or less.

  The overall evaluation was a good evaluation of the three evaluations: punched surface property evaluation by punching test, friction wear resistance evaluation by pin-on-disk friction wear test, and heat spot resistance evaluation by heat spot resistance test. In Table 2 was marked as ◯.

  The test conditions and test results are shown in Table 2.

  As shown in Table 2, all of the present examples had good punchability, friction wear resistance, and heat spot resistance.

  On the other hand, test No. which is a comparative example. In 6-b, the coiling temperature of hot rolling was low and the cooling rate was slow, so the TiC of the surface layer became coarse, and the warpage amount exceeded 20 μm in the low temperature heating test. Further, the difference in hardness between the surface layer and the inside in the rapid heating / quenching portion was −50 HV or more.

  Test No. which is a comparative example. In 7-b, since the coiling temperature of hot rolling was high, decarburization occurred on the surface of the plate, and the amount of TiC produced was small and the particle size was small, so the wear resistance was poor, and the low temperature heating test and rapid heating / quenching Also in the test, the amount of warpage and hardness increased.

  Test No. which is a comparative example. In No. 17, since the TiC content was extremely small, there was almost no precipitation of TiC, and the wear resistance was poor, and the warpage amount and the hardness difference were large in the low temperature heating test and the rapid heating / quenching test.

  Test No. which is a comparative example. No. 18 had an excessive Q value of 1.18, so martensitic transformation occurred in the rapid heating / cooling portion, and irregularities were generated on the plate surface.

  Test No. which is a comparative example. In No. 19, since the C content of the steel material was as low as 0.02%, the production of TiC and cementite was small, and the wear resistance was poor. Also, the amount of warpage and hardness difference increased in the low temperature heating test and the rapid heating / cooling test.

  Test No. which is a comparative example. No. 21 had a high Mn content in the steel material and an excessive Q value, so that the hardenability was high, and the hardening in the rapid heating / quenching portion exceeded 100 HV.

  Test No. which is a comparative example. No. 22 had a high Q value due to the high Mn content of the steel material, and the hardening at the heat / quenching part exceeded 100 HV. In addition, the high C content affected the thermal conductivity.

Claims (4)

In mass%, C: 0.03-0.08%, Si: 0-1.0%, Mn: 0.2-0.8%, P: 0.03% or less, S: 0.03% or less Al: 0.05% or less,
Further, Nb: 0.03 to 0.4%, V: 0.01 to 0.3%, Ti: 0.01 to 0.3%, or one or two or more of the following (1) formula and ( 2) satisfying the formula, having a chemical component consisting of the balance Fe and inevitable impurities,
The average particle size of the carbide containing any of Nb, V and Ti is 20 to 100 nm,
A cold-rolled steel sheet having a heat resistance of 200HV to 400HV and excellent heat resistance.
5 × C% −Si% + Mn% −1.5 × Al <1 (1)
0.04 <(Nb% ÷ 1.4) + (V% ÷ 1.1) + Ti% <0.3 (2) Further, by mass%, Cr: 0.10 to 2.0%, Ni: 0 to 0.5%, Mo: 0.05 to 0.5%, B: 0.0002 to 0.002% The cold-rolled steel sheet according to claim 1, comprising a seed so as to satisfy the formula (3).
5 × C% −Si% + Mn% + 1.6 × Cr + 0.8 × Ni% −1.5 × Al <1 (3)   The cold-rolled steel sheet according to claim 1 or 2, wherein an average particle diameter of a carbide containing any of Nb, V, and Ti in a surface layer portion from the steel sheet surface to at least 200 µm is 20 to 100 nm. A steel slab having the chemical component according to any one of claims 1 to 3 is heated to 1200 ° C or higher,
The material is a hot-rolled coil that is hot-rolled at a coiling temperature of 500 ° C or higher and 700 ° C or lower,
A method for producing a cold-rolled steel sheet having a cross-sectional hardness of 200 to 400 HV, which is directly cold-rolled or annealed and then cold-rolled.